tnt2012 abstract book
DESCRIPTION
TNT2012 is being held in large part due to the overwhelming success of earlier TNT Nanotechnology Conferences and will be organised in a similar way to the prior events. This high-level scientific meeting series aims to present a broad range of current research in Nanoscience and Nanotechnology worldwide, as well as initiatives such as EU/ICT/FET, MANA, CIC nanoGUNE Consolider, etc. TNT events have demonstrated that they are particularly effective in transmitting information and promoting interaction and new contacts among workers in this field. Furthermore, this event offers visitors, exhibitors and sponsors an ideal opportunity to interact with each other.TRANSCRIPT
© 2011 FEI Company. We are constantly improving the performance of our products, so all specifications are subject to change without notice.
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For over 60 years, FEI has been a global leader in focused
electron and ion beam microscopy technologies. From the
most powerful, commercially-available microscope, the
Titan™ G2 60-300 S/TEM, to the Magellan™, the first extreme
high resolution (XHR) SEM, FEI produces innovative imaging
solutions for the material science, life science, electronics and
natural resource markets, revolutionizing your exploration and
discovery at the nanoscale.
Your Journey to
the Nanoscale
Begins Here
TNT2012 i
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Foreword 02
Committees 04
Poster awards 05
Sponsors 06
Exhibitors 07
Speakers 13
Abstracts 27
Posters list 203
Image credit: Atomic motion tracks newly presented by merging the STM images before and after X-ray irradiation.
Akira Saito (Osaka University and RIKEN SPring-8 Center, Japan)
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On behalf of the International, Local and Technical Committees, we take great pleasure in welcoming you to Madrid (Spain) for the 13th “Trends in NanoTechnology” International Conference (TNT2012). TNT2012 is being held in large part due to the overwhelming success of earlier TNT Nanotechnology Conferences and will be organised in a similar way to the prior events. This high-level scientific meeting series aims to present a broad range of current research in Nanoscience and Nanotechnology worldwide, as well as initiatives such as EU/ICT/FET, MANA, CIC nanoGUNE Consolider, etc. TNT events have demonstrated that they are particularly effective in transmitting information and promoting interaction and new contacts among workers in this field. Furthermore, this event offers visitors, exhibitors and sponsors an ideal opportunity to interact with each other. One of the main objectives of the Trends in Nanotechnology conference is to provide a platform where young researchers can present their latest work and also interact with high-level scientists. For this purpose, the Organising Committee provides every year around 60 travel grants for students. In addition, this year, 9 awards (2400 Euros in total) will be given to young PhD students for their contributions presented at TNT. More than 40 senior scientists are involved in the selection process. Grants and awards are funded by the TNT Organisation in collaboration with several governmental and research institutions.
TNT is now one of the premier European conferences devoted to nanoscale science and technology. We are indebted to the following Scientific Institutions, Companies and Government Agencies for their financial support: Phantoms Foundation, Escuela Técnica Superior de Ingenieros Industriales (ETSII Madrid), Universidad Politécnica de Madrid (UPM) / Campus de Excelencia Internacional, Instituto de Fusión Nuclear (IFN), Fundación para el Fomento de la Innovación Industrial (F2I2), Donostia International Physics Center (DIPC), CIC nanoGUNE, Universidad Autónoma de Madrid (UAM), Instituto Español de Comercio Exterior (ICEX) & “españa-technology for life” program, NIMS (Nanomaterials Laboratory) and MANA (International Center for Materials and Nanoarchitectonics), Institute for Bioengineering of Catalonia (IBEC), FEI, nanotec Red, Tecnan, Carl Zeiss Microscopy, European Physical Society (EPS), AtMol Integrated Project (EU/ICT/FET) and Viajes El Corte Inglés. We would also like to thank the following companies and institutions for their participation: nanotec Electronica, nanotec Red, Raith, nanoimmunotech, IOP Publishing, Schaefer Techniques, Omicron Nanotechnology, NanoInnova Technologies, MONCLOA Campus of International Excellence, ICEX, Irida, Renishaw, Techno Fusión and UAM+CSIC Campus of International Excellence. In addition, thanks must be given to the staff of all the organising institutions whose hard work has helped planning this conference.
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Image credit: SEM image of PVDF nanostructures prepared by solution template wetting. Mari Cruz García-Gutiérrez (IEM-CSIC, Spain)
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TNT2012 Committees
Organising Committee
Jose-Maria Alameda (Universidad de Oviedo, Spain)
Masakazu Aono (MANA, NIMS, Japan)
Robert Baptist (CEA / DRT / LETI, France)
Xavier Cartoixa (UAB, Spain)
Antonio Correia (Phantoms Foundation, Spain) –
Conference Chairman
Pedro Echenique (DICP / UPV, Spain)
Jose Maria Gonzalez Calbet (UCM, Spain)
Uzi Landman (Georgia Tech, USA)
Alfonso Lopez (Grupo Atenea, Spain)
Jose Manuel Perlado Martin (IFN-ETSII / UPM, Spain)
Jose Maria Pitarke (CIC nanoGUNE Consolider, Spain)
Ron Reifenberger (Purdue University, USA)
Jose Rivas (INL, Portugal)
Juan Jose Saenz (UAM, Spain)
Josep Samitier (IBEC - Universitat de Barcelona, Spain)
Frank Scheffold (University of Fribourg, Switzerland)
Didier Tonneau (CNRS-CINaM, France)
International Scientific
Committee
Masakazu Aono (MANA / NIMS, Japan)
Emilio Artacho (CIC nanoGUNE Consolider, Spain)
Andreas Berger (CIC nanoGUNE Consolider, Spain)
Fernando Briones (IMM / CSIC, Spain)
Remi Carminati (Ecole Centrale Paris, France)
Jose-Luis Costa Kramer (IMM / CSIC, Spain)
Antonio Garcia Martin (IMM / CSIC, Spain)
Raquel Gonzalez Arrabal (IFN-ETSII / UPM, Spain)
Pierre Legagneux (Thales, France)
Annick Loiseau (ONERA - CNRS, France)
Stefan Roche (ICN and CIN2, Spain)
Josep Samitier (IBEC - Universitat de Barcelona, Spain)
Technical Committee
Carmen Chacón Tomé (Phantoms Foundation, Spain)
Viviana Estêvão (Phantoms Foundation, Spain)
Maite Fernández Jiménez (Phantoms Foundation, Spain)
Paloma Garcia Escorial (Phantoms Foundation, Spain)
Pedro Garcia Mochales (UAM, Spain)
Adriana Gil (Nanotec, Spain)
Carlo Guerrero (IFN-ETSII / UPM, Spain)
Conchi Narros Hernández (Phantoms Foundation, Spain)
Joaquin Ramon-Laca (Phantoms Foundation, Spain)
Jose-Luis Roldan (Phantoms Foundation, Spain)
Local Organising
Committee
Carlos Conde Lázaro (UPM, Spain) –
Conference Honorary Chairman
Jesus Felez (ETSII / UPM, Spain)
Gonzalo Leon (UPM, Spain)
Jose María Martínez Val (F2I2, Spain)
Emilio Minguez (UPM, Spain)
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TNT2012 Poster awards
Funded by Award
NIMS / MANA 300 Euros300 Euros300 Euros300 Euros
IBEC 300 Euros300 Euros300 Euros300 Euros
European Physical Society 250 Euros250 Euros250 Euros250 Euros
Phantoms Foundation Digital Video CameraDigital Video CameraDigital Video CameraDigital Video Camera
Phantoms Foundation Digital Video CameraDigital Video CameraDigital Video CameraDigital Video Camera
Phantoms Foundation Digital Video CameraDigital Video CameraDigital Video CameraDigital Video Camera
David Prize Private donation 300 US Dollars300 US Dollars300 US Dollars300 US Dollars
Keren Prize Private donation 300 US 300 US 300 US 300 US DollarsDollarsDollarsDollars
TNT 2012 Organisation Free registration to the Free registration to the Free registration to the Free registration to the
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TNT2012 Sponsors
Platinum Sponsor
Sponsors
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TNT2012 Exhibitors
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Nanotec Electronica is one of the leading companies in the Nanotechnology Industry. In only ten years Nanotec Electronica has established itself as one of the strongest companies that design, manufacture and supply Scanning Probe Microscopes (SPM). Our highly qualified team uses cutting-edge technology in order to provide a cost-effective tool to gain access to the nanometer scale for both scientific and industrial communities. With its headquarters based in Spain and distributors located around the world, Nanotec ensures global presence and guarantees total customer satisfaction. Nanotec´s Cervantes FullMode Atomic Force Microscope (AFM) in its several configurations allows not only imaging samples with atomic precision but also the study of magnetic, electronic and mechanical properties at the nanoscale, making it a powerful tool for physicists, chemists, biologists and engineers willing to characterize their samples at the nanometer scale. Its robust design provides strong mechanical stability to ensure high imaging resolution, and its semi-automated and open design allows scientists to exploit the capability of SPM to its maximum for both research and academic purposes. Nanotec Electronica also provides Dulcinea Control Systems, with an open and modular design that facilitates interfacing with any other standard AFM/SNOM/STM system available in the market. Highly versatile, it allows different modes of operation from Contact Mode to Frequency Modulation Mode and lithography ensuring a reliable and accurate performance of all SPM systems. Nanotec has also developed and freely distributes SPM software WSxM. Its user-friendly interface ensures easy operation of SPM microscopes and data processing. WSxM is available for its free download at www.nanotec.es. If you have any questions, or want any information about Nanotec Electronica, please contact us at: Nanotec Electronica
Centro Empresarial Euronova 3 Ronda de Poniente 12, 2º C 28760 Tres Cantos (Madrid) SPAIN Tel: +34-918043347 www.nanotec.es
Nanotec Red with offices in Spain, Argentina, Brazil, and the USA is dedicated to the transfer of Nanotechnology solutions to the retail sector, industrial companies, big and SME companies, and government entities in Spanish speaking countries.
Our team of experts is in constant contact with companies and government entities interested in embracing advanced technology to achieve their objectives and they rely on Nanotec Red to find the best solutions.
Talk to Nanotec Red if you want representation in these countries representing over 500MM people and thousands of companies that will adopt Nanotechnology over the coming 10 years. Rely on us, this is a great opportunity, don't let it pass.
Nanotec Red
Via Augusta 252 , planta 4, puerta A 08017 Barcelona España Tel: (+34) 902 009 469 Email: [email protected] Web: www.nanotecred.com
Raith manufactures high performance electron and ion beam lithography tools for nanotechnology applications in research and development. Raith tools are designed to meet the needs of researchers, designers, and engineers in both university and industry settings. Raith nanolithography products range from stand alone electron or ion beam lithography and nanoengineering tools (RAITH150TWO, e_LiNEplus, PIONEER, ionLiNE) to retrofit lithography attachments for SEM or SEM/FIB systems (ELPHY MultiBeam, ELPHY Plus, ELPHY Quantum). Raith electron beam lithography tools are in use throughout the world. Customers such as ST Microelectronics, The Massachusetts Institute of Technology in Boston or the IBM Research Centre are among the Raith clientele. The Raith ELPHY pattern generator family has become a standard for SEM and FIB based nanolithography during past 30 years. Raith GmbH
Exhibit Contact: Andreas REMSCHEID Konrad-Adenauer-Allee 8 - PHOENIX West 44263 Dortmund- Germany Phone: +49 (0)231 / 95004 - 0 Fax: +49 (0)231 / 95004 - 460 E-mail: [email protected] / [email protected] Web: www.raith.com
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nanoimmunotech is the first European company specialized in the functionalization, biological and physico-chemical characterization of nanoparticles. Our main area of activity is focused on biomedical, pharmaceutical and biotechnology companies, cosmetic, veterinary and agro-food market and research groups interested in the use of nanostructures with potential biotechnological applications. nanoimmunotech main objective is to become a world leader in Functionalization and Characterization of nanometric systems, offering products and services within the Biotechnology and Health sectors. The company has highly qualified and internationally recognized human resources, state-of-the-art laboratory capabilities, standardized protocols and finally, the know how to perform proper supervision, advice and validation of different nanosystems, as a first step to the previous use of nanoparticles in biotechnological applications. nanoimmunotech
Anaïs Normand Marketing Department Edificio Cero Emisiones Avenida de la Autonomía 7 50003 Zaragoza, Spain Mobile: (+34) 610 182 755 Phone: (+34) 876 440 071 Fax: (+34) 876 440 200 Email: [email protected] Website: www.nanoimmunotech.es
IOP Publishing provides publications through which leading-edge scientific research is distributed worldwide. Since launch we have expanded rapidly to become one of the leading international STM publishers. We have a global reach, with offices in Philadelphia, Washington DC, Mexico City, Munich, Moscow, St. Petersburg, Wroclaw, Beijing and Tokyo as well as Bristol and London in the UK Web: http://publishing.iop.org/
Schaefer Techniques has a long history as a supplier of high performance and reliable scientific instruments. We provide a wide range of products in the fields of vacuum technology, scanning probe microscopy, surface and materials analysis. During the TNT conference, we will present mainly four different products:
1. TT-AFM from AFM Workshop: the TT-AFM is a complete and affordable AFM for nanotechnology researchers, instruments innovators and teachers. Right out of the box, the TT-AFM includes all standard modes such as contact, dynamic, phase and lateral forces. All I/O electronic signals are accessible from rear panel connectors. With an open design, the LabView-based software is ready for custom applications.
2. GBS smartWLI product family, white light interferometers: Two economical microscopes called smartWLI-Basic and smartWLI-Extended as well as an upgrade to existing microscopes called smartWLI-microscope are available. The strength of these instruments is the economical price as well as an extremely fast calculation algorithm which makes them the fastest WLI on the market! smartWLI allows non-contact measurement with nanometer accuracy.
3. RHK Technology: RHK manufactures and supports customized, integrated UHV AFM/STM Systems and Controls used by University and Government Labs worldwide for advanced surface science research. RHK products include the new all-digital, ultra-fast, ultra low-noise R9 Universal SPM Controller; multi-purpose Beetle VT (25-1500 K) AFM/STM; rugged PanScan LT AFM/STM for mK and high-Tesla applications; sophisticated QuadraProbe LT AFM/STM 4-Probe (<6 K) for electrical measurements and transport studies; and specialized Prep/Analysis chambers and instruments.
4. Alemnis: In-situ SEM Indenter. Alemnis is specialized in developing, manufacturing and integrating customized instruments and tools for mechanical characterization and manipulation in all kinds of micro- and nanotechnology applications. The in-situ indenter is a compact test platform for in-situ materials characterization. It has been developed to work inside scanning electron microscopes as well as other types of microscopes. It includes long-range stick-slip piezoelectric actuators to position and test the samples with nanometer resolution.
Schaefer Techniques
1, rue du Ruisseau Blanc F-91620 NOZAY Tel : +33(0)1 64 49 63 50 e-mail : [email protected] Web : www.schaefer-tec.com
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Nanotechnology has been our everyday business since long before the term ever existed.
Founded in 1984 by Norbert Nold, Omicron started business by introducing the SPECTALEED and the legendary Ultra High Vacuum STM 1 as their first and highly successful products. The STM 1, which still delivers state-of-the-art performance even by today's standards in nearly 200 laboratories worldwide, firmly established Omicron's present position as the world market leader in UHV scanning probe microscopy.
Today, our products like, for example, the new NanoESCA or the UHV Gemini Column are right at the forefront of research. We are used to redefining the limits of the technically feasible again and again. More than 500 articles demonstrate this to the full. Many of them were published in leading journals such as Nature, Science, Physical Review Letters or Chemical Review Letters.
Omicron NanoTechnology GmbH
Limburger Str. 75 65232 Taunusstein Germany Tel: 06128/987-0 / Fax: 06128/987-185 email: [email protected] web: www.omicron.de
NanoInnova Technologies SL (www.nanoinnova.com) is a spin-off company of the Universidad Autónoma de Madrid. NanoInnova Technologies designs, develops and commercializes Chemical Vapor Deposition (CVD) instruments for bottom up graphene synthesis and chemically modified graphene.
A range of raw materials such as graphene oxide, reduced graphene oxide, Palladium (0) nanoparticles supported in reduced graphene oxide, etc, are part of the Nanoinnova Technologies SL portfolio. Nanoinnova Technologies SL is involved in the development and commercialization of new catalyst for fine chemical transformations such as cross coupling reactions, nanostructured modification of electrodes, new stationary phases in purification and new supports and functionalities of biomolecules.
Nanoinnova Technologies SL
Science Park of Madrid C/Faraday 7 28049-Madrid Tel: +34 918317366 Web: www.nanoinnova.com Email: [email protected]
This ambitious project is presented jointly by the Complutense and the Technical Universities of Madrid, together with other partner institutions located in the Campus such as the CIEMAT, the CSIC and the INIA. Its main purpose is to transform the Campus of Moncloa into an international reference regarding research, education and innovation. The project is structured as a collaborative agreement between the integrating institutions to achieve scientific excellence and internationalization; to guarantee connectivity and integration; to make the Campus a sustainable system that will boost student employment and contribute to innovation and development. Our aim is to create a plural and participatory campus, fuelled by the transforming power of diversity, exchanges and dialogue; an efficient and transparently-governed university campus, open to all its members and to all its partner institutions, as well as to the interaction with the social, economic and cultural fabric. The Campus commits itself to a specialization into six thematic clusters to achieve scientific and teaching excellence:
• Global Change and New Energies • Materials for the Future • Agriculture, Food Industry and Health • Innovative Medicine • Heritage • Sustainable mobility
The distinctive strengths in each of them converge to create unique configurations marked by their innovative and interdisciplinary character, being not only highly competitive at the European level, but also capable of producing a significant progress in the transfer of knowledge. Campus de Excelencia Internacional: Campus Moncloa
CEI Campus Moncloa Office Royal Botanic Gardens Building, Alfonso XIII Ciudad Universitaria 28040 Madrid, Spain www.campusmoncloa.es
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Irida Iberica is one of the youngest but most dynamic nanotechnology instruments providers in Spain. We introduce novel techniques and the best technological solutions for most of the nanotechnology applications challenges. Irida offers a unique value to price combination for a wide variety of surface analysis products like Optical Profilers or Atomic Force Microscopes, as well as the most versatile configurations for material science and biological samples analysis. Our products, manufactured by world leading companies, are some of the most sophisticated instruments in the market because of their cutting edge technology. But it is our service department that makes the difference because is what gives our clients the security of a nonstop research or production work.
Irida Iberica S.L.
Diligencia 9 28108 Madrid, Spain Tel. +34911130824 Email: [email protected] Web: www.irida.es
Renishaw is a global company with core skills in measurement, motion control, spectroscopy and precision machining. We develop innovative products that significantly advance our customers' operational performance - from improving manufacturing efficiencies and raising product quality, to maximising research capabilities and improving the efficacy of research procedures.
Renishaw manufactures a wide range of optical spectroscopy products, including: Raman microscopes, Raman analyzers for scanning electron microscopes, combined systems for Raman/SPM measurements etc...Recent developments in ultra-fast imaging enables you to produce Raman chemical images far faster than has been possible before. Raman images that used to take hours to produce can now be created in minutes. This technology is perfectly suited to carbon measurements for Nanotechnology (Graphene, Carbon Nanotubes etc...)
Renishaw Ibérica, S.A.U.
Gavà Park C. Imaginació, 3 08850 GAVÀ Barcelona Email: [email protected] Web: www.renishaw.es
The TechnoFusión project, currently in a preparatory study phase, involves the construction of a Singular Scientific-Technical Facility (National Centre for Fusion Technologies - TechnoFusión) in the Region of Madrid, Spain, creating the required infrastructure for the development of the technologies required for future commercial fusion reactors, and assuring participation by Spanish research groups and companies. The performance of materials and components under the extreme conditions of a fusion reactor is largely unknown. For this purpose, facilities are required for the manufacture, testing and analysis of critical materials. Additional resources will be needed to develop and exploit numerical codes for the simulation of materials in special environments, to develop remote handling technologies and other areas related to the management of liquid metals used in several components of the reactor. TechnoFusión Scientific-Technical Facility will consist of a complex of seven large research areas related to fusion technologies: material production and processing, material irradiation, plasma-wall interaction studies, liquid metal technologies, material characterization techniques, remote handling technologies and computer simulation. Many of these technological areas will be unique in the world. The goal of TechnoFusión is to bring together sufficient human and material resources to contribute significantly to the development of a safe, clean, and inexhaustible source of energy for future generations. Web: www.technofusion.es
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UAM (Universidad Autónoma de Madrid, with 2500 teaching staff and 34000 students) and CSIC (Spanish National Research Council, that has in UAM's campus four institutes and five mixed UAM+CSIC institutes, with a research staff of more than 2000) joined forces to host a large number of top scientists from both institutions that carry out highly competitive research in several areas. The aggregation of the UAM and CSIC in the International Campus of Excellence (CEI), along with other research and transfer centres, companies, business organisations, local authorities and Madrid regional authorities, will give significant impetus to improve the Campus teaching, research and knowledge transfer capacities. The project’s main goals are two: to increase the international relevance of this particular Campus of Excellence, seeking that the CEI UAM+CSIC be the leading Spanish campus by 2015 and among the 100 top universities in the world and top 50 in Europe and to integrate it very closely with its surroundings, in order to lead the social, cultural and economic development of Madrid North. Web: http://campusexcelencia.uam-csic.es
The Spanish Institute for Foreign Trade (ICEX) ("Instituto Español de Comercio Exterior") is the Spanish Government agency serving Spanish companies to promote their exports and facilitate their international expansion, assisted by the network of Spanish Embassy’s Economic and Commercial Offices and, within Spain, by the Regional and Territorial Offices. It is part of the Spanish Ministry of Economy and Competitiveness (“Ministerio de Economía y Competitividad”). España, Technology for life: www.spainbusiness.com Web: www.icex.es
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TNT2012 Speakers
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Pablo Alonso González (CIC nanoGUNE Consolider, Spain) "Optical nano-imaging of gate-tuneable graphene plasmons"
Oral Senior Plenary Session 29292929
Masakazu Aono (MANA / NIMS, Japan) "Synaptic characteristics of the atomic switch"
Keynote Plenary Session 30303030
Takao Aoyagi (MANA / NIMS, Japan) "Molecular design of Smart Biomaterials for Nano Life"
Keynote Plenary Session 32323232
Carlos Arroyo Rodríguez (Delft University of Technology , Netherlands) "Quantum interference effects on charge transport through a single benzene ring"
Oral Senior Plenary Session 34343434
Joël Azevedo (CEA Saclay / SPEC, France) "Graphene and carbon nanotubes film organization with a new solution-based method: a substrate
independent transfer for transparent electrode applications”
Oral PhD Parallel Session
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Myriam Barrejón (Universidad de Castilla-La Mancha, Spain) "Synthesis of a new GO-C60 hybrid by “click” chemistry"
Oral PhD Parallel Session 37373737
Tiziana Bond (Lawrence Livermore National Lab, USA) "Plasmonic to enhance sense and sensitivity at the nanoscale"
Keynote Plenary Session ----
Paolo Bondavalli (Thales Research and Technology, France) "Electrodes based on mixture of Graphene/Graphite/Carbon nanotubes obtained by a new dynamic
spray-gun technique for supercapacitor related applications"
Oral Senior Plenary Session
38383838
Eduardo M. Bringa (Universidad Nacional de Cuyo, Argentina) "Multiscale simulations of irradiated nanofoams"
Keynote Plenary Session 40404040
Andreu Cabot (IREC, Spain) "I2–II–IV–VI4 Nanocrystals: Synthesis and Thermoelectric Properties"
Oral Senior Plenary Session 41414141
Fernando Calle Gómez (ISOM and ETSI Telecomunicación / UPM, Spain) "Nanotechnology for high frequency communications: nitrides and graphene"
Keynote Plenary Session 42424242
Mercedes Carrascosa (Universidad Autónoma de Madrid, Spain) "Applications of photovoltaic fields of iron doped LiNbO3 in nanotechnology"
Oral Senior Parallel Session 44444444
Jean-Christophe Charlier (Université Catholique de Louvain, Belgium) "Electronic properties and quantum transport in doped and defective graphene"
Keynote Plenary Session 46464646
Eugene Choulkov (DIPC - UPV/EHU, Spain) "Electronic Stucture of Topological Insulators"
Keynote Plenary Session 48484848
Fabiano Corsetti (Asociacion CIC nanoGUNE, Spain) "New implementations of the orbital minimization method in the SIESTA code"
Oral Senior Parallel Session 49494949
Aron W. Cummings (Sandia National Laboratories, United States) "Enhanced Performance of Carbon Nanotube Field-Effect Transistors Due to Gate-Modulated Electrical
Contact Resistance"
Oral Senior Plenary Session
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Silvano de Franceschi (CEA, France) "Silicon-based quantum electronics"
Keynote Plenary Session 53535353
Carmen Del Hoyo Martínez (University of Salamanca, Spain) "Nanoclays as adsorbents of organic contaminants for a sustainable application"
Oral Senior Parallel Session 54545454
Francisco Del Pozo (CTB-UPM, Spain)
Oral Senior Parallel Session ----
Alexandr Dobrovolsky (Linkoping University, Sweden) "Optical studies and defect properties of GaP/GaNP core/shell nanowires"
Oral Senior Parallel Session 56565656
Index alphabetical order
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Maysoun Douas (Inst. Ciencia Materiales de Madrid (ICMM),Spain) "Identification of nanocavities water content"
Oral PhD Parallel Session 57575757
Alberto Eljarrat Ascunce (Universitat de Barcelona, Spain) "EELS-HAADF spectrum imaging for characterization of (AlGa)N multilayer heterostructures."
Oral PhD Parallel Session 59595959
Toshiaki Enoki (Tokyo Institute of Technology, Japan) "Electronic properties of graphene edges"
Keynote Plenary Session 61616161
Roch Espiau de Lamaestre (CEA-Leti, France) "Integration of plasmonics within a CMOS environment"
Keynote Plenary Session 63636363
Virginia Estévez (Universidad del Pais Vasco, Spain) "Angular dependence of the tunneling magnetoresistance in nanoparticle arrays"
Oral Senior Plenary Session 64646464
Maël Dehlinger (CNRS-CINaM, France) "Towards sub-100nm resolution chemical mapping by XRF combined to simultaneous topography"
Oral Senior Plenary Session 65656565
Michael Fluss (Lawrence Livermore National Laboratory, USA) "Nano-dispersed particles in Fe(Crx) and their performance under dual (He+Fe) and triple (H+He+Fe) ion
beam irradiation"
Keynote Plenary Session
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Katerina Foteinopoulou (Institute of Optoelectronics and Microsystems (ISOM) and ETSII, UPM, Spain) "Entropy-driven phase transition in dense packings of athermal chain molecules"
Oral Senior Parallel Session
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Alberto Fraile García (Institute of Nuclear Fusion, Spain) "Molecular Dynamics simulation of liquid metals for nuclear fusion technology"
Oral PhD Parallel Session 70707070
Luis S. Froufe-Pérez (Inst. de Estructura de la Materia, CSIC, Spain) "Light emission statistics as a local probe for structural phase switching"
Oral Senior Plenary Session 72727272
Javier García de Abajo (IQFR-CSIC, Spain) "Graphene plasmonics"
Keynote Plenary Session 74747474
Sandra García-Gil (CEMES-CNRS, France) "Progress towards a single swap molecule with Ruthenium complexes: DFT study on a gold surface"
Oral Senior Parallel Session 75757575
Mari Cruz García Gutiérrez (Instituto de Estructura de la Materia, IEM-CSIC, Spain) "Tuning physical properties of polymers by nanoconfinement"
Oral Senior Plenary Session 76767676
Francisco José García Vidal (UAM, Spain) "Light-matter coupling mediated by surface plasmons"
Keynote Plenary Session 78787878
David Garoz (Institute of Nuclear Fusion, Spain) "Crack mechanical failure in ceramic materials under ion irradiation: case of lithium niobate crystal"
Oral Senior Parallel Session 79797979
Philippe Ghosez (Université de Liège, Belgium) “Coupling of lattice modes in oxides superlattices: Wedding of three"
Keynote Plenary Session 80808080
María José Gómez-Escalonilla (U. Castilla-La Mancha, Spain) "Photochemical Evidence of Electronic Interwall Communication in Double-Wall Carbon Nanotubes"
Oral Senior Parallel Session 81818181
Raquel Gómez-Medina (Universidad Autónoma de Madrid, Spain) "Negative scattering asymmetry parameter for dipolar particles: Unusual reduction of the transport
mean free path and radiation pressure"
Oral Senior Parallel Session
83838383
Nuria Gordillo García (Instituto de Fusión Nuclear/ ETSI de Industriales-UPM, Spain) "Nanostructured tungsten as a first wall material for the future nuclear fusion reactors"
Oral Senior Plenary Session 85858585
Kurt Gothelf (Aarhus University, Denmark) "DNA programmed assembly of molecules"
Keynote Plenary Session 86868686
Stephan Götzinger (Max Planck Institute for the Science of Light, Germany) "Optical antennas: nanoscience meets quantum optics"
Keynote Plenary Session 199199199199
Peter Gruetter (McGill University, Canada) "What can AFM tell us about organic photovoltaic systems?"
Keynote Plenary Session 87878787
Francisco Guinea (ICMM-CSIC, Spain) "Interaction effects in graphene heterostructures"
Keynote Plenary Session 88888888
Kelli Hanschmidt (Institute of Physics, University of Tartu, Estonia) "Properties optimisation of titania microfibers by direct drawing"
Oral PhD Parallel Session 89898989
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Kikuo Harigaya (Nanosystem Research Institute, AIST, Japan) "Theoretical Study of Edge States in BC2N Nanoribbons with Zigzag Edges"
Oral Senior Parallel Session 91919191
Anwar Hasmy (Universidad Simón Bolívar, Venezuela) "Nanotechnology in Latin America and the Caribbean: Current Situation and perspective"
Keynote Plenary Session 93939393
Antonio Hernando (Universidad Complutense, Spain) "Metallic microwires as non-reflective microwave systems"
Keynote Plenary Session 94949494
Tibor Hianik (Comenius University, Slovakia) "Application of nanostructures in aptamer based biosensors"
Keynote Plenary Session 95959595
Kevin Inderbitzin (U. Zurich - Physics-Institute, Switzerland) "Ultrafast X-Ray Nanowire Single-Photon Detectors and Their Energy-Dependent Response"
Oral PhD Parallel Session 97979797
Masashi Ishii (National Instit. for Materials Science (NIMS), Japan) "Nano-probing of the surface excited by keV photon: What should we detect for high spatial
resolution?"
Keynote Plenary Session
99999999
José Ignacio Izpura (GMME-CEMDATIC. UPM, Spain) "On the origin of RTS noise in nanoFETs "
Oral Senior Parallel Session 101101101101
Christian Joachim (CEMES/CNRS - GNS, France) "Design of Atom and Single Molecule Boolean Logic gates"
Keynote Plenary Session 103103103103
Gerald Kada (Agilent Technologies, Austria) "Calibrated Nanoscale Capacitance and Dopant Profile Measurements using a novel Nearfield Scanning
Microwave Microscope"
Oral Senior Parallel Session
104104104104
W. Joshua Kennedy (NASA Johnson Space Center, United States) "Optical limiting by absorption bleaching in carbon nanotube devices: comparison of field-induced and
electrochemically-induced charge injection “
Oral Senior Parallel Session
106106106106
Vladimir Labunov (Belarusian State University of Informatics and Radioelectronics, Belarus) "Novel “Carbon Nanotube/Graphene Layer” Nanostructures Obtained by Injection CVD Method for
Electronic Applications "
Oral Senior Parallel Session
107107107107
Uzi Landman (Georgia Tech, USA) "Emergent non-scalable behavior in the nanoscale"
Keynote Plenary Session 109109109109
Yael Liebes (Ben Gurion University of the Negev, Israel) "Fabrication and characterization of nanopores in Si based materials"
Oral PhD Parallel Session 110110110110
Cheng-An Lin (Chung Yuan Christian University, Taiwan) "Rapid Conversion from Protein-Caged Nanomaterials to Microbubbles: A Sonochemical Route toward
Bimodal Imaging Agents"
Oral Senior Plenary Session
111111111111
Dan Lis (University of Namur - FUNDP, Belgium) "Nanopillars as Plasmonic Platform to Enhance Nonlinear Vibrational Sum-Frequency Generation Spectroscopy"
Oral Senior Plenary Session 112112112112
Fco. Javier Llorca (IMDEA Materiales, Spain) "Nanoscale Metallic and Metal-Ceramic Multilayers for Radiation-Resistant Applications"
Keynote Plenary Session 114114114114
Maria Jesús López Bosque (Parc Cientific de Barcelona/Plataforma de Nanotecnologia, Spain) "Hierarchical micro-nano-structures for cell adhesion studies"
Oral Senior Parallel Session
115115115115
Fernando López-Tejeira (Instituto de Estructura de la Materia (IEM-CSIC), Spain) "Refractive Index Sensing based on Plasmonic Fano-like Interference"
Oral Senior Parallel Session 117117117117
Raquel Lucena García (I. de Catálisis y Petroleoquímica-CSIC,Spain) "New Intermediate band sulphide nanoparticles acting in the full visible light range spectra as an active
photocatalyst"
Oral PhD Parallel Session
118118118118
Antonio Luque (Universidad Politécnica de Madrid, Spain) "Quantum Dot Intermediate Band Solar Cells: Issues for an Attractive Concept"
Keynote Plenary Session 120120120120
Maria Ada Malvindi (Italian Institute of Technology, Center for Bio-Molecular Nanotechnologies@Unile, Italy) "Silica nanostructures toxicity assessment and their potential for biomedical applications"
Oral Senior Parallel Session
122122122122
José María Riola (Ministry of Defense, Spain) "Nanotechnologies for security and defense - Sectors of interest"
Oral Senior Plenary Session ----
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Manuel Marqués (Universidad Autónoma de Madrid, Spain) "Plasmonic nanoparticle chain in a light field: a resonant optical sail"
Oral Senior Plenary Session 124124124124
Richard Martel (Université de Montreal, Canada) "Environmental Effects in Carbon Nanotube and graphene-based Transistors"
Keynote Plenary Session 200200200200
Gema Martínez-Criado (European Synchrotron Radiation Facility, France) "Imaging the carrier confinement within a single nanowire"
Oral Senior Parallel Session 111125252525
Remo Masut (École Polytechnique de Montréal, Canada) "Reciprocal space and transmission electron microscopy study of heterogeneous GaP:MnP magnetic
epilayers containing MnP nanoclusters"
Oral Senior Parallel Session
126126126126
Diogo Mata (University of Aveiro, Portugal) "Spatial and temporal control of osteoblastic cells proliferation on electroconductive carbon nanotube-
based bone grafts"
Oral PhD Parallel Session
128128128128
Sébastien Maussang (Renishaw Ibérica, Spain) "Recent advances in fast imaging Raman technology for nano materials characterisation"
Oral Senior Parallel Session 130130130130
Jean-Louis Mergny (INSERM U869 – U.Bordeaux Segalen, France) "Unusual nucleic acid structures for DNA-based nanotechnologies"
Keynote Plenary Session 131131131131
Rodolfo Miranda (UAM/IMDEA Nanociencia, Spain) "Evidence for magnetic order in a purely organic 2D layer adsorbed on epitaxial graphene"
Keynote Plenary Session 132132132132
Laurens W. Molenkamp (Wurzburg University, Germany) "Dirac fermions in HgTe quantum wells"
Keynote Plenary Session 133133133133
Juan Ramon Morante (IREC, Spain) "Three dimensional electrodes base on core/shell nanowires for photoelectrochemical cells"
Oral Senior Parallel Session 134134134134
Edgar Muñoz (Instituto de Carboquímica (ICB-CSIC), Spain) "Metal-Carbon Nanohybrid Foams: from Laser Chemistry to Nanochemistry"
Oral Senior Parallel Session 135135135135
Jeffrey B. Neaton (Lawrence Berkeley National Laboratory, USA) "Understanding Electronic Structure and Charge Transport in Single-Molecule Junctions"
Keynote Plenary Session 137137137137
Bernat Olivera (University of Alicante, Spain) "Measurement of the capacitance across a tunnel barrier"
Oral PhD Parallel Session 138138138138
Cornelia G. Palivan (University of Basel, Switzerland) "Protein-polymer nanoreactors and processors act as artificial organelles"
Oral Senior Parallel Session 139139139139
Ovidio Y. Peña Rodríguez (IFN - ETSII Madrid /UPM, Spain) "Plasmonic nanoparticles for the protection of the final optics in inertial confinement fusion facilities:
Capabilities and limitations"
Keynote Plenary Session
141141141141
Daniel Pérez-Estévez (University of Vigo, Spain) "Functionalizated magnetic nanoparticles for biodetection, imaging and separation of Mytilus
galloprovincialis larvae using NIT-zipper® technology”
Oral Senior Parallel Session
142142142142
Laetitia Philippe (EMPA Materials Science & Technology, Switzerland) "Urchin-inspired zinc oxide as building blocks for nanostructured solar cells"
Oral Senior Plenary Session 143143143143
Marcos Pita (Inst. of Catalysis and Petroleumquemistry-CSIC,Spain) "Improving the Direct Electron Transfer Efficiency in Laccase Electrodes for Biofuel Cell Cathodic Reactions"
Oral Senior Parallel Session 145145145145
Julio Plaza (Technological Institute "La Marañosa" (Ministry of Defense), Spain) "Strategies and activities in nano"
Oral Senior Plenary Session 147147147147
Dieter Pohlenz (Omicron NanoTechnology GmbH, Germany) "High Precision local electrical Probing: A New Low Temperature 4-Tip STM with Gemini UHV-SEM Navigation"
Oral Senior Parallel Session 148148148148
Dietmar Pum (BOKU - University of Natural Resources and Life Sciences, Austria) "S-layer proteins as patterning elements in the life and non-life sciences"
Keynote Plenary Session 149149149149
Juris Purans (University of Latvia, Latvia) "Near field X-ray spectromicroscopies: new tools for nanoscience"
Keynote Plenary Session 150150150150
Akhilesh Rai (University of Coimbra, Portugal) "One pot synthesis of potent antimicrobial gold nanoparticles"
Oral Senior Parallel Session ----
Rebeca Ribeiro (Laboratoire National des ChamO Magnetiques Inteses, France) "Unveiling the Landau Levels Structure of Graphene Nanoribbons"
Oral PhD Parallel Session 152152152152
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Carlos Rivera (Technological Institute "La Marañosa" (Ministry of Defense), Spain) "Graphene potentialities for space and defense applications: focus on mechanical properties"
Oral Senior Plenary Session 154154154154
Juan Rodríguez (Universidad Nacional de Ingenieria, Peru) "Supported Nanomaterials for Photocatalytic Water disinfection at rural areas: From Lab. Scale to on site
experiments"
Keynote Plenary Session
156156156156
Miguel Romera (Universidad Politécnica de Madrid, Spain) "Substantial increase of the critical current on a Spin Transfer Nanopillar by adding
an Fe/Gd/Fe trilayer"
Oral Senior Parallel Session
157157157157
Volker Rose (Argonne National Laboratory, USA) "New Capabilities at the Interface of X-rays and Scanning Tunneling Microscopy"
Keynote Plenary Session 159159159159
Gabino Rubio-Bollinger (Universidad Autónoma de Madrid, Spain) "Mechanical properties of freely suspended atomically thin dielectric layers of mica"
Oral Senior Plenary Session 160160160160
Amalia Ruíz (ICMM-CSIC, Spain) "An Efficient MRI Contrast Agent Based on PEGylated Iron Oxide Nanoparticles"
Oral PhD Parallel Session 161161161161
Carlos Sabater (Universidad de Alicante, Spain) "Creating nanowires with atomic precision"
Oral PhD Parallel Session 163163163163
Akira Saito (Osaka University, Japan) "Nanoscale elemental analysis and applications using STM combined with brilliant hard X-rays"
Keynote Plenary Session 165165165165
Beatriz Salinas (Centro Nacional de Investigaciones Cardiovasculares, Spain) "Biorthogonal chemistry for the functionalization of superparamagnetic nanoparticles: cross olefin metathesis"
Oral PhD Parallel Session 167167167167
Pablo San José (Instituto de Estructura de la Materia (CSIC), Spain) "AC Josephson effect in finite-length nanowire junctions with Majorana modes"
Oral Senior Plenary Session 169169169169
Cristina Sánchez (CTB-UPM, Spain) "Thermal and mechanical effects of different excitation modes based on low frequency laser modulation
in optical hyperthermia"
Oral PhD Parallel Session
170170170170
Rafael Sánchez (ICMM-CSIC, Spain) "Maximal entanglement out of transport through double quantum dots"
Oral Senior Parallel Session 172172172172
Daniel Sánchez Portal (CFM/EHU-CSIC, Spain) “TDDFT simulations of the energy loss of moving projectiles in solids and nanostructures"
Keynote Plenary Session 173173173173
Marcus Semones (WaveGuide Corp., USA) “WaveGuide's u-NMR and Magnetic Nanoswitches for Security and Defense Applications"
Keynote Plenary Session 175175175175
Paz Sevilla (Universidad Complutense de Madrid, Spain) "Fluorescence and Raman characterization of a transport system formed by the anti tumoral drug
emodin, silver nanoparticles and porous silicon”
Oral Senior Parallel Session
176176176176
We-Hyo Soe (IMRE / A*STAR, Singapore) "Manipulation of molecular quantum states in an STM tunneling junction using classical metal atom inputs"
Keynote Plenary Session 178178178178
David Soriano (Institut Català de Nanotecnologia (ICN), Spain) "Disorder-induced Randomization of Spin Polarization and Interfacially Protected Surface States in Three-
dimensional Models of Topological Insulators"
Oral Senior Plenary Session
179179179179
Marek Szymonski (Jagiellonian University/NANOSAM, Poland) "Atomically precise construction and electronic properties of dangling-bond nanostructures on hydrogen
passivated Ge(001) surface"
Keynote Plenary Session
181181181181
Philippe Tamarat (LP2N, Université de Bordeaux, Institut d'Optique Graduate School & CNRS, France) "Efficient biexciton emission in single CdSe nanocrystals"
Oral Senior Plenary Session
182182182182
Concha Tojo (University of Vigo, Spain) "Microemulsions as reaction media for the synthesis of bimetallic nanoparticles"
Oral Senior Parallel Session 184184184184
Jessica Topple (McGill University, Canada) "Small Molecule Organic Photovoltaics at the Nanoscale"
Oral Senior Parallel Session 186186186186
Alessandro Troisi (University of Warwick, UK) "Atomistic Models of Charge Separation and Recombination in Organic Photovoltaics Interfaces"
Keynote Plenary Session 188188188188
18 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
TNT2012
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Joaquin Tutor (ETSI-ICAI Universidad Pontificia Comillas, Spain) "Present and Perspectives on Dissemination and Training in Nanotechnology in IberoAmerica: Red
NANODYF – CYTED"
Oral Senior Plenary Session
189189189189
Takashi Uchihashi (NIMS, Japan) "Superconductivity at adatom/molecule-induced silicon surfaces and interfaces"
Keynote Plenary Session 190190190190
Yoshio Ukyo (Toyota R&D Labs, Japan) “Microstructural change of li(NiCo)O2 based materials of li ion battery during charge and discharg"
Keynote Plenary Session 192192192192
Helena Varela (Universidad de Alicante, Spain) "Monitoring the oxygen content in graphene oxide"
Oral Senior Plenary Session 194194194194
Hiroshi Yao (University of Hyogo, Japan) "Postsynthetic Asymmetric Transformation of Boronic-Acid-Protected Gold Nanoclusters Studied by
Magnetic Circular Dichroism (MCD) and Electronic Circular Dichroism (ECD)"
Oral Senior Plenary Session
195195195195
Mariusz Zdrojek (Warsaw University of Technology, Poland) "Laser heating control with polarized light in isolated multi-walled carbon nanotubes"
Oral Senior Plenary Session 197197197197
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 19
TNT2012 Speakers
pagepagepagepage
Masakazu Aono (MANA / NIMS, Japan) "Synaptic characteristics of the atomic switch"
30303030
Takao Aoyagi (MANA / NIMS, Japan) "Molecular design of Smart Biomaterials for Nano Life"
32323232
Tiziana Bond (Lawrence Livermore National Lab, USA) "Plasmonic to enhance sense and sensitivity at the nanoscale"
----
Eduardo M. Bringa (Universidad Nacional de Cuyo, Argentina) "Multiscale simulations of irradiated nanofoams"
40404040
Fernando Calle Gómez (ISOM and ETSI Telecomunicación / UPM, Spain) "Nanotechnology for high frequency communications: nitrides and graphene"
42424242
Jean-Christophe Charlier (Université Catholique de Louvain, Belgium) "Electronic properties and quantum transport in doped and defective graphene"
46464646
Eugene Choulkov (DIPC - UPV/EHU, Spain) "Electronic Stucture of Topological Insulators"
48484848
Silvano de Franceschi (CEA, France) "Silicon-based quantum electronics"
53535353
Toshiaki Enoki (Tokyo Institute of Technology, Japan) "Electronic properties of graphene edges"
61616161
Roch Espiau de Lamaestre (CEA-Leti, France) "Integration of plasmonics within a CMOS environment"
63636363
Michael Fluss (Lawrence Livermore National Laboratory, USA) "Nano-dispersed particles in Fe(Crx) and their performance under dual (He+Fe) and triple (H+He+Fe) ion beam
irradiation"
66666666
Javier García de Abajo (IQFR-CSIC, Spain) "Graphene plasmonics"
74747474
Francisco José García Vidal (UAM, Spain) "Light-matter coupling mediated by surface plasmons"
78787878
Philippe Ghosez (Université de Liège, Belgium) “Coupling of lattice modes in oxides superlattices: Wedding of three"
80808080
Kurt Gothelf (Aarhus University, Denmark) "DNA programmed assembly of molecules"
86868686
Stephan Götzinger (Max Planck Institute for the Science of Light, Germany)
"Optical antennas: nanoscience meets quantum optics"
199199199199
Peter Gruetter (McGill University, Canada) "What can AFM tell us about organic photovoltaic systems?"
87878787
Francisco Guinea (ICMM-CSIC, Spain) "Interaction effects in graphene heterostructures"
88888888
Anwar Hasmy (Universidad Simón Bolívar, Venezuela) "Nanotechnology in Latin America and the Caribbean: Current Situation and perspective"
93939393
Antonio Hernando (Universidad Complutense, Spain) "Metallic microwires as non-reflective microwave systems"
94949494
Keynotes
20 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
TNT2012
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rs
pagepagepagepage
Tibor Hianik (Comenius University, Slovakia) "Application of nanostructures in aptamer based biosensors"
95959595
Masashi Ishii (National Instit. for Materials Science (NIMS), Japan) "Nano-probing of the surface excited by keV photon: What should we detect for high spatial resolution?"
99999999
Christian Joachim (CEMES/CNRS - GNS, France) "Design of Atom and Single Molecule Boolean Logic gates"
103103103103
Uzi Landman (Georgia Tech, USA) "Emergent non-scalable behavior in the nanoscale"
109109109109
Fco. Javier Llorca (IMDEA Materiales, Spain) "Nanoscale Metallic and Metal-Ceramic Multilayers for Radiation-Resistant Applications"
114114114114
Antonio Luque (Universidad Politécnica de Madrid, Spain) "Quantum Dot Intermediate Band Solar Cells: Issues for an Attractive Concept"
120120120120
Richard Martel (Université de Montreal, Canada) "Environmental Effects in Carbon Nanotube and graphene-based Transistors"
200200200200
Jean-Louis Mergny (INSERM U869 – U.Bordeaux Segalen, France) "Unusual nucleic acid structures for DNA-based nanotechnologies"
131131131131
Rodolfo Miranda (UAM/IMDEA Nanociencia, Spain) "Evidence for magnetic order in a purely organic 2D layer adsorbed on epitaxial graphene"
132132132132
Laurens W. Molenkamp (Wurzburg University, Germany) "Dirac fermions in HgTe quantum wells"
133133133133
Jeffrey B. Neaton (Lawrence Berkeley National Laboratory, USA)
"Understanding Electronic Structure and Charge Transport in Single-Molecule Junctions"
137137137137
Ovidio Y. Peña Rodríguez (IFN - ETSII Madrid /UPM, Spain) "Plasmonic nanoparticles for the protection of the final optics in inertial confinement fusion facilities: Capabilities
and limitations"
141141141141
Dietmar Pum (BOKU - University of Natural Resources and Life Sciences, Austria) "S-layer proteins as patterning elements in the life and non-life sciences"
149149149149
Juris Purans (University of Latvia, Latvia) "Near field X-ray spectromicroscopies: new tools for nanoscience"
150150150150
Juan Rodríguez (Universidad Nacional de Ingenieria, Peru) "Supported Nanomaterials for Photocatalytic Water disinfection at rural areas: From Lab. Scale to on site
experiments"
156156156156
Volker Rose (Argonne National Laboratory, USA) "New Capabilities at the Interface of X-rays and Scanning Tunneling Microscopy"
159159159159
Akira Saito (Osaka University, Japan) "Nanoscale elemental analysis and applications using STM combined with brilliant hard X-rays"
165165165165
Daniel Sánchez Portal (CFM/EHU-CSIC, Spain) “TDDFT simulations of the energy loss of moving projectiles in solids and nanostructures"
173173173173
Marcus Semones (WaveGuide Corp., USA) “WaveGuide's u-NMR and Magnetic Nanoswitches for Security and Defense Applications"
175175175175
We-Hyo Soe (IMRE / A*STAR, Singapore) "Manipulation of molecular quantum states in an STM tunneling junction using classical metal atom inputs"
178178178178
Marek Szymonski (Jagiellonian University/NANOSAM, Poland) "Atomically precise construction and electronic properties of dangling-bond nanostructures on hydrogen
passivated Ge(001) surface"
181181181181
Alessandro Troisi (University of Warwick, UK) "Atomistic Models of Charge Separation and Recombination in Organic Photovoltaics Interfaces"
188188188188
Takashi Uchihashi (NIMS, Japan) "Superconductivity at adatom/molecule-induced silicon surfaces and interfaces"
190190190190
Yoshio Ukyo (Toyota R&D Labs, Japan) “Microstructural change of li(NiCo)O2 based materials of li ion battery during charge and discharg"
192192192192
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 21
TNT2012 Speakers
pagepagepagepage
Pablo Alonso González (CIC nanoGUNE Consolider, Spain) "Optical nano-imaging of gate-tuneable graphene plasmons"
29292929
Carlos Arroyo Rodríguez (Delft University of Technology , Netherlands) "Quantum interference effects on charge transport through a single benzene ring"
34343434
Paolo Bondavalli (Thales Research and Technology, France) "Electrodes based on mixture of Graphene/Graphite/Carbon nanotubes obtained by a new dynamic spray-gun
technique for supercapacitor related applications"
38383838
Andreu Cabot (IREC, Spain) "I2–II–IV–VI4 Nanocrystals: Synthesis and Thermoelectric Properties"
41414141
Aron W. Cummings (Sandia National Laboratories, United States) "Enhanced Performance of Carbon Nanotube Field-Effect Transistors Due to Gate-Modulated Electrical Contact
Resistance"
51515151
Virginia Estévez (Universidad del Pais Vasco, Spain) "Angular dependence of the tunneling magnetoresistance in nanoparticle arrays"
64646464
Maël Dehlinger (CNRS-CINaM, France) "Towards sub-100nm resolution chemical mapping by XRF combined to simultaneous topography"
65656565
Luis S. Froufe-Pérez (Inst. de Estructura de la Materia, CSIC, Spain)
"Light emission statistics as a local probe for structural phase switching"
72727272
Mari Cruz García Gutiérrez (Instituto de Estructura de la Materia, IEM-CSIC, Spain) "Tuning physical properties of polymers by nanoconfinement"
76767676
Nuria Gordillo García (Instituto de Fusión Nuclear/ ETSI de Industriales-UPM, Spain) "Nanostructured tungsten as a first wall material for the future nuclear fusion reactors"
85858585
Cheng-An Lin (Chung Yuan Christian University, Taiwan) "Rapid Conversion from Protein-Caged Nanomaterials to Microbubbles: A Sonochemical Route toward Bimodal
Imaging Agents"
111111111111
Dan Lis (University of Namur - FUNDP, Belgium) "Nanopillars as Plasmonic Platform to Enhance Nonlinear Vibrational Sum-Frequency Generation Spectroscopy"
112112112112
José María Riola (Ministry of Defense, Spain) "Nanotechnologies for security and defense - Sectors of interest"
----
Manuel Marqués (Universidad Autónoma de Madrid, Spain) "Plasmonic nanoparticle chain in a light field: a resonant optical sail"
124124124124
Laetitia Philippe (EMPA Materials Science & Technology, Switzerland) "Urchin-inspired zinc oxide as building blocks for nanostructured solar cells"
143143143143
Julio Plaza (Technological Institute "La Marañosa" (Ministry of Defense), Spain) "Strategies and activities in nano"
147147147147
Carlos Rivera (Technological Institute "La Marañosa" (Ministry of Defense), Spain) "Graphene potentialities for space and defense applications: focus on mechanical properties"
154154154154
Gabino Rubio-Bollinger (Universidad Autónoma de Madrid, Spain) "Mechanical properties of freely suspended atomically thin dielectric layers of mica"
160160160160
Pablo San José (Instituto de Estructura de la Materia (CSIC), Spain) "AC Josephson effect in finite-length nanowire junctions with Majorana modes"
169169169169
Orals - senior
(plenary session)
22 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
TNT2012
Sp
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pagepagepagepage
David Soriano (Institut Català de Nanotecnologia (ICN), Spain) "Disorder-induced Randomization of Spin Polarization and Interfacially Protected Surface States in Three-
dimensional Models of Topological Insulators"
179179179179
Philippe Tamarat (LP2N, Université de Bordeaux, Institut d'Optique Graduate School & CNRS,
France) "Efficient biexciton emission in single CdSe nanocrystals"
182182182182
Joaquin Tutor (ETSI-ICAI Universidad Pontificia Comillas, Spain) "Present and Perspectives on Dissemination and Training in Nanotechnology in IberoAmerica: Red NANODYF –
CYTED"
189189189189
Helena Varela (Universidad de Alicante, Spain) "Monitoring the oxygen content in graphene oxide"
194194194194
Hiroshi Yao (University of Hyogo, Japan) "Postsynthetic Asymmetric Transformation of Boronic-Acid-Protected Gold Nanoclusters Studied by Magnetic
Circular Dichroism (MCD) and Electronic Circular Dichroism (ECD)"
195195195195
Mariusz Zdrojek (Warsaw University of Technology, Poland) "Laser heating control with polarized light in isolated multi-walled carbon nanotubes"
197197197197
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 23
TNT2012 Speakers
pagepagepagepage
Mercedes Carrascosa (Universidad Autónoma de Madrid, Spain) "Applications of photovoltaic fields of iron doped LiNbO3 in nanotechnology"
44444444
Fabiano Corsetti (Asociacion CIC nanoGUNE, Spain) "New implementations of the orbital minimization method in the SIESTA code"
49494949
Carmen Del Hoyo Martínez (University of Salamanca, Spain) "Nanoclays as adsorbents of organic contaminants for a sustainable application"
54545454
Francisco Del Pozo (CTB-UPM, Spain)
----
Alexandr Dobrovolsky (Linkoping University, Sweden) "Optical studies and defect properties of GaP/GaNP core/shell nanowires"
56565656
Katerina Foteinopoulou (Institute of Optoelectronics and Microsystems (ISOM) and ETSII, UPM, Spain) "Entropy-driven phase transition in dense packings of athermal chain molecules"
68686868
Sandra García-Gil (CEMES-CNRS, France) "Progress towards a single swap molecule with Ruthenium complexes: DFT study on a gold surface"
75757575
David Garoz (Institute of Nuclear Fusion, Spain) "Crack mechanical failure in ceramic materials under ion irradiation: case of lithium niobate crystal"
79797979
María José Gómez-Escalonilla (U. Castilla-La Mancha, Spain) "Photochemical Evidence of Electronic Interwall Communication in Double-Wall Carbon Nanotubes"
81818181
Raquel Gómez-Medina (Universidad Autónoma de Madrid, Spain) "Negative scattering asymmetry parameter for dipolar particles: Unusual reduction of the transport mean free
path and radiation pressure"
83838383
Kikuo Harigaya (Nanosystem Research Institute, AIST, Japan) "Theoretical Study of Edge States in BC2N Nanoribbons with Zigzag Edges"
91919191
José Ignacio Izpura (GMME-CEMDATIC. UPM, Spain) "On the origin of RTS noise in nanoFETs "
101101101101
Gerald Kada (Agilent Technologies, Austria) "Calibrated Nanoscale Capacitance and Dopant Profile Measurements using a novel Nearfield Scanning
Microwave Microscope"
104104104104
W. Joshua Kennedy (NASA Johnson Space Center, United States) "Optical limiting by absorption bleaching in carbon nanotube devices: comparison of field-induced and
electrochemically-induced charge injection “
106106106106
Vladimir Labunov (Belarusian State University of Informatics and Radioelectronics, Belarus) "Novel “Carbon Nanotube/Graphene Layer” Nanostructures Obtained by Injection CVD Method for Electronic
Applications "
107107107107
Maria Jesús López Bosque (Parc Cientific de Barcelona/Plataforma de Nanotecnologia, Spain) "Hierarchical micro-nano-structures for cell adhesion studies"
115115115115
Fernando López-Tejeira (Instituto de Estructura de la Materia (IEM-CSIC), Spain) "Refractive Index Sensing based on Plasmonic Fano-like Interference"
117117117117
Maria Ada Malvindi (Italian Institute of Technology, Center for Bio-Molecular Nanotechnologies@Unile, Italy) "Silica nanostructures toxicity assessment and their potential for biomedical applications"
122122122122
Orals - senior
(parallel session)
24 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
TNT2012
S
pe
ak
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Gema Martínez-Criado (European Synchrotron Radiation Facility, France) "Imaging the carrier confinement within a single nanowire"
125125125125
Remo Masut (École Polytechnique de Montréal, Canada) "Reciprocal space and transmission electron microscopy study of heterogeneous GaP:MnP magnetic epilayers
containing MnP nanoclusters"
126126126126
Sébastien Maussang (Renishaw Ibérica, Spain) "Recent advances in fast imaging Raman technology for nano materials characterisation"
130130130130
Juan Ramon Morante (IREC, Spain) "Three dimensional electrodes base on core/shell nanowires for photoelectrochemical cells"
134134134134
Edgar Muñoz (Instituto de Carboquímica (ICB-CSIC), Spain) "Metal-Carbon Nanohybrid Foams: from Laser Chemistry to Nanochemistry"
135135135135
Cornelia G. Palivan (University of Basel, Switzerland) "Protein-polymer nanoreactors and processors act as artificial organelles"
139139139139
Daniel Pérez-Estévez (University of Vigo, Spain) "Functionalizated magnetic nanoparticles for biodetection, imaging and separation of Mytilus galloprovincialis
larvae using NIT-zipper® technology”
142142142142
Marcos Pita (Inst. of Catalysis and Petroleumquemistry-CSIC,Spain) "Improving the Direct Electron Transfer Efficiency in Laccase Electrodes for Biofuel Cell Cathodic Reactions"
145145145145
Dieter Pohlenz (Omicron NanoTechnology GmbH, Germany) "High Precision local electrical Probing: A New Low Temperature 4-Tip STM with Gemini UHV-SEM Navigation"
148148148148
Akhilesh Rai (University of Coimbra, Portugal) "One pot synthesis of potent antimicrobial gold nanoparticles"
----
Miguel Romera (Universidad Politécnica de Madrid, Spain) "Substantial increase of the critical current on a Spin Transfer Nanopillar by adding
an Fe/Gd/Fe trilayer"
157157157157
Rafael Sánchez (ICMM-CSIC, Spain) "Maximal entanglement out of transport through double quantum dots"
172172172172
Paz Sevilla (Universidad Complutense de Madrid, Spain) "Fluorescence and Raman characterization of a transport system formed by the anti tumoral drug emodin,
silver nanoparticles and porous silicon”
176176176176
Concha Tojo (University of Vigo, Spain) "Microemulsions as reaction media for the synthesis of bimetallic nanoparticles"
184184184184
Jessica Topple (McGill University, Canada) "Small Molecule Organic Photovoltaics at the Nanoscale"
186186186186
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 25
TNT2012 Speakers
pagepagepagepage
Joël Azevedo (CEA Saclay / SPEC, France) "Graphene and carbon nanotubes film organization with a new solution-based method: a substrate
independent transfer for transparent electrode applications”
33335555
Myriam Barrejón (Universidad de Castilla-La Mancha, Spain) "Synthesis of a new GO-C60 hybrid by “click” chemistry"
37373737
Maysoun Douas (Inst. Ciencia Materiales de Madrid (ICMM),Spain) "Identification of nanocavities water content"
57575757
Alberto Eljarrat Ascunce (Universitat de Barcelona, Spain) "EELS-HAADF spectrum imaging for characterization of (AlGa)N multilayer heterostructures."
59595959
Alberto Fraile García (Institute of Nuclear Fusion, Spain) "Molecular Dynamics simulation of liquid metals for nuclear fusion technology"
70707070
Kelli Hanschmidt (Institute of Physics, University of Tartu, Estonia) "Properties optimisation of titania microfibers by direct drawing"
89898989
Kevin Inderbitzin (U. Zurich - Physics-Institute, Switzerland) "Ultrafast X-Ray Nanowire Single-Photon Detectors and Their Energy-Dependent Response"
97979797
Yael Liebes (Ben Gurion University of the Negev, Israel) "Fabrication and characterization of nanopores in Si based materials"
110110110110
Raquel Lucena García (I. de Catálisis y Petroleoquímica-CSIC,Spain) "New Intermediate band sulphide nanoparticles acting in the full visible light range spectra as an active
photocatalyst"
118118118118
Diogo Mata (University of Aveiro, Portugal) "Spatial and temporal control of osteoblastic cells proliferation on electroconductive carbon nanotube-based
bone grafts"
128128128128
Bernat Olivera (University of Alicante, Spain) "Measurement of the capacitance across a tunnel barrier"
138138138138
Rebeca Ribeiro (Laboratoire National des ChamO Magnetiques Inteses, France) "Unveiling the Landau Levels Structure of Graphene Nanoribbons"
152152152152
Amalia Ruíz (ICMM-CSIC, Spain) "An Efficient MRI Contrast Agent Based on PEGylated Iron Oxide Nanoparticles"
161161161161
Carlos Sabater (Universidad de Alicante, Spain) "Creating nanowires with atomic precision"
163163163163
Beatriz Salinas (Centro Nacional de Investigaciones Cardiovasculares, Spain) "Biorthogonal chemistry for the functionalization of superparamagnetic nanoparticles: cross olefin metathesis"
167167167167
Cristina Sánchez (CTB-UPM, Spain) "Thermal and mechanical effects of different excitation modes based on low frequency laser modulation in
optical hyperthermia"
170170170170
Orals - PhD
(parallel session)
TNT2012 Abstracts
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 29
Optical nano-imaging of
gate-tuneable graphene plasmons 1 CICnanoGUNE, 20018, Donostia–SanSebastián, Spain
2 ICFO-Institut de Ciéncies Fotoniques, Mediterranean Technology Park,
08860 Castelldefels (Barcelona), Spain 3 IQFR-CSIC, Serrano119, 28006, Madrid, Spain
4 IKERBASQUE, BasqueFoundationforScience, 48011, Bilbao, Spain
5 Centro de Fisica de Materiales (CSIC-UPV/EHU) and Donostia International
Physics Center (DIPC), 20018, Donostia-San Sebastián, Spain 6 NeaspecGmbH, 82152, Martinsried, Munich, Germany
7 Graphenea S.A., 20018, Donostia-SanSebastián, Spain
8 CNM-IMB-CSIC–Campus UAB, 08193, Bellaterra, Barcelona, Spain
9 GREMAN, UMR7347, UniversitédeTours/CNRS, France
Graphene holds great promise for ultra-compact
and electronically controlled plasmonics [1,2].
Recently, resonant coupling of propagating THz
waves to plasmons in micro-ribbons has been
demonstrated [3], while IR near-field microscopy
has been applied to observe the coupling of
graphene plasmons to phonons [4]. In our work [5]
we use (similar to ref. [6]) scattering-type scanning
near-field optical microscopy (s-SNOM) to visualize
propagating and localized infrared plasmon modes
in graphene nanostructures in real space (Fig. 1). By
spectroscopic imaging we measure the graphene
plasmon wavelength λp as a function of excitation
wavelength, which confirms the theoretically
predicted plasmon dispersion. We observe that the
plasmon wavelength λp=λ0/40 is remarkably
reduced compared to the illumination wavelength
λ0, which can directly be attributed to the two-
dimensionality and unique conductance properties
of graphene. Furthermore, we demonstrate
tunability of the plasmon wavelength by gating
graphene nanoribbons on a SiO2 substrate. The
possibility to tune plasmons of extreme
subwavelength electronically opens up a new
paradigm in optical and opto-electronic
telecommunications and information processing.
References
[1] A. Vakil, N. Engheta, Science 332, 1291–1294
(2011)
[2] F.H.L. Koppens, D.E. Chang, J. Garcia de Abajo,
Nano lett. 11, 3370 (2011)
[3] L. JU, et al., Nat. Nanotech. 6, 630 (2011)
[4] Z. Fei, et al., Nano Lett. 11, 4701 (2011)
[5] J. Chen, et al., arXiv:1202.4996
[6] Z. Fei, et al., arXiv:1202.4993
Figure 1. Imaging propagating and localized
graphene plasmons by s-SNOM. a) Schematic
of the experimental configuration used to
launch and detect propagating surface waves
in graphene. The near fields generated at the
apex of an illuminated metal tip launch
plasmons on graphene. Back reflection of the
plasmons at the graphene edge yields plasmon
interference. b) Near-field amplitude image
acquired for a tapered graphene ribbon on top
of 6H-SiC, revealing interference of graphene
plasmons. The imaging wavelength is λ0=9.7
μm. The tapered ribbon is 12 μm long and up
to 1 μm wide.
P. Alonso-González1,
J. Chen5,1
, M. Badioli2,
S. Thongrattanasiri3,
F. Huth1,6
, J. Osmond2,
M. Spasenović2,
A. Centeno7, A. Pesquera
7,
P. Godignon8, A. Zurutuza
7,
N. Camara9, J. Garcia de
Abajo3, R. Hillenbrand
1,4 and
F. Koppens2
30 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Synaptic characteristics of
the atomic switch 1 WPI Center for Materials Nanoarchitectonics (MANA),
National Institute for Materials Science (NIMS), Tsukuba, Japan 2 Low-power Electronics Association and Project (LEAP), Tsukuba, Japan
More than ten years ago, some of the present
authors (Aono, Hasegawa and Terabe) and co-
workers developed the atomic switch [1, 2]. The
atomic switch is generally known as such nanoscale
switching devices that make ON/OFF switching by
the growth and shrinkage of a conduction path
composed of metal atoms (in contrast with other
nanoscale switching devices collectively called the
resistive switch in which a conduction path is
formed by anion [e.g. oxygen ion] vacancies, etc.).
Actually, the atomic switch has more interesting
functionalities depending on its structure and
constituent materials (see Fig. 1). In this paper,
after reviewing the general characteristics of the
atomic switch briefly, we would like to concentrate
on the discussion of the synaptic characteristics of
the atomic switch.
Figure 1. Various types of the atomic switch, which have
different structures and constituent materials.
The atomic switch was first developed as a
nanoscale, two-terminal, nonvolatile switch with a
nanoscale vacuum gap between a solid-electrolyte
(Ag2S) electrode and a simple-metal counter
electrode, i.e. a gap-type atomic switch [1, 2]; if
necessary, a volatile atomic switch can be made [3].
It has been found later that the vacuum gap can be
filled with soft organic molecules [4] and if the
molecules are photoconductive, a photosensitive
atomic switch can be made, where ON/OFF
switching is controlled by photons [4]. The
switching mechanism of the gap-type atomic switch
has been studied in detail [5-7].
Soon after the development of the gap-type atomic
switch, we developed a gapless- type atomic switch
without a gap between a solid-electrolyte electrode
(Cu2S was used) and a simple-metal counter
electrode [8-11]; this gapless-type atomic switch is
advantageous for practical application. We have
also found that the solid electrolyte in the gapless-
type atomic switch can be a polymer-based
electrolyte (e.g. poly-ethylene + AgClO4) [12],
suggesting that a flexible two-dimensional atomic
switch array can be fabricated. Moreover, it has
been found that the electrolyte in the gapless-type
atomic switch can be replaced by a metal oxide
(e.g. Ta2O5) [13-17]; the metal oxide is not a solid
electrolyte but works as an ion transport layer. The
switching mechanism of this ion-transport-layer
atomic switch has been studied in detail [18-21].
We have succeeded to develop three-terminal
atomic switches (transistors) using a solid
electrolyte (Cu2S) [22, 23] or an ion-transport layer
(Ta2O5) [24, 25]. Interest-ingly, an atomic transistor
using Ta2O5 can be operated in either volatile or
non-volatile modes by simply controlling applied
voltage [24].
Interestingly, we have revealed that the two-
terminal gap-type atomic switch exhibits learning
ability [26, 27]; namely, the conductivity of the
Masakazu Aono1,
Tsuyoshi Hasegawa1,
Kazuya Terabe1,
Tohru Tsuruoka1,
Takeo Ohno1,
Alpana Nayak1 and
Toshitsugu Sakamoto2
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 31
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switch can have inter-mediate values between the
OFF and ON conductivities, depending on the
history of input signals. More interestingly, the
atomic switch show interesting characteristics
similar to a synapse in neural network [28-30]; such
characteristics are also observed in a certain
gapless-type atomic switch [31]. On the basis of
these results, we have been developing
neuromorphic circuits made of atomic switches [28,
31, 32]. These studies have been partially reviewed
in Refs. 33-37.
Remarkable results related to the neuromorhpic
circuits constructed by atomic switches are
discussed in detail in this paper.
References
[1] K. Terabe et al., Riken Review No. 37 (July,
2001) 7.
[2] K. Terabe et al., Nature 433 (2005) 47.
[3] T. Hasegawa et al., to be published.
[4] T. Hino et al., Small 6 (2010) 1745.
[5] A. Nayak et al., J. Phys. Chem. Lett. 1 (2010)
604.
[6] A. Nayak et al., Appl. Phys. Lett. 98 (2011)
233501.
[7] I. Valov et al., Nature Mater., in press.
[8] T. Sakamoto et al., Appl. Phys. Lett. 82 (2003)
3032.
[9] S. Kaeriyama et al., IEEE J. Solid-State Circuits
40 (2005) 168.
[10] N. Banno et al., IEICE Trans. Electron. E89-C
(2006) 1492.
[11] N. Banno et al., IEEE Trans. Electron Devices
55 (2008) 3283.
[12] S. Wu et al., Adv. Funct. Mater. 21 (2011) 93.
[13] T. Sakamoto et al., Appl. Phys. Lett. 91 (2007)
092110.
[14] N. Banno et al., Appl. Phys. Lett. 97 (2010)
113507.
[15] M. Tada et al., IEEE Trans. Electron Devices
57 (2010) 1987.
[16] Y. Tsuji et al., Appl. Phys. Lett. 96 (2010)
023504.
[17] N. Banno et al., Jpn. J. Appl. Phys. 50 (2011)
074201.
[18] T. Tsuruoka et al., Nanotechnology 21 (2010)
425205.
[19] T. Tsuruoka et al., Nanotechnology 22 (2011)
379502.
[20] T. Tsuruoka et al., Adv. Funct. Mater. 22
(2012) 70.
[21] A. Nayak et al., Nanotechnology 22 (2011)
235201.
[22] T. Sakamoto et al., IEDM Technical Digest
(2005) 475.
[23] T. Sakamoto et al., Appl. Phys. Lett. 96 (2010)
252104.
[24] T. Hasegawa et al., Appl. Phys. Express 4
(2011) 015204.
[25] H. Kawaura et al., Electronics and
Communications in Japan 94 (2011) 55.
[26] T. Hasegawa et al., Adv. Mater. 22 (2010)
1831.
[27] T. Hasegawa et al., Appl. Phys. A 102 (2011)
811.
[28] T. Ohno et al., Nature Mater. 10 (2011) 591.
[29] T. Ohno et al., Appl. Phys. Lett. 99 (2011)
203108.
[30] A. Nayak et al., submitted.
[31] R. Yang et al., submitted.
[32] A. Stieg et al., Adv. Mater. 24 (2012) 286.
[33] R. Waser, M. Aono, Nature Mater. 6 (2007)
833.
[34] T. Hasegawa et al., MRS Bulletin 34 (2009)
929.
[35] M. Aono, T. Hasegawa, Proc. IEEE 12 (2010)
2228.
[36] T. Hino et al., Sci. Technol. Adv. Mater. 12
(2011) 013003.
[37] T. Hasegawa et al., Adv. Mater. 24 (2012)
252.
32 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Molecular design of smart
biomaterials for nano life
International Center for Materials Nanoarchitectonics (WPI-MANA),
National Institute for Materials Science, 1-1, Namiki, Tsukuba, Ibaraki, 305-0044, Japan
Recent progress in biological field enables development
of new biological drugs for human health.
Nanostructured materials also contribute to fabricate
new diagnosis or medical devices and so on. That is,
interdisciplinary research including biology, materials
science and nanotechnology give us new system or
materials to open new area more and more. We are
interested in developing ‘smart’ biotechnologies using
nanostructured stimuli-responsive polymers that
respond to small changes in external stimuli with large
discontinuous changes in their physical properties. These
‘smart’ biomaterials are designed to act as an “on-off”
switch for drug delivery technologies, gene therapy,
affinity separations, chromatography, diagnostics etc.
Design of nanostructure of smart polymers and
application for smart nanofiber
Poly(N-isopropylacrylamide) (abbreviated as PIPAAm) is
one of the typical thermo-responsive materials and
much attention is attracting in nanobio-field. So far, we
newly designed series of functional IPAAm-based
functional monomers as shown in Figure 1. Such
monomers have the same polymerizable group
(acrylamide) and corresponding copolymer shows
completely random sequences and as a result, can show
very sensitive responses. For example, the copolymers
with carboxyl group are useful stimuli-responsive thin
hydrogel coating with nano-level thickness (Figure 2).
The modified magnetite nano particles were attracted to
magnet and speed was accelerated by heating over it
transition temperature. Moreover, the particles can
response to the external alternating magnetic field
based on inductive heating. Hydorphilicity and
hydrophobicity of nanoparticles surface can be
modulated by on–off of only current switch [1]. Such
materials would be applied to diagnosis after
conjugation with biomolecules such as antibody using
functional groups effectively.
Such functional group enables the design of highly
functional stimuli-responsive materials. Photo-, pH- and
temperature-responsive polymers were designed as
shown in Figure 3 [2]. Photo-reactive benzophenone is
very effective to C-C bond formation by radical reaction.
Namely, photo irradiation leads cross-linking reaction in
the materials. Then, we prepared here a new type of
“smart” nanofibers (NFs) with dynamically and reversibly
tunable properties using thermally crosslinkable IPAAm
copolymers via electrospinning. PIPAAm is soluble in
aqueous milieu below LCST. Cross-linking reaction
prevent the nanofibers from solubilization. Actually, the
cross-linked NFs web was used for cell capture and
release aiming at cell container [3]. First, temperature-
responsive dynamic behavior of the NF web was
investigated. When soaked in PBS and heated to 37C,
the web underwent drastic shrinking due to a
conformational change of the copolymer. As the cross-
linked NFs had an LCST of approximately 18C, the web
surface size decreased to almost one-third of the original
size after this first heating. The temperature was then
alternated below and above the LCST and,
correspondingly, the web first swelled, and then shrank.
Takao Aoyagi, Yong-Jin Kim,
Yohei Kotsuchibashi and
Mitsuhiro Ebara
Figure 1. Molecular structures of developed monomers.
Figure 2. Magnetite nanoparticle coated with stimuli-
responsive polymers.
Figure 3. Photo, pH and temperature-responsive polymer.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 33
TNT2012
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Figure 4. SEM image of cross-linked nanofiber composed
of PIPAAm.
Interestingly, the web did not return to the original size
when the temperature was lowered below the LCST. It is
plausible that the porosity of the NF web gradually
decreased during heating and cooling cycles, thereby
reducing the ability of water to hydrate the entire
surface area of the web.
Next, the cell wrapping, encapsulation, and releasing
capability of NF webs were evaluated by incubating cells
on the webs. Normal human dermal fibroblasts (NHDFs)
were dropped on cross-linked NF webs at 37C. We found
that the web immediately started to fold upperward and
wrapped the droplet. The releasing capability of cells
from the NF webs was evaluated by collecting released
medium from the web during the heating process from 4
to 37C. Approximately 70%, 19%, and 6% of cells were
released from the web at 1st, 2nd, and 3rd cycle of
temperature alternation, respectively. In other words,
almost all cells seeded on the web were released after 3
temperature cycles, whereas only negligible amounts of
cells were released during the swelling process from 37
to 4C.
Block copolymer design for nano-assembly
We designed the double thermo-responsive block
copolymer aiming at effective targeting drug delivery. To
achieve this purpose, we synthesized the block
copolymers applying an atom transfer radical
polymerization (abbreviated as ATRP). The block
copolymer, Poly(PIAAm-b-poly(IPAAm-co-BMAAm),
comprises two segments (blocks), which have two
different lower critical solution temperatures
(abbreviated as LCST) as shown in Figure 5 [4].
As seen in Figure 6, in cold condition that is below first
LCST, the block copolymer is completely soluble in
aqueous milieu. Increasing the solution temperature,
between first and second LCST, they form the micelle-
like associates and are very useful to reserve drug
molecules in the core phase. In hot condition that is
above second LCST, the outer polymer chains that form
shell structure also shrink and eventually they form the
aggregates. The unstable structure would improve the
drug release form the core phase.
Recently, we developed highly functional nano-assembly
as shown in Figure 7 [5]. This system comprises the
mixing of three kinds of well-designed block copolymer.
These copolymers contain common segment structure
with lower specific LCST. Heating above the specific
LCST, all copolymer participate and form micelle-like
structure. Sugar moieties are pilot to interact to
hepatocyte. Actually, we confirmed the affinity in vitro.
Figure 5. Synthesis of double thermo-responsive block
copolymer by ATRP.
Figure 6. Nano-assembly by double thermo-responsive
block copolymer.
Figure 7. Highly functional nano-assembly for target drug
delivery.
References
[1] H. Wakamatsu, K. Yamamoto, A. Nakao, T.
Aoyagi, J. Mag. Mag. Mater., 302, (2006) 327.
[2] D. Matsukuma, K. Yamamoto, T. Aoyagi ,
Langmuir, 22, (2006) 5911.
[3] Y-J Kim, M. Ebara, T. Aoyagi, Angew. Chem.,
submitted.
[4] Y. Kotsuchibashi, M. Ebara, K. Yamamoto, T.
Aoyagi, J. Polym. Sci.: Polym. Chem., 48,(2010)
4393.
[5] Y. Kotsuchibashi, M Ebara, N. Idota, R. Narain,
Takao Aoyagi, Polym. Chem., in press.
O
OO
O
OHO
nOHN OHN
O
b
OHN OHN OHN OHN
O
b
O
NH
OOO
OH
OH
OH
OH
HO
34 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Quantum interference effects on
charge transport through a single
benzene ring 1 Kavli Institute of Nanoscience, Delft University of Technology, Lorentzweg 1,
2628 CJ Delft, The Netherlands 2 Department of Chemical Engineering, Delft University of Technology,
Julianalaan 136, 2628 BL Delft, The Netherlands
We explore charge transport through a single benzene ring, which is a prototypical molecular system where
quantum interference effects are expected. Using the mechanically controllable break junction technique,
we measured the low-bias conductance of molecular junctions where the benzene ring is wired between
gold electrodes through thienyl anchoring groups and ethynyl spacers. We show that the conductance for a
meta-coupled benzene ring is more than an order of magnitude smaller than that of a para-coupled
benzene. The dramatic reduction of the conductance is consistent with destructive quantum interference
effects in the meta-coupled benzene. This is supported by non-equilibrium Green’s function calculations that
confirm the occurrence of quantum interference in these systems.
Figure 1. (a) Layout of a mechanically controlled break-junction (MCBJ) setup. Two-dimensional trace
histograms constructed from 500 consecutive breaking traces taken at ambient conditions and 0.1 V
bias for junctions exposed to molecules coupled in (b) para and (c) meta configuration. Calculated
transmission of para (blue line) and meta (red line) in the gas phase.
Carlos R. Arroyo1, Simge
Tarkuc2, Riccardo Frisenda
1,
Johannes S. Seldenthuis1,
Charlotte H.M. Woerde2,
Rienk Eelkema2, Ferdinand
C. Grozema2 and Herre S. J.
van der Zant1
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 35
Graphene and carbon nanotubes film
organization with a new solution-
based method: a substrate
independent transfer for transparent
electrode applications 1 CEA Saclay, IRAMIS, SPEC (URA CNRS 2464), LEM, 91191 Gif sur Yvette, France
2 CEA Saclay, IRAMIS, SPEC (URA CNRS 2464), MOB, 91191 Gif sur Yvette, France
3 Université Paris-Sud 11, LCP, 91405 Orsay Cedex, France
Graphene and carbon nanotubes (CNT) have
exceptional properties that make them fascinating
objects for both academic and application-oriented
studies. In particular, with the combination of their
electronic, mechanical and optical properties, they
are considered as potential candidates for new
generations of transparent electrodes in o-PV cells,
touch screens and flexible displays. However, such
technologies rely on the capacity to form high-
quality thin-films with a controlled morphology.
In order to address the related issues a low-cost
and original method based on the transfer of
surfactant-stabilized water films has been
developed in our group. This bubble deposition
method (BDM) proved very efficient to organize
and transfer, under ambient conditions, dense and
homogeneous monolayers of nano-objects such as
nanowires and nanoparticles, over large areas. The
BDM does not require sophisticated transfer
processes and is compatible with a large panel of
substrates (silicon, glass, polymers…), both
hydrophilic or hydrophobic.
Recently we proved the usefulness of this approach
to self-assemble carbon materials such as single-
wall carbon nanotubes (SWNTs)[1] and graphene
oxide sheets (GO)[2] into close-packed monolayers.
Of particular interest is the compatibility of this
technique with: (i) a pre-structuration of the
substrate in micro-channels, such structuration
leading to the specific increase of the deposition
density within the channels (see figure 1)[3]; (ii)
homogeneous transfers at the wafer scale using
vertical water films in place of bubbles; (iii) a simple
layer-by-layer approach, enabling the formation of
thickness-adjusted films through multiple
depositions. This layer-by-layer approach was
extended notably to realize hybrid materials and, as
a proof of concept, a stacked structure was formed
by alternating SWNTs and GO layers[2].
Figure 1. SEM images of a carbon nanotube film
transferred on a lithographically patterned glass
substrate.
Our results provide insight into important problems
that impeded the development of SWNT and
Graphene based devices. Indeed, in contrast with
most methods (such a spin coating), BDM leads to
the transfer of the full amount of engaged material.
It is thus compatible with high added-value
materials, such as SWNTs selected by chirality. We
also present how this method can be used to
aligned carbon nanotubes at various scales using
the drainage of the water confined in the double
surfactant wall of the bubble[1].
Joël Azévédo1, S.
Campidelli1, Claire Costa-
Coquelard2, Jean-Jacques
Benattar2, Sébastien
Sorgues3, Christophe
Colbeau-Justin3 and V.
Derycke1
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Despite the variety of existing methods there is still
a lack of a simple, efficient and substrate-
independent technique enabling the deposition of
graphene sheets free of wrinkles. The Langmuir
Blodgett approach is highly efficient to self-
assemble a monolayer but the roughness of the
films deteriorates rapidly when several layers are
tentatively stacked. In contrast, we show that this
drawback can be almost completely suppressed
using our approach with both small (1-10 µm2) and
large (10-500 µm2) GO sheets (see figure 2). As well
as the precise control of the nano-objects
assembly, the efficient chemical reduction of GO
into graphene is still a pressing issue that limits the
development of GO-based electrodes. We are
currently investigating this point and will report our
last results combining the BDM with a post-
deposition reduction step.
Figure 2. AFM images of a close-packed arrangement of
small (left) and large (right) graphene oxide sheets in a
dense and homogeneous monolayer film.
Figure 3. Amplitude of the TRMC signal of Si, {SDBS-
CNT}-Si and CNT-Si surfaces.
The BDM is both versatile and scalable, and is
adapted to a wide variety of applications. Of
particular interest are conductive films that are
optically transparent and yield adequate and
uniform electronic properties. They could be used
as replacement for ITO in both light emitting
devices and photovoltaic ones. Concerning PV, one
particularly interesting system is the carbon/silicon
heterostructure that was shown to display very
high efficiency of light-to-current conversion
despite its simplicity. Using the BDM, ultra-thin and
uniform films of both SWNTs and GO were
deposited on silicon substrates and the mechanism
of charge separation at the carbon/silicon
interfaces is studied by the non-invasive Time
Resolved Microwave Conductivity (TRMC)
method.[3] This technique is based on the analysis
of the evolution of the microwave absorption of the
studied samples containing mobile charges
generated by a nanosecond laser excitation. The
measured signal is proportional to the conductance
change and consequently to the number of charge
carrier and to their mobility. It allows studying the
evolution of the lifetime of the photo-generated
carriers as a function of the heterostructure
properties. As an example, the charge carrier
lifetime in the case of a modified silicon-nanotube
junction (see figure 3) is 100 times longer than for
the bare silicon. Such signature of an efficient
charge separation at the carbon/silicon interface
measured by TRMC is very helpful to understand
and optimize nanotube-silicon solar cells.
References
[1] Guolei Tang, Xinfeng Zhang, Shihe Yang,
Vincent Derycke, Jean-Jacques Benattar, Small,
6 (2010), 1488
[2] J. Azevedo, C. Costa-Coquelard, P. Jegou, T. Yu
and J.-J. Benattar, Journal of Physical
Chemistry C, 115 (2011), 14678
[3] Claire Costa-Coquelard, Joël Azevedo, Florence
Ardiaca and Jean-Jacques Benattar, submitted
to Applied Surface Science
[4] C. Swiatkowski, A. Sanders, K.-D. Buhre and M.
Kunst, Journal of Applied Physics, 78(3) (1995),
1763
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Synthesis of a new GO-C60 hybrid
by “click” chemistry 1 Instituto de Nanociencia, Nanotecnología y Materiales Moleculares (INAMOL),
Universidad de Castilla-La Mancha, 45071 Toledo, Spain 2 Instituto de Catálisis y Petroleoquímica, CSIC, Cantoblanco, 28049, Madrid, Spain
3 Université de Strasbourg,France
Graphene (GS) and graphene oxide (GO) have
attracted great interest for its superior physical,
chemical, mechanical, and electrical properties that
enable a wide range of applications from
electronics to nanoelectromechanical systems [1].
Functionalization of these materials can allow to
modulate their electronic, optical and electrical
properties, and due to the insolubility and the
relatively inert surface of the GS and GO, new
methods for functionalization are being
explored [2].
As precedent, hybrid materials of Carbon
Nanotubes (CNTs) and fullerenes have generated
intense attention, driven by the possibility of
combining some of the outstanding properties of
the CNTs with those of fullerenes rising new
properties of the hybrid. The presence of fullerenes
in the SWCNTs environment could improve the
mechanical properties of the SWCNTs and tune the
electronic and optical properties of both, the CNT
and the fullerene cage, a subject of great interest
for optoelectronic applications [3].
"Click” chemistry is a well-known, versatile and
clean reaction and it is extremely efficient to
connect discrete molecules, polymers or
nanoparticles onto the nanotube sidewalls, through
the formation of a triazole ring linker.
In this sense, the preparation of hybrids involving
graphene and fullerenes will permit to explore the
potentials applications of these materials. Based on
this consideration, we present the synthesis and
the characterization of a soluble hybrid material,
GO-C60 that combines fullerene and graphene oxide
(GO) into a single structure. The GO was firstly
modified by the Tour procedure, affording the
alkyne group followed by click chemistry between
the modified GO and an azide fullerene derivative
yielding the fullerene-triazole-GO (GO-C60) hybrid.
This hybrid material has been fully characterized by
using a number of complementary techniques,
including Raman, X-ray photoelectron spectroscopy
(XPS), thermogravimetric analysis (TGA), high
resolution transmission electron microscopy (HR-
TEM); finally the photophysical properties of the
resulting multicomponent system have been
investigated in detail.
References
[1] M.J. Allen, V. C. Tung and R. B. Kaner, Chem.
Rev,110, (2010),132.
[2] L. Yan, Y. B. Zheng, F. Zhao, S. Li, X. Gao, B. Xu,
P. S. Weiss and Y. Zhao, Chem. Soc. Rev., 41,
(2012), 97.
[3] (a) M. Vizuete, M. J. Gómez-Escalonilla, J. L.
G. Fierro, M. Yudasaka, S. Iijima, M. Vartanian,
J. Iehl, J.-F Nierengarten and F. Langa, Chem.
Commun., 47, (2011), 12771 (b) M. Vizuete, M.
Barrejón, María J. Gómez-Escalonilla and F.
Langa, Nanoscale, (2012), DOI:
10.1039/c2nr30376.
Myriam Barrejón1,
María Vizuete1, María José
Gómez-Escalonilla1,
Jose Luis G. Fierro2,
Jean François Nierengarten3
and Fernando Langa1
38 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Electrodes based on mixture of
Graphene/Graphite/Carbon
nanotubes obtained by a new
dynamic spray-gun technique for
supercapacitor related applications
Thales Research and technology, 128 Rt Dpt, Palaiseau, France
The emergency of a new generation of
supercapacitors based on new kind of
nanomaterials has been pointed out by several
important papers recently issued [1-3]. In this
context the graphene/graphite and carbon
nanotubes present extremely interesting
properties. This contribution deals with the
fabrication of supercapacitors using an original
dynamic air-brush deposition technique [4]. The
advantages of this technique are the compatibility
with different kind of surfaces, the completely
automatic process (Figure 1a and 1b), the
uniformity of the material deposited and the
versatility. Using this technique we have fabricated
graphite/carbon nanotubes based electrodes (Fig.2
and 3) using different percentages of the two
materials sprayed on the surface in order to study
the influence of the different concentrations [5].
We are able to achieve flexible electrodes using
graphite as collectors with capacitances from 20 to
50F/g with energy density of around 5 Wh/kg and
power density around 10 kW/kg. Thickness can be
modulated from some nms to tenths of µms. Our
aim is to exploit the mixing of the two
nanomaterials in order to enhance the potential
electrode surface allowing to the ions to access all
the potential surface achieving a sort of hierarchical
assembly of the nanomaterials [3]. All the materials
are put into solution using a very simple process
(Figure 2). This technique can constitute a real
breakthrough for the fabrication of new kind of
electrodes using fine mixing of nanomaterials to
improve supercapacitor performances using an
industrially suitable process, moreover compatible
with flexible surfaces. Our process is able to impact
very quickly product for everyday life and can be
considered relatively low-cost considering that it
can be easily employed in a extremely reproducible
way.
a) b)
Figure 1. a) and b) Spray-gun deposition machine
Figure 2. Carbon
Nanotubes/Graphite
solution
Figure 3. Electrode achieved
using spray-gun deposition
method
Paolo Bondavalli and
Colin Delfaure
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References
[1] Simon, P. Gogotsi Y, Materials for electrochemical capacitors, Nature Materials, 7, 845-854, 2008.
[2] A. Izadi-Najafabadi, T.Yamada,D.N.Futaba, M. Yudasaka, H. Takagi, H. Hatori, Sumio Iijima, and K.
Hata, High-Power Supercapacitor Electrodes from Single-Walled Carbon Nanohorn/ Nanotube
Composite, , 5, 2, pp 811–819, ACNANO, 2011.
[3] Q.Cheng, J.Tang, J.Ma, H.Zhang, N. Shinyaa and L-C.Qin, Graphene and carbon nanotube composite
electrodes for supercapacitors with ultra-high energy density, Phys. Chem. Chem. Phys., 13, 17615–
17624, 2011.
[4] Nouvelle méthode pour la réalisation de dépôts modulables et reproductibles de nanomatériaux sur
des grandes surfaces et potentielles applications, P.Bondavalli, L. Gorintin, P. Legagneux, 2010 Patent
FR1004031.
[5] Procédée de fabrication d’ un assemblage collecteur-électrode pour cellule de stockage d 'énergie
électrique, assemblage collecteur-électrode cellule de stockage d'énergie, P.Bondavalli, P.Legagneux
2011 FR 11 01690.
40 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Multiscale simulations of
irradiated nanofoams
CONICET & Instituto de Ciencias Básicas, Universidad Nacional de Cuyo,
5500 Mendoza, Argentina
Materials with nanoscale porosity appear in several
different scenarios, from radiation damage in
nuclear reactors to evolution of astrophysical dust.
Nanoscale porosity can affect mechanical
properties and evolution of radiation damage,
leading to possible tailoring of desirable properties
like enhanced ductility and radiation endurance.
We use molecular dynamics (MD) and Monte Carlo
simulations to analyze the radiation damage and
surface modification of nanofoams, i.e. solids with
large porosity at the nanoscale. Atomistic
simulations can provide valuable insights when
experimental techniques can be difficult to use and
interpret. We consider two different irradiation
regimes: (a) irradiation with ions with keV energies,
where nuclear stopping dominates radiation
damage, of interest for fusion and fission energy
applications; (b) swift heavy ion irradiation, with
energies up to few GeV, relevant for track
formation and interstellar grain evolution.
We find that irradiation effects have larger spatial
extent than for full-density solids and include the
production of point-defects and twins which
change the mechanical properties of the samples.
For swift ions, porosity does not always decrease
surface ejection [J. Rodriguez-Nieva et al.,
Astrophys. J. Letters 743, L5 (2011)]. We use our
MD results as input for a Monte Carlo (MC) code to
calculate sputtering yields from nanofoams of
different geometries under different irradiation
conditions. For keV ions, we find that nanofoams
can act as efficient sinks for radiation-induced
defects and, therefore, that they can be radiation
resistant [E.M. Bringa et al., Nano Letters 12, 3351
(2012)]. We then use our MD results to build
models which predict possible radiation endurance
under intense irradiation.
This work was carried out in collaboration with J.
Rodriguez-Nieva, J. Monk, J.A. Caro, M.J. Loeffler, T.
Cassidy, R. E. Johnson, R. Baragiola, and D. Farkas.
E. M. Bringa
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I2–II–IV–VI4 Nanocrystals: synthesis
and thermoelectric properties
Departament Electronica, Universitat de Barcelona, Barcelona, 08028, Spain &
Catalonia Institute for Energy Research, IREC, Sant Adria del Besos, Barcelona,
08930, Spain
Today’s main strategy to produce materials with
high thermoelectric figures of merit is to trigger
phonon scattering at multiple length scales without
disturbing the charge carrier transport. The goal is
to minimize the lattice thermal conductivity in
highly electrically conductive materials; the so-
called electron-crystal phonon-glass paradigm. This
strategy is implemented by two main approaches: i)
the scattering of phonons at the atomic length
scale by the synthesis of complex crystal phases
that include 1D phonon scattering centers, such as
vacancies or rattling atoms, and/or 2D layered
crystallographic structures; ii) the scattering of
phonons at the 1-100 nm scale by reducing the
crystal domain dimensions to the nanoscale.
In this scenario, colloidal synthesis routes are
particularly well suited for the production of
thermoelectric materials. Solution-processing
methods have a high potential for the production
of low-cost, high-yield, large-scale, high-output and
shape-adaptable devices. Moreover, bottom-up
approaches allow to directly obtain
nanocomposites with reduced crystal domain size
and controlled geometry.
At the same time, some quaternary chalcogenides
have the required attributes to be potentially
excellent thermoelectric materials. Not only the
complex structures of these quaternary compounds
are associated with intrinsically low thermal
conductivities, but also their different cationic
valences provide a means of controlling their Fermi
level by adjusting their cation ratios. Besides, some
I2-II-IV-VI4 materials crystallizing in the stannite
phase are characterized by a convenient structure
layering, which allows decoupling the electrical
conductivity from both the thermal conductivity
and the Seebeck coefficient.
We will present a novel colloidal synthetic route to
prepare I2–II–IV–VI4 quaternary nanocrystals with
controlled size, shape and composition. We put
special effort in designing a cost-effective and
scalable process susceptible of being implemented
in real applications. The synthetic route is applied
to the preparation of grams of the quaternary
chalcogenide Cu2+xCd1-xSnSe4 (0 ≤ x ≤ 0.5) with
accurately controlled composition and narrow size
distributions. The electrical and thermoelectric
properties of these materials were characterized
over a wide temperature range. We will show how
these materials have high Seebeck coefficients
(150-300 μV/K), electrical conductivities up to
14000 S/m, and thermal conductivities down to
0.3 W/mK, leading to ZT values up to 0.4 at 700 K.
Besides, the advantages and disadvantages of this
bottom-up approach to produce thermoelectric
nanomaterials will be discussed.
Maria Ibáñez,
Doris Cadavid,
Joan Ramon Morante and
Andreu Cabot
42 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Nanotechnology for high
frequency communications:
nitrides and graphene 1 ISOM and Dept. Ingeniería Electrónica, ETSI Telecomunicación, UPM, Campus de
Excelencia Internacional Moncloa. Avda. Complutense 30, 28040 Madrid, Spain 2 Dept. Electrical Engineering and Computer Science, Massachusetts Institute of
Technology, 77 Massachusetts Ave., Bldg. 39-567B, Cambridge, MA 02139
The achievement of higher frequencies (HF) and
the reduction of energy consumption, to improve
sensing, communication and computation, involve
the continued scaling down to the nanometer level.
This scaling is enabled by of innovative device
designs, improved processing technologies and
assessment tools, and new material structures. In
this work, we have used all these factors to
demonstrate state-of-the-art HF devices in two
materials with quite different electronic properties:
wide semiconductor bandgap III-nitrides for
resonators and power amplifiers; and graphene, a
zero bandgap material expected to revolutionize
low noise and HF flexible electronics. Some issues
faced during their development will be discussed
during the talk.
Surface acoustic wave (SAW) devices are required
for radar systems and wireless communications, as
well as for high performance sensors. These SAW
devices consist of an interdigitated transducer (IDT)
on a piezoelectric substrate with a large sound
velocity. To enhance their frequency, we exploit the
combination of a compact IDT fabricated with e-
beam lithography, the highest sound velocity
provided by a diamond substrate, and the confined
Sezawa modes in a thin AlN piezoelectric layer
deposited on top. Both the IDT period and the film
thickness are key parameters in the design and
fabrication of the devices. The sputtering
deposition of the piezoelectric layer on micro and
nanocrystalline diamond and the lithography of the
transducers are optimized. HF SAW resonators
operating in the 10-20 GHz range (Fig. 1), showing
up to 40 dB out-of-band rejection and Q factors
larger than 10,000 are demonstrated [1]. Pressure
sensors have also been developed on free standing
AlN/diamond membranes.
Figure 1. Measured and simulated reflection coefficient
(S11) (top) and susceptance (bottom) for λ=800 nm one-
port SAW resonators on a 600 nm thick AlN film on
diamond. Several resonances corresponding to Sezawa
modes are observed.
The huge power density of AlGaN/GaN high
electron mobility transistors (HEMTs) has brought
during the last decade new possibilities and
advantages for the design of wide and multiband
amplifiers. High power-gain cutoff frequency (fmax)
has been achieved by combining low-damage gate-
recess technology, scaled device geometry, and
recessed source/drain ohmic contacts to enable
minimum short-channel effects (i.e., high output
resistance Rds) and very low parasitic resistances
[2]. SiC substrates are required to minimize self-
heating, as shown in Fig. 2(a). Some challenges for
long-term reliability and device scaling, due to the
strain induced by the large lattice mismatch
between the AlGaN barrier and the GaN buffer,
Fernando Calle1 and
Tomás A. Palacios2
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may be solved using the lattice-matched InAlN/GaN
heterostructure. LG=30 nm InAlN/GaN HEMTs on a
SiC substrate with a record fT in excess of 300 GHz
were obtained by applying an oxygen plasma
treatment [3]. The thin oxide layer on the InAlN
surface suppressed the gate leakage current,
passivated the surface, and significantly improved
the RF performance. Further efforts are dedicated
to identify the limiting factors and dominant failure
mechanisms to improve GaN-based HEMT
reliability, in particular heat spreading, by means of
diamond layers and other C-based materials such
as graphene and nanotubes.
Figure 2. Left: Tchannel vs output power for different Tamb
in devices grown on sapphire (a) and SiC (b). Right: RF
performance of the 30-nm-gate-length InAlN/GaN HEMT
with fT = 300 GHz. (From [3]).
Graphene is a carbon, one-atom-thick layer, the
thinnest but strongest material in the world. It is a
zero bandgap semiconductor with a room-
temperature electron and hole mobility above
100,000 cm2/V.s. A multidisciplinary effort among
physicists, chemists, material scientists and device
engineers has led to new electronic devices and
circuits taking advantage of its unique properties.
Some examples include RF multipliers, mixers,
modulators and demodulators [4] (see fig. 3).
Several technological issues during graphene
devices processing (including growth technique,
substrates, electrical isolation, contamination and
passivation, etc. [5]) will be discussed.
(a)
(b)
Figure 3. Top: First BN/Graphene/BN field effect
transistor with LG=400 nm. Bottom: Output power of a
HF doubler for an input signal of 8 GHz (a), and gain
frequency response (b).
The authors thank their students and colleagues at
ISOM-UPM and MIT for their contribution to this
work. That at ISOM-UPM has been funded by the
Spanish Government projects ReADi (TEC2010-19511),
AEGAN (TEC2009-14307) and RUE (CSD-2009-00046).
References
[1] J.G. Rodríguez, G.F. Iriarte, J. Pedrós, O.A. Williams,
F. Calle, IEEE Electron Dev. Lett. 33 (2012) 495.
[2] J. Chung, W. Hoke, E. Chumbes, T. Palacios, IEEE
Electron Dev. Lett. 31 (2010) 195.
[3] D.S. Lee, X. Gao, S. Guo, D. Kopp, P. Fay, T. Palacios,
IEEE Electron Dev. Lett. 32 (2011) 1525.
[4] T. Palacios, A. Hsu, H. Wang, IEEE Commun. Mag.
48 (2010) 122.
[5] F. Calle, A. Boscá, D. López-Romero, T. Palacios,
Graphene Sectorial Meeting, Castelldefels (2011).
0 50 100 150 200 2500
50
100
150
200
250
300
350
400
Gate Length Lg (nm)
Current Gain Cutoff Frequency f T (GHz)
0 100 2000
5
10
15
20
L (nm)
f T x Lg (GHz µµ µµm)
100 200
Lg (nm)
250 1 10 100 3000
10
20
30
40
50
60
Frequency (GHz)
Gain (dB)
lh21l2
fT = 300 GHz
U
Lg = 30-nm
Vds = 4 V
Vgs = -2.9 V
300
400
500
600
700
800
RTH=56 Kmm/W
RTH=45 Kmm/W
RTH=36 Kmm/W
Tchannel (K)
Sim:300 K
400 K
500 K
300 K
400 K
500 K
Sapphire substrate Exp:(a)
0 1 2 3 4 5 6 7300
400
500
600
700
800
RTH=21 Kmm/W
RTH=11 Kmm/W
Sim:
300 K
400 K
500 K
300 K
400 K
500 K
Tchannel (K)
P (W/mm)
SiC substrate Exp:
RTH=16 Kmm/W
(b)
44 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Applications of photovoltaic fields of
iron doped LiNbO3 in
nanotechnology 1 Dpto. de Física de Materiales, Universidad Autónoma de Madrid, 28049 Madrid, Spain
2 CMAM, Universidad Autónoma de Madrid, 28049 Madrid, Spain
3 Instituto de Ciencias Biomédicas, CSIC, C/ Arturo Duperier 4 28029 Madrid, Spain
4 Dpto. de Biología, Universidad Autónoma de Madrid, 28049 Madrid, Spain
As it is well known, the bulk photovoltaic effect
(PVE) [1] appears in certain crystalline materials
(usually ferroelectrics), that show an asymmetric
crystal cell unit arrangement. It produces a
directional electronic drift when electrons are
excited to the conduction band through visible light
illumination. The drift induces a charge separation
and generates an electric field between the
illuminated edges of crystal. Reported
measurements of this electric field reach values as
high as 105 V/cm in the material employed in our
experiments, i.e. iron doped LiNbO3 [2].
In this communication we will summarize our
results in two applications of the PV fields in
nanotechnology i) micro/nanoparticle trapping and
structuring on the surface of LiNbO3 crystals, and ii)
Effects of PV fields of LiNbO3 micro- and
nanoparticles in tumour cells.
As photovoltaic material we have used congruent
LiNbO3 with a 0.1% wt Fe doping
([Fe] = 4.25×1019
cm3). In these crystals,
photovoltaic fields in the range 50-70 kV/cm have
been measured using optical techniques.
Particle trapping and structuring
Recently, a method based on the evanescent fields
generated by the bulk photovoltaic effect in iron
doped LiNbO3 has been proposed and first
experiments reported [3-5]. The main advantage of
this procedure for particle trapping is that the
involved electrophoretic and/or dielectrophoretic
forces do not require any electrodes and massive
manipulation of nanoparticles can be achieved
using the patterning capabilities of light. Then, we
have developed a set of experiments with different
kind of particles, either dielectric (CO3Ca,
polystyrene) or conducting (graphite, aluminium
and silver). Holographic patterns as well as single
beam illumination have been used. The data are
analyzed within a theoretical scheme we have
recently proposed [6]. The results allow for a more
meaningful assessment of the possible applications
of the PV effect for trapping and patterning of
nanoparticles. As an illustration, Fig. 1 shows the
particle arrangements obtained using dielectric
(CO3Ca, diameter ~1 μm) particles (a), and metallic
(silver, diameter ~100 nm) particles, (b), under
periodic light pattern with spatial periodicity Λ = 20
and 10 μm respectively. In all cases the periodicity
of the obtained pattern was the same to that of the
exciting light.
Figure 1. Particle pattern obtained on the surface of
LiNbO3 plates after sinusoidal illumination with period Λ:
(a) CaCO3 particles (Λ=20 μm) (b) silver particles
(Λ=10 μm).
Biomedical applications
We have recently demonstrated the effect of PV
fields on biological media by culturing tumour cells
on Fe:LiNbO3 plates. A massive necrotic cell death
was induced in human tumour cell cultures after
H. Burgos1, M. Jubera,
A. García-Cabañes1,
Blázquez-Castro1,
J. Espada3, J. C. Stockert
4,
F. Agulló-López1,2
and
M. Carrascosa1
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irradiation with low intensity visible light [7]. In
order to explore the potential of PVE for future
biomedical applications we are now investigating
the effect of LiNbO3:Fe micro-nanoparticles on
tumour (HeLa) cell cultures. In a first experiment
cells were incubated with microparticles (1-3 μm
diameter). Cells did not show any morphology
change in dark whereas after 60 min irradiation
(546 nm, 133.2 J/cm2 light dose), about half of the
cells had a round and refringent aspect, i.e. they
show a certain damage. Two hours after ending
illumination most cells were necrotic as
represented in Figure 2. Control cultures (without
microparticles) exposed to 546 nm light for 60 min
showed no damage.
Figure 2. Time evolution of the number of viable (circles)
and necrotic (squares) cells evaluated through
morphological criteria for HeLa cell cultures with LNB
micro-particles. Representative viable and necrotic cells
are shown in the microphotographs at the top of both
figures. The gray bars indicate the period of green light
exposure.
The next step is to reduce particle size to a
diameter of tenths of nm to induce their
incorporation by cells. Experiments to evaluate the
effect of nanoparticles in cells for different light
doses are now in progress.
This work was supported by MICIN under grant
MAT2008-06794-C03 and MAT2011-28379-C03-01.
References
[1] B. Sturman and V. M. Fridkin, The Photovoltaic
and Photorefractive Effects in Non-
centrosymetric Materials, Gordon & Breach
Science Publishers, Amsterdam 1992.
[2] E. M. de Miguel.,J. Limeres, M. Carrascosa and
L.Arizmendi, J. Opt. Soc. Am. B 17, (2000)
1140.
[3] X. Zhang, J. Wang, B. Tang, X. Tan, R.A. Rupp, L.
Pan, Y. Kong, Q. Sun, J. Xu, Opt. Express 17,
(2009) 9981.
[4] H.A. Eggert, F.Y. Kuhnert, K. Buse, J.R.
Adleman, D. Psaltis, Appl. Phys. Lett. 90, (2007)
241909.
[5] M. Esseling, F. Holtmann, M. Woerdemann, C.
Denz, Opt. Express 18, (2010) 17404.
[6] J. Villarroel, H. Burgos, A. García-Cabañes, M.
Carrascosa, A. Blázquez-Castro, F. Agulló-
López; Opt. Express 19, (2011) 24320.
[7] A. Blázquez-Castro, J.C. Stockert, B. López-
Arias, A. Juarranz, F. Agulló-López, A. García-
Cabañes, M. Carrascosa, Photochem.
Photobiol. Sci. 10, (2011) 956.
46 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Electronic properties and
quantum transport in doped and
defective graphene 1 Université catholique de Louvain (UCL), Institute of Condensed Matter and Nanoscience
(IMCN), Nanoscopic Physics (NAPS), Chemin des étoiles 8, 1348 Louvain-la-Neuve, Belgium 2 CIN2 (ICN-CSIC) and Universitat Autonoma de Barcelona (UAB),
Catalan Institute of Nanotechnology, Campus UAB, 08193 Bellatera (Barcelona), Spain
Graphene, a one atom-thick membrane, has
sparked out intense research activities from both
experimental and theoretical sides since almost a
decade now. The striking properties of graphene in
various fields, such as mechanical, thermal, or
electronic transport properties, are intrinsically
related to its two-dimensional aspect and to its
honeycomb lattice structure yielding both to the
peculiar electronics of Dirac Fermions. From the
electronic transport point of view, clean graphene
samples exhibit particularly long coherence length
and high electronic mobility both interesting for
devices applications in nanoelecronics. Graphene
provide simultaneously is genuine playground for
fundamental researches such as exploration of
Anderson (anti-)localization phenomena in real
two-dimensional systems.
In this presentation, simulations of electronic
transport in defective graphene membranes are
exposed. Employing tight-binding models validated
by ab initio calculations, and using a real-space
order-N Kubo-Greenwood transport method [1-2],
the effect of structural defects disrupting the ideal
honeycomb lattice is investigated theoretically. The
effect of various concentrations of “point defects”
such as vacancies and Stone-Wales defects on both
the electronic and transport properties of graphene
is examined. Using molecular dynamics simulations,
highly defective graphene membranes presenting
domains of amorphous graphene structure [3] are
created, and their transport properties are carefully
inspected. Structural defects are found to induce
strong resonant scattering states at different
energies depending on the nature and the
concentration of defects. These induced resonant
scattering states can yield to extremely short mean
free paths and low mobilities. At low temperatures,
they also lead to an enhanced contribution of
quantum interferences driving to localization
phenomena in the quantum transport regime. In
case of highly defective graphene membrane, the
amorphization of the structure changes the system
into a strong two-dimensional Anderson insulator
material [3], which could be experimentally
confirmed by the observation of a variable range
hopping transport behavior at low temperatures.
The modification of the electronic properties of sp2
carbon nanostructures by the controlled addition of
foreign atoms into the carbon lattice has been
widely proposed and investigated, in close analogy
to the doping of silicon in the semiconductors
industry. However, in contrast with conventional
materials, the effect of foreign atoms in
nanostructures is expected to depend significantly
on the position and surrounding of each atom due
to the quantum confinement of the electrons. In
principle, the fact that nitrogen atoms contain one
additional electron than carbon, suggests that
nitrogen doped carbon nanostructures will exhibit
the characteristics of an n-type material [4].
Furthermore, recent experiments on graphene
reveal through scanning tunneling microscopy
(STM) images, that N doping can occur in different
kinds of geometries [4]. This presentation explores
different configurations for nitrogen atoms
incorporated onto graphene, and investigates their
effects and properties using ab initio electronic
structure calculations. The computed total and
local density of states reveal specific signatures for
each type of defect, which could be correlated with
experimental scanning tunneling spectroscopy (STS)
measurements. In addition, STM images are
Jean-Christophe Charlier1,
Aurelien Lherbier1,
Andrés R. Botello-Méndez1
and Stephan Roche2
jean-
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presented in order to aid the eventual large scale identification of these defects. Our calculations, and recent
experimental observations suggest that the classically assumed nitrogen incorporations into graphitic
structures (i.e., single substitution and pyridinic), are not necessarily the most common [4]. It is generally
true, however, that substitution defects (single, double substitution) dopes graphene with electrons, and
vacancy-nitrogen complexes (e.g. pyridinic, or single nitrogen + vacancy) add holes to the system.
References
[1] A. Lherbier, S.M.-M. Dubois, X. Declerck, S. Roche, Y.M. Niquet, and J.-C. Charlier, Phys. Rev. Lett. 106, 046803
(2011). [2] A. Lherbier, S.M.-M. Dubois, X. Declerck, Y.M. Niquet, S. Roche, and J.-C. Charlier, Phys. Rev. B 86, 075402 (2012).
[3] A. Lherbier, S. Roche, O.A. Restrepo, Y.M. Niquet, A. Delcorte, J.-C. Charlier, submitted for publication (2012).
[4] R. Lv, Q. Li, A.R. Botello-Méndez, et al., NATURE Scientific Reports, in press (2012).
48 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Electronic stucture of
topological insulators a Departamento de Física de Materiales, Facultad de Ciencias Químicas, UPV/EHU,
Apdo. 1072, 20080 San Sebastián, Basque Country, Spain b Donostia International Physics Center (DIPC), Paseo de Manuel Lardizabal, 4,
20018 San Sebastián/Donostia, Basque Country, Spain c Centro de Física de Materiales, CFM-MPC, Centro Mixto CSIC-UPV/EHU,
Apdo.1072, 20080 San Sebastián/Donostia, Basque Country, Spain d Tomsk State University, pr. Lenina 36, 634050, Tomsk, Russian Federation
e Institute of Strength Physics and Materials Science,
pr. Academicheskiy 2/4, 634021, Tomsk, Russian Federation f Max-Planck-Institut für Mikrostrukturphysik Weinberg 2, D-06120, Halle, Germany
g Graduate School of Science, Hiroshima University,
1-3-1 Kagamiyama, Higashi Hiroshima 739-8526, Japan h Physik-Institut, Universität Zürich,
Winterthurerstrasse 190, CH-8057 Zürich, Switzerland
The recently discovered three-dimensional
topological insulators (TIs) belong to a class of
insulators in which the bulk gap is inverted due to
the strong spin-orbit interaction [1]. A direct
consequence of such bulk band structure arises at
the surface: the spin-polarized topologically
protected massless metallic states, forming a Dirac
cone [2-5]. These surface states (SS) exhibit many
interesting properties resulting from the fact that
the spin of electron is locked perpendicular to its
momentum, thus forming a SS spin structure that
protects electrons from backscattering. This makes
topological insulators potentially promising
materials for creation of new quantum devices.
Here recent theoretical and experimental results on
electronic structure obtained for new families of TIs
are presented. Comparison of topological surface
states with classical and Rashba split surface states
as well as Dirac cone state in graphene is given. The
origin of buried topological surface states is
discussed. Materials science problems and
perspectives in the field of TIs are discussed.
References
[1] M. Z. Hasan and C. L. Kane, Rev. Mod. Phys. 82,
3045 (2010).
[2] K. Kuroda et al., Phys. Rev. Lett., 105, 076802
(2010).
[3] S. V. Eremeev, Yu. M. Koroteev, and E. V.
Chulkov, JETP Lett. 92, 161 (2010).
[4] K. Kuroda et al., Phys. Rev. Lett., 108, 206803
(2012).
[5] S.V. Eremeev et al., Nature Communications,
3, 635 (2012).
Evgueni V. Chulkova,b,c
,
Sergey V. Eremeevb,d,e
,
Tatiana V. Menshchikovad,
Maia Vergnioryb,
Yury M.Koroteevb,d,e
,
Arthur Ernstf,
Jürgen Henkf, A. Kimura
g
and J. Hugo Dilh
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 49
New implementations of the orbital
minimization method in the SIESTA
code
a CIC nanoGUNE Consolider, E-20018 Donostia-San Sebastián, Spain
b Department of Earth Sciences, University of Cambridge, Downing Street,
Cambridge CB2 3EQ, United Kingdom
The orbital minimization method (OMM) is the
general name given to a class of iterative
minimization algorithms devised for solving the
generalized eigenvalue problem in the context of
linear-scaling DFT [1]. The central idea of the
method is to find the Wannier functions of the
electronic system that describe the occupied
subspace by direct unconstrained minimization of
an appropriately constructed functional [2,3]. The
method is made to scale linearly with system size
by imposing a localization radius on the Wannier
functions, which in turn determines the truncation
range of the density matrix.
Unfortunately, the OMM suffers from a serious
problem of multiple local minima, requiring in
practice that the initial guess reflect the correct
bonding properties of the system. Alternatively,
Kim et al. [4] have proposed to work with more
orbitals than those needed to span the occupied
subspace, leading to a linearly dependent basis.
This eliminates the local minima problem, but
introduces the electronic chemical potential as an
unknown parameter.
We report on several new implementations of the
OMM in the SIESTA [5] DFT code, that aim to
exploit the efficiency and stability of the method
while circumventing the limitations described
above.
Firstly, we show the potential of the original OMM
method as a conventional DFT solver (without the
linearscaling approximation), as the local minima
are no longer present when the Wannier functions
are allowed to extend over the whole system. The
algorithm is therefore both accurate and efficient,
due to the fact that no explicit orthogonalization
operation is required between orbitals, and that
the solution from each minimization can be reused
iteratively for multiple self-consistent field steps
and ab initio MD steps. We also show that the
sparsity pattern of the Hamiltonian matrix in SIESTA
can be used in this context to significantly reduce
the computational cost; in conclusion, the method
has proven to be competitive with explicit
diagonalization even in small systems despite the
large ratio of occupied states to total basis size that
is used in SIESTA and other atomic orbital codes.
Secondly, we discuss a number of approaches for
imposing the correct electron number in the
augmented OMM of Kim et al. that can be used
with Wannier localization for linear-scaling DFT
calculations; we report on an automated
adjustment of the chemical potential to preserve
electron number, a projected gradient method and
a normalization transformation of the Wannier
function coefficients. We discuss the connection
between our approaches and those used in density
matrix methods; in particular, the OMM presents
further challenges in this respect due to the fact
that we do not have direct access to the density
matrix in the Wannier basis. Finally, we present
initial results for a modified OMM functional that
allows for smeared Fermi level calculations (pseudo
finite temperature), opening up the possibility of
performing linear-scaling DFT for metallic systems
in SIESTA.
Fabiano Corsettia and
Emilio Artachoa,b
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References
[1] D. R. Bowler and T. Miyazaki, Rep. Prog. Phys., 75 (2012) 036503.
[2] P. Ordejón, D. A. Drabold, R. M. Martin, and M. P. Grumbach, Phys. Rev. B, 51 (1995) 1456.
[3] F. Mauri, G. Galli, and R. Car, Phys. Rev. B, 47 (1993) 9973.
[4] J. Kim, F. Mauri, and G. Galli, Phys. Rev. B, 52 (1995) 1640.
[5] J. M. Soler et al., J. Phys.: Condens. Matter, 14 (2002) 2745.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 51
Enhanced performance of carbon
nanotube field-effect transistors due
to gate-modulated electrical contact
resistance
Sandia National Laboratories, MS9161, Livermore, CA, USA
Due to their unique electrical properties, carbon
nanotubes (CNTs) have attracted a great deal of
interest for their potential in next-generation
nanoelectronics [1,2]. While individual CNTs can
exhibit favorable electronic properties, it is often
the CNT/metal contacts that govern the behavior
and performance of CNT devices [3,4]. Thus, it is
important to develop a fundamental understanding
of contacts to CNTs in order to fully realize the
potential of CNT devices. Recent experimental work
[5,6] has provided new insight by demonstrating
that the nanotube/palladium (Pd) contact
resistance depends on the contact length, and that
appropriate control of the contacts allows for the
realization of high-performance short-channel CNT
field-effect transistors (FETs) with subthreshold
swings that surpass those expected from
conventional scaling theory. This last result is
particularly important not only for technology, but
also because it suggests that new paradigms govern
the properties of these nanoscale transistors. For
example, it has been suggested that modulation of
the contacts by the gate, a phenomenon not
usually observed in conventional transistors, could
lead to such behavior [6].
In this work [7], we use numerical simulations to
study these recent experimental measurements
and explicitly demonstrate that the superior scaling
behavior is due to a strong modulation of the
contacts by the gate. This results not only in
modulation of the band alignment at the contact,
but also leads to a novel phenomenon where the
subthreshold swing is dominated by gate control of
the near-contact region in the channel. This gives
rise to subthreshold swings for short-channel
devices that are below what is predicted by
standard theory, allowing for improved
performance.
The simulated CNT FET is shown in Figure 1. For
this work, we consider a (16,0) nanotube with a
diameter (dCNT) of 1.2 nm, which matches the
average size of the CNTs in Ref. 5. We also consider
two different contact geometries. In Figure 1a,
there is metal both above and below the nanotube,
as a model for a CNT completely embedded in
metal. In Figure 1b, we consider a contact where
the metal only sits on top of the CNT. To determine
the transport properties of the FET, we use a self-
consistent non-equilibrium Green’s function (NEGF)
approach [8] that allows us to calculate the low-
bias current through the device.
Figure 1. Schematic of a carbon nanotube field-effect
transistor. In part (a) the source and drain metals are
above and below the nanotube (embedded contact),
while in part (b) the metal only sits on top of the
nanotube (top contact).
Using the NEGF approach, we calculated the
transfer characteristics of the CNT FETs for channel
and contact lengths that match the experimental
devices. The results are shown in Figure 2, where
the experimental data is given by the symbols and
the theoretical data is given by the solid lines. The
top row of Figure 2 shows the results for Lch = 40
nm, the middle row is for Lch = 20 nm, and the
Aron W. Cummings and
François Léonard
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bottom row is for Lch = 15 nm. The left column
shows the simulation results for embedded
contacts (see Figure 1a), while the right column is
for top contacts (see Figure 1b). The experimental
data is the same for both columns. An important
feature of the experimental data is the extremely
good scaling of the transistor characteristics as the
channel length is reduced. Indeed, comparing the
experimental data for the channel lengths of 40, 20,
and 15 nm in Figure 2, one can see that the
subthreshold swing is essentially unchanged as the
channel length is scaled down. While the thin HfO2
dielectric provides good control over the FET
channel, our simulations indicate that this by itself
is not sufficient to explain the good subthreshold
behavior. This can be seen by comparing the left
and right columns of Figure 2. The left column
shows the simulation results for the embedded
contacts. In this case, the theoretical subthreshold
swing is much larger than the experimental value
for small channel lengths, and we see a poor fit to
the experimental results. However, when we
remove the metal below the CNT, the subthreshold
swing is significantly reduced for the short-channel
devices and we obtain excellent agreement with
the experimental data, as shown in the right
column of Figure 2. Thus, the geometry of the
contact plays a crucial role in determining device
performance and scaling, and the improved
behavior upon removing the bottom metal
indicates a strong influence of the gate on the
contact properties.
In summary, we presented simulations of short-
channel ballistic CNT FETs that explain recent
experimental results using Pd contacts. We have
reached the important conclusion that the contacts
are strongly modulated by the gate when no
bottom metal contact is present, allowing for lower
subthreshold swings for short channels and
improved scaling behavior. This result introduces
important design considerations for CNT electronic
devices, and should also apply to devices made of
other nanomaterials such as nanowires and
graphene.
Figure 2. Current vs. gate voltage for short-channel CNT
FETs. The top, middle, and bottom rows are for Lch = 40,
20, and 15 nm, respectively. The left (right) column is the
case for embedded (top) contacts. The symbols
represent experimental results from Ref. 5, and the solid
lines represent the results from numerical simulations.
References
[1] J.-C. Charlier, X. Blase, and S. Roche, Rev. Mod.
Phys. 79 (2007), 677-732.
[2] P. Avouris, Z. Chen, and V. Perebeinos, Nat.
Nanotechnol. 2 (2007), 605-615.
[3] Z. Chen, J. Appenzeller, J. Knoch, Y. Lin, and P.
Avouris, Nano. Lett. 5 (2005), 1497-1502.
[4] F. Léonard and A. A. Talin, Nat. Nanotechnol. 6
(2011), 773-783.
[5] A. D. Franklin and Z. Chen, Nat. Nanotechnol. 5
(2010), 858-862.
[6] A. D. Franklin, M. Luisier, S.-J Han, G. Tulevski,
C. M. Breslin, L. Gignac, M. S. Lundstrom, and
W. Haensch, Nano Lett. 12 (2012), 758-762.
[7] A. W. Cummings and F. Léonard, ACS Nano, in
press, DOI: 10.1021/nn301302n.
[8] S. Datta, Electronic Transport in Mesoscopic
Systems (Cambridge University Press,
Cambridge, 1995).
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 53
Silicon-based
quantum electronics
CEA, Grenoble, France
Low-dimensional silicon-based nanostructures
constitute a versatile and convenient platform for
novel electronic devices with quantum
functionalities. After a brief overview of the most
promising development routes, I shall report on a
recent experiment in which we have been able to
observe a gate-tunable tunneling current through a
series of two donor atoms embedded in the
channel of a multi-gate silicon transistor. The
lowest energy states, corresponding to a single
electron on either of the two donors, form a two-
level system well separated from all other
electronic levels. Gigahertz driving results in a
quantum interference pattern associated with the
absorption or the stimulated emission of up to ten
microwave photons, from which we estimate a
charge dephasing time of 0.3 nanoseconds. This
experimental achievement is an essential step
towards either charge- or spin- based quantum
computing devices in silicon.
Related publications:
[1] Katsaros et al., “Hybrid superconductor-
semiconductor devices made from self-
assembled SiGe nanocrystals on silicon”,
Nature Nanotechnology 5, 458 (2010).
[2] Katsaros et al., “Observation of spin-selective
tunneling in SiGe nanocrystals”, Phys. Rev.
Lett. 107, 246601 (2011).
[3] Dupont-Ferrier et al., “Coupling and coherent
electrical control of two dopants in a silicon
nanowire”, arXiv:1207.1884v1.
Silvano De Franceschi
54 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Nanoclays as adsorbents of organic
contaminants for a sustainable
application
Facultad de Ciencias Químicas
Plaza de la Merced s/n- 37008 Salamanca
University of Salamanca - Spain
Thanks to the development of the science and the
technology of the nourishment in the last 50 years,
there have revealed itself several new substances
that can fulfill beneficial functions in the food, and
these substances, named food additives, are today
within reach of all. The food additives recover a
very important role in the complex nourishing
supply. The additives fulfill several useful functions
in the food, which often we give for sat.
Nevertheless the widespread use of food additives
in the food production also influences the public
health. The food industries, which are very
important for the economy, spill residues proved
from its activity that they have to be controlled to
evaluate the environmental impact and to offer the
necessary information about the quantitative
evaluation of the chemical risk of the use of food
additives for the public health.
The clay materials have led to numerous
applications in the field of public health (del Hoyo,
2007; Volzone, 2007) having been demonstrated its
effectiveness as adsorbents of all contaminants.
Some biodegradable materials are used for for
adsorption of chemical contaminants: lignins
(Valderrabano et al., 2008) and also clays and clay
minerals, whose colloidal properties, ease of
generating structural changes, abundance in
nature, and low cost make them very suitable for
this kind of applications.
Among the strategies used at present to preserve
the quality of the water and this way to diminish
the environmental risk that supposes the chemical
pollution, stands out the use of adsorbents of
under cost, already they are natural or modified, to
immobilize these compounds and to avoid the
pollution of the water with the consequent
reduction of environmental and economic costs.
Regarding innocuous and low cost materials, it is
necessary to mention clays and clay minerals,
which colloidal properties, facility of generating
structural modifications, abundance in the nature
and low cost make them very adapted for the
adsorption of chemical pollutants. The clayey
materials have given place to numerous
applications to preserve the water contamination
and its efficiency having being demonstrated as
natural or modified adsorbents of all kinds of
pollutants (Yariv, 2002). We have studied the
adsorption of several food additives by natural or
thermally modified clays, searching their
interaction mechanisms and the possible recycling
of these materials for environmental purposes and
prevention of the public health.
There are different materials used in the adsorption
and immobilization of chemical contaminants, most
of whom remain under patent, so they do not know
the procedures and products used, but in all cases
the safety and / or biodegradability of materials
used is an important issue in their choice for
environmental applications. The most used are
based on the use of organo-montmorillonites and
hydrotalcite (del Hoyo et al., 2008; Undabeytia et
al. 2008).
Likewise, by means of mechanical and chemical
treatments clays can be transformed in materials
with a high surface (> 300m2) and high reactivity.
The acid treatment causes the partial dissolution of
the octahedric layer giving place to an increase of
Carmen del Hoyo Martínez,
Jorge Cuéllar Antequera,
Vicente Sánchez Escribano,
Marina Solange Lozano
García and Raul Cutillas Díez
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the acid sites type Brönsted (Torrers Sánchez et al., 1999). Other treatments of the clays that might
optimize the adsorption of organic compounds, are the utilization of the grinding by attrition and the
thermal treatment of clays (del Hoyo et al., 1999). The grinding by attrition provokes a modification in the
crystalline structure of the clays, which produces a change in the properties of superficial load, modification
of the coordination of the octahedric Al and irreversible collapse of the interlayer.
We have studied the adsorption of several contaminants by natural or modified clays, searching their
interaction mechanisms and the possible recycling of these materials for environmental purposes and
prevention of the health.
References
[1] del Hoyo, C., Rives, V., Vicente, M.A. (1999). PhD Thesis. Drug-clay systems. University of Salamanca.
[2] del Hoyo, C.; Dorado, C.; Rodríguez-Cruz, S.; Sánchez-Martín, M.J. (2008). Journal of Thermal Analysis
and Calorimetry. 1, 1-8. Physico-chemical study of selected surfactant-clay mineral systems.
[3] del Hoyo, C. (2007b). Applied Clay Science. 36, 103-121.Layered Double Hydroxides and human health:
An overview.
[4] Torres-Sánchez L, Lopez-Carrillo L, Ríos C. (1999). Salud Pública de México. 41, 106-108. Lead
elimination by traditional acidic curing.
[5] Undabeytia T., Nir S, Sanchez-Verdejo T, Morillo, E. Water Research. 42. 1211-1219. (2008). A
clayvesicle system for water purification from organic pollutants.
[6] Valderrábano, M., Rodríguez-Cruz, S., del Hoyo, C., Sánchez-Martín, M.J. (2006). 4th International
Workshop "Bioavalailability of pollutants and soil remediation". 1, 5-6. Physicochemical study of the
adsorption of pesticides by lignins.
[7] Volzone, C. (2007). Applied Clay Science. 36, 191-196. Retention of pollutant gases: Comparison
between clay minerals and their modified products.
[8] Yariv S., Cross H. (2002). Marcel Dekker, New York, U.S.A. 225 pp. Organo-clays complexes and
interactions
56 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Optical studies and defect properties
of GaP/GaNP core/shell nanowires 1 Department of Physics, Chemistry and Biology, Linköping Univ, 581 83 Linköping, Sweden
2 Department of Physics, University of California, San Diego, La Jolla, California 92093, USA
3 Graduate Program of Material Science and Engineering, University of California, San
Diego, La Jolla, California 92093, USA 4 Department of Electrical and Computer Engineering, University of California, San Diego,
La Jolla, California 92093, USA
III-V core/shell nanowires (NWs) have recently
attracted much attention due to their potential
applications in optoelectronic and photonic
devices, in particular solar cells and LEDs. Among all
III-V compounds, GaP-based materials have the
smallest lattice mismatch to Si and are, therefore,
the best candidate for epitaxial growth of III-V
materials on Si substrates. Adding a small amount
of N to GaP allows one to tune the band gap energy
and also to change the band gap character from an
indirect one in GaP to a direct-like one in the GaNP
alloys, leading to improvements in light emission
efficiency. Unfortunately, the above described
properties desired for optoelectronic applications
have not been fully utilized, largely due to
degradation of optical and electrical properties
caused by defects present in GaNP. The growth of
these materials in the form of NWs offers the
possibility to overcome the limitations. In this work,
we investigate optical properties and influence of
defects on optical quality of the GaP/GaNxP1-x
core/shell NWs grown on Si (111) substrates
employing temperature-dependent
photoluminescence (PL), time-resolved PL and
optically detected magnetic resonance (ODMR)
measurements.
The GaP/GaNxP1-x core/shell NW samples with
x = 0.9% studied in this work were grown by gas-
source molecular beam epitaxy (MBE). For a
comparison, a 250 nm-thick GaN0.009P0.991 epilayer
grown by gas-source MBE on a (001)-oriented GaP
substrate was also investigated. Scanning electron
microscopy (SEM) showed that the GaP/GaNP NWs
are uniform in sizes and have an axial length of
about 2.5 μm, a total diameter of about 220 nm,
and a typical diameter of the GaP core of ~110 nm.
By using a variety of optical characterization
techniques we demonstrate the NWs grown on Si
substrates have an excellent optical quality that is
comparable to that of the GaNP epilayer grown on
GaP substrates. In all structures, the PL spectra
have the same line shape and originate from
radiative transitions within N-related localized
states. However, the core/shell NW samples have
weaker PL intensity and faster PL decay at room
temperature, indicative for a higher defect density
leading to efficient nonradiative recombination.
From the performed ODMR measurements, the
responsible defects most likely involve a P atom at
their core and are located either at the GaP/GaNP
interface or at the GaNP surface. The high defect
density in the NWs is tentatively attributed to a
high surface-to-volume and interface-to-volume
ratios in these structures.
A. Dobrovolsky1, S. Chen
1,
J. Stehr1, Y. J. Kuang
2,
S. Sukrittanon3, H. Li
4,
C. W. Tu3,4
, W. M. Chen1,
and I. A. Buyanova1
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Identification of
nanocavities water content 1 Departamento de Física de Materiales, Facultad de Ciencias, Universidad Autónoma de
Madrid, Cantoblanco 28049 Madrid, Spain. 2 Instituto de Ciencia de Materiales de Madrid, Consejo Superior de Investigaciones
Científicas, Cantoblanco, 28049 Madrid, Spain.
Water condensation at the nanoscale is known to
play an important role in the collapse of virial
capsids during desiccation [1]. The meniscus
formation along with the geometry of the
nanocavity allows capillary force to modify the
mechanical stability towards collapse [2]. The
changes on the near field optics, during the
desiccation process, may be a good tool showing
how this process takes place. Indeed, scan near
field optical microscope (SNOM) can characterize
sample composition by the changes in the optical
near field. Since the virial capsides are almost
transparent at optical wavelengths [3], different
water contents in these nanocavities will produce
different output signals distinct enough to
characterize the desiccation sequence by SNOM
experiments. Here we present a theoretical study in
which we combine the lattice gas model to
simulate water meniscus formation and a finite
difference time domain (FDTD) algorithm for light
propagation through the media involved. We
simulate a tapered dielectric waveguide that scans,
at constant height, a sample containing a virial
capsides (Fig. 1). Our results show different
contrasts related to different water contents (Fig.
2) and different meniscus orientations. We propose
this method as a way to study water content and
evaporation process in nanocavities being either
biological, like virial capsides, or nonbiological like
photonic crystals.
References
[1] C. Carrasco, M. Douas, R. Miranda, M.
Castellanos, P.A. Serena, J.L. Carrascosa, M.G.
Mateu, M.I. Marqués, and P.J.d. Pablo,
Proceedings of the National Academi of
Science, 106 (2009) 5475-5480.
[2] P.A. Serena, M. Douas, M.I. Marqués, C.
Carrasco, P.J.d. Pablo, R. Miranda, J.L.
Carrascosa, M. Castellanos, and M.G. Mateu,
Physica Status Solidi C, 6 (2009) 2128-2132.
[3] W. M. Balch, J. Vaughn, J. Novotny, D. T.
Drapeau, R. Vaillancourt, J. Lapierre, and A.
Ashe, Limnol. Oceanogr., 45 (2000) 492-498
Figure 1. Schematic representation of the region of
interest for the simulated tapered coated optical fiber
tip. The tip is used for illuminating the region under the
aperture, while transmitted signal is detected at a
distance of 100 nm form the sample (Integration plane).
Maysoun Douas1,2
,
Manuel. I. Marqués1 and
Pedro. A. Serena2
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Figure 2. Optical signal intensity maps coming from the contribution of both, water content and nanocavity during the
desiccation process, we have removed the signal due to the absence of virial capside, therefore both positive and
negative values are present. Water occupation is100 % (A), 75% (B) and 50% (C).
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 59
EELS-HAADF spectrum imaging for
characterization of (AlGa)N
multilayer heterostructures 1 Lab. of Electron NanoScopies, LENS-MIND-IN2UB, Dept. Electrònica,
Universitat de Barcelona, Spain 2 Inst. de Sistemas Optoelectrónicos y Microtecnología, ISOM, Univ. UPM, Spain
3 Also at Paul-Drude-Institut für Festkörperelektronik, Hausvogteiplatz 5–7,
D-10117 Berlin, Germany 4 Laboratorio de Microscopías Avanzadas (LMA) - INA and Departamento de Física de la
Materia Condensada, Universidad de Zaragoza, 50018 Zaragoza, Spain 5 Fundación ARAID, 50004 Zaragoza, Spain.
6 TEM-MAT, (CCiT), Universitat de Barcelona, Solís i Sabarís 1, Barcelona, Spain
Group III nitride materials promise production of optoelectronic devices that cover the entire visible range thanks to their widely–tunable room–temperature band gap energy. Nevertheless, in–plane lattice mismatch between the binary components is an issue affecting their design and growth. This causes proneness of the structures to present defects at the interfaces between compounds, finally decreasing the overall performance of the devices. In the present case we deal with a heterostructure of the binaries AlN/GaN for the configuration of distributed Bragg reflectors (DBR) [1-3]. Reflectivity and X-ray diffraction reciprocal space mapping (XRD–RSM) measurements have been performed in high reflectivity, crack–free, 6, 10 and 20 period AlN/GaN multilayer structures grown by Molecular Beam Epitaxy. These methods are useful for testing optical and structural properties of the samples, viewed as a whole. Furthermore, the sample is thoroughly probed at a local scale through combined high angle annular dark field (HAADF) and low-loss electron energy loss spectroscopy (EELS) in a scanning transmission electron microscope (STEM) equipped with an aberration corrected and a monochromator. Our own-made computer routines are presented as they are useful in the automatization of the analysis of this kind of spectra [4-5]. The combination of these techniques and the great quality of the measured data allows us to recover information of the sample at the nanoscale, with sub-eV energy resolution (for the
EEL spectra [6]). Besides the complete structural characterization of the AlN and GaN layers, the formation of AlGaN transient layers is demonstrated (thick and thin, see Fig.1). The origin of these layers is investigated and its impact in the DBRs optical properties is discussed. Z contrast HAADF imaging shows that structural quality is preserved through the formation of transient AlGaN layers with exceptionally high reproducibility of the segregation phenomenon (See Fig.1). Peak reflectivity and stopband width results are presented for all the samples and compared to theoretically expected values. The analysis points out that to further improve the optical performance of the DBRs, the thicker transient AlGaN interlayer has to be significantly reduced. This would increase interface abruptness and decrease the “thickness disorder” bringing thus direct benefits to the peak reflectivity and stopband width. The mechanisms to control interlayer thickness remain unclear at the moment, constraining thus further advance. Reflectivity in our samples is high (> 90%), and XRD-RSM has shown a good structural quality, assessed by HAADF-STEM micrographs showing a crack–free, highly periodic structure, up to 20 periods. The widths of four layers that compose the periodic heterostructure are measured through the combined HAADF-EELS techniques: ~ 10, 15, 50 and 15 nm for AlGaN1 (AlN–on–GaN), GaN, AlGaN2 (GaN–on–AlN) and AlN layers.
A. Eljarrat1, L. López-
Conesa1, Ž. Gačević2, S. Fernández-Garrido2,3, E. Calleja2, C. Magén4,5, S. Estradé1,6 and F. Peiró1
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Finally, hyper-spectral images at the nanoscale are analyzed with some new designed specialized computer routines. These retrieve important information for the chemical and structural characterization of some anomalous segregations in the multilayer heterostructure (See Fig.1). 2D maps are produced measuring and filtering properties present in the spatially localized spectra. Among these properties are the plasmon excitation, relative thickness or zero-loss-peak (elastic scattering). The combination of EELS and HAADF in STEM has proved to be a valuable tool in the characterization of structural properties from local measurements with great spatial resolution and chemical sensibility.
References
[1] T. Ive, O. Brandt, H. Kostial, T. Hesjedal, M. Ramsteiner, and K. H. Ploog, Appl. Phys. Lett. 85 (2004).
[2] G. Koblmueller, F. Wu, T. Mates, J. Speck, S. Fernandez-Garrido, and E. Calleja, Appl. Phys. Lett. 91 (2007).
[3] G. Koblmueller, R. Averbeck, L. Geelhaar, H. Riechert, W. Hosler, and P. Pongratz, J. Appl. Phys. 93 (2003).
[4] A. Eljarrat, Z. Gacevic, S. Fernández-Garrido, E. Calleja, C. Magén, S. Estradé, and F. Peiró, Journal of Physics: Conference Series 326 (2011).
[5] Z. Gacevic, S. Fernández-Garrido, D. Hosseini, S. Estradé, F. Peiró, and E. Calleja, J. Appl. Phys. 108, 113117 (2010).
[6] R. F. Egerton, Rep. Mod. Phys. 72, 016502 (2009).
Figure 1. (a) STEM-HAADF image of a 20-period AlN/GaN DBR showing the full structure, from the GaN buried layer at right hand side to the top of the DBR. The high periodicity of the structure is appreciated in this image, while lower panel (c) shows a detail of two successive periods. Top graph, (b), shows the aluminum ratio profiles (circles) calculated through Vegard Law analysis of the plasmon excitation energy position along with the HAADF intensity profile (blue). Below, (d) shows the result of determining the plasmon excitation energy (chemically sensitive) in a whole hyperspectral image datacube, corresponding to a nanoscale anomalous segregation.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 61
Electronic properties of
graphene edges
Department of Chemistry, Tokyo Institute of Technology,
2-12-1 Ookayama, Meguro-ku, Tokyo 152-8551, Japan
The presence of edges significantly modifies the
electronic properties of graphene where low
energy electrons behave like massless Dirac
fermions. When graphene is cut into pieces and
edges are introduced into the infinite π-electron
system, the electronic properties near the edges
are changed from the intrinsic one. The resultant
modulation of the electronic states depends on the
distinct type of graphene edge termination called
zigzag- and armchair- directions (Fig. 1), which
correspond to the two fundamental crystal
directions of bipartite lattice. Graphene bipartite
lattice consists of inequivalent A and B hexagonal
sublattices, in which zigzag direction is defined as a
line across A-A (B-B) atoms, while armchair
direction is a line along A-B atoms.
In this presentation, we report the results of
scanning probe characterization of the two finite
effects on the electronic properties near the
graphene edges. The standing wave state is
identified as superperiodic patterns in observed π
states of armchair-terminated graphene edges [1]
and nanographene [2]. The standing wave state is
highly correlated with geometry-dependent
electronic properties of polycyclic aromatic
hydrocarbon molecules in terms of Clar theory. The
observed π state with √3a×√3a periodicity (a = 0.25
nm) in armchair-terminated nanographene
fragments that is prepared by chemical oxidation of
graphene [2] (Fig. 2) is in good agreement with
expected π-electron distributions based on the Clar
theory. In Clar theory armchair-terminated
nanographene is characterized by localization of
aromatic sextets, which is analogous to the
localized standing wave due to the interference.
The edge state is characterized as enhanced
amplitude of local density of state (LDOS) at the
zigzag edges, in which energy dispersion of the π
state reveals a sharp distribution at the Fermi level
[3]. The observed high-resolution LDOS image of
the zigzag edge that is prepared by expansion of
atomic vacancies of graphite by exposure of atomic
hydrogen [4] shows good matching with simulated
Toshiaki Enoki and
Shintaro Fujii
Figure 1. Schematic illustration of zigzag- and armchair-
edges.
Figure 2. Observed π state with √3a×√3a periodicity in
armchair-terminated nanographene fragments.
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image based on density functional theory (Fig. 3).
The key point in achieving well-defined zigzag
edges is to perform all preparation and
measurement procedures strictly under the ultra-
high vacuum conditions, avoiding contact with
ambient environment. As predicted from π-
electron distributions based on the Clar theory,
zigzag-terminated nanographene has π radical
character at the edge sites, indicating that the
zigzag edge site is chemically reactive and can be
oxidized in ambient conditions. In general,
electronic properties of graphene edges can be
altered by edge terminations and therefore it is
essential to gain better understanding of the
influence of edge chemistry on the edge state. We
will thus focus on the experimental characterization
of modified edge states musty due to variation in
edge terminations such as di-hydrogenated- and/or
klein- sites. Depending on the edge terminations
the edge state i.e. the enhanced LDOS at the edge
sites is vanished. Detail will be discussed in
combination with DFT simulations.
Figure 3. Experimental LDOS image of hydrogenated
zigzag edge (left) and simulated DFT image (right).
References
[1] Sakai, K., Takai, K., Fukui, K., Nakanishi, T.
and Enoki, Phys. Rev. B 81 (2010) 235417-1-7.
[2] Fujii, S.; Enoki, T. Angew. Chem. Int. Ed. (2012),
10.1002/anie.201202560 and 10.1002
/ange.201202560.
[3] Kobayashi, Y., Fukui, K., Enoki, T. and Kusakabe,
K., Phys. Rev. B 73 (2006), 125415-1-8.
[4] M. Ziatdinov, S. Fujii, K. Kusakabe, M. Kiguchi,
T. Mori, and T. Enoki, to be submitted.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 63
Integration of plasmonics
within a CMOS environment
CEA, LETI, MINATEC Campus, 17 rue des Martyrs, 38054 Grenoble Cedex, France
We are interested in assessing the potential of
plasmonics for improved optical performances in
various fields of applications such as imaging,
sensing and integrated Si-photonics. Indeed the use
of nanostructured metals can help achieve, for
example, compact color filters or low loss, low
energy consumption optical components. We have
taken up the corresponding challenges of the
development of large scale fabrication of plasmonic
components, in a microelectronic environment
such as the one provided by the CMOS platforms at
CEA-LETI.
I will highlight some noticeable realizations of past
years, and emphasize the peculiarities of CMOS
plasmonics. For example, elementary CMOS
processes can be used to fabricate metallic optical
filters in the IR range whose rejection properties
are interesting for imaging and sensing applications
[1]. We also demonstrated that Cu interconnect
technology can be very valuable to achieve low
optical loss plasmonic functionalities, thanks to
very high quality materials. Impact of grain
boundaries on the plasmon propagation at a Cu
surface will be illustrated [2], as well as use of Cu in
some Si-photonics integrated devices such as
couplers [3] or electro-optical modulators [4].
Throughout those examples, I will discuss the
CMOS compatibility of plasmonics in terms of
technological process and devices’ reliability.
References
[1] J. Le Perchec, et al., Optics Express 19 (2011)
15720.
[2] H.S. Lee, et al, Optics Express 20 (2012) 8974.
[3] C. Delacour, et al, NanoLetters 10 (2010) 2922.
[4] A. Emboras, et al., Optics Express 20 (2012)
13612.
Roch Espiau de Lamaestre
64 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Angular dependence of the
tunneling magnetoresistance in
nanoparticle arrays
Dpto. Física de Materiales, Universidad del Pais Vasco, 20018 San Sebatian, Spain
Due to the small size of the nanoparticles, the
transport through metallic nanoparticle arrays is
governed by the Coulomb blockade physics. To add
one charge to a nanoparticle costs a finite energy,
the charging energy Ec. The transport is suppressed
for energies smaller than the charging energy. Once
there is current through the system, it is a strongly
non-linear function of the voltage because of the
charging effects [1]. When the nanoparticle arrays
are placed between two ferromagnetic electrodes,
the interplay between the ferromagnetism and the
charging effects controls the transport through the
system. In the case of a single nanoparticle if the
spin relaxation time is long, spin accumulation
appears when the magnetic moments of the
electrodes have anti-parallel orientation, but not
for parallel one. In a recent paper [2], it has been
showed that the interplay between ferromagnetism
and charging effect has a dramatic influence on the
nanoparticle arrays, leading to unexpected results.
For arrays with N≥ 3 nanoparticles, there is a
regime with large negative differential conductance
and a huge enhancement of the tunneling
magnetoresistance with respect to the cases of one
or two nanoparticles, see Fig. 1. How these effects
are affected by different factors as asymmetry,
dimensionality, disorder or range of interaction
have been also analyzed [3]. The works [2,3] have
been done for parallel and antiparallel magnetic
orientations of the electrodes. Now we want to
study the case in which the magnetization
directions of the electrodes are noncollinear. This
means that the magnetization directions of the
electrodes form an angle θ, that is different to 0 or
π. For noncollinear magnetization, the spin
accumulation at the nanoparticles, the flow of
current and the tunneling magnetoresistance will
depend on θ [4], as occurs in the case of a single
nanoparticle, see Fig 2.
Figure 1. Tunneling magnetoresistance as a function of
the bias voltage for different arrays sizes at KBT=10-4
Ec ,
and spin polarization p=0.7. Main figure: arrays of
N=3,10 and 20 nanoparticles. Inset: values for one and
two nanoparticles.
Figure 2. Tunneling magnetoresistance as a function of θ
for a single nanoparticle at KBT=10-4
Ec, and p=0.7.
References
[1] E. Bascones, V. Estévez, J.A. Trinidad, and A.H.
MacDonald, Phys. Rev. B, 77 (2008) 245422.
[2] V. Estévez and E. Bascones, Phys. Rev. B, 83
(2011) 020408 (R).
[3] V. Estévez and E. Bascones, Phys. Rev. B, 84
(2011) 075441.
[4] V. Estévez and K.Y. Guslienko, in preparation.
V. Estévez and
K.Y. Guslienko
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 65
Towards sub-100nm resolution
chemical mapping by XRF combined
to simultaneous topography
Aix Marseille Université, CNRS, CINaM UMR 7325, 13288, Marseille, France
The aim of our work is to develop new
instrumentation providing physical and chemical
characterization of individual nanoobjects. For that
purpose, we have designed and fabricated a new
characterization tool combining X-Ray Spectroscopy
and Shear Force Microscopy, working at ambient
conditions, allowing surface topography
measurement simultaneously to chemical mapping
[1,2]. This apparatus is based on the visible
luminescence collection of a sample through the
microscope probe. However, this apparatus only
allows the study of luminescent materials, limited
mainly to semiconductors. To extend the use of the
technique to a wider range of materials, we want
now to collect the X-ray Fluorescence instead of the
visible luminescence during SFM scan, in a similar
concept, as shown in Fig. 1.
Figure 1. Scheme of the instrument principle designed to
simultaneous collect XRF and topography, based on a
Shear-Force Microscope
An incident X-ray beam laterally irradiates a sample
which emits XRF collected through an X-ray
monocapillary and analyzed by an EDX detector.
Approached in near-field mechanical interaction
with the surface and vibrating thanks to a quartz
tuning fork, its apex can be used as a probe of a
shear-force microscope head. This equipment is
thus able to combine simultaneous chemical
mapping and topography of a sample.
For that purpose, we have designed a test-bed to
show the feasibility of this project. Experiments
achieved with a 10 µm diameter X-ray capillary
used for detection carried out with an in-lab
microfocused source show high signal to noise
ratio. Extrapolation of signal intensity that can be
expected if the capillary used is shrunk to 1 µm and
indicate that the concept is realistic in lab, and that
sub 100 nm lateral resolution is achievable in
synchrotron environment.
References
[1] C. Fauquet, M. Dehlinger, F. Jandard, S.
Ferrero, D. Pailharey, S. Larcheri, R. Graziola, J.
Purans, A. Bjeoumikhov, A. Erko, I. Zizak, B.
Dahmani and D. Tonneau, Nanoscale Research
Letters, 6 (2011) 308.
[2] M. Dehlinger, C. Dorczynski, C. Fauquet, , F.
Jandard, A. Bjeoumikhov, S. Bjeoumikhova, R.
Gubzhokov, A. Erko, I. Zizak, D. Pailharey, S.
Ferrero, B. Dahmani, D. Tonneau, Int. J.
Nanotechnol., 9 No 3-7 (2012) 460.
X-ray fluorescence
Xray
monocapillary
Sample
Excitation X-ray beam
EDX detector
pinhole
Quartz
tuning fork
X-ray fluorescence
Xray
monocapillary
Sample
Excitation X-ray beam
EDX detector
pinhole
Quartz
tuning fork
C. Fauquet, M. Dehlinger,
S. Lavandier and
D. Tonneau
66 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Nano-dispersed particles in Fe(Crx)
and their performance under dual
(He+Fe) and triple (H+He+Fe) ion
beam irradiation 1 Lawrence Livermore National Laboratory, Livermore, CA
2 Department of Nuclear Engineering, University of California, Berkeley, CA
Considerable research has been performed on
irradiated nano-dispersed ferritic-martensitic steels
to deduce their radiation hardening and
embrittlement behavior. At low doses (1-5 dpa) the
radiation hardening and DBTT shift saturates [1].
Higher dose studies are necessary to confirm this
behavior and to also investigate the effects of
helium and hydrogen production at relevant doses
for fusion conditions. These studies can be
accomplished with triple beam irradiation where
displacement damage is produced by heavy-ions
and hydrogen and helium are injected
“simultaneously”. A particularly interesting
candidate material class is the nano scale oxide
dispersed strengthened (ODS) steels.
Figure 1. The triple ion beam chamber at CEA Saclay
where heavy ions, H, and He can simultaneously
irradiate one or more specimens (p’vt communication).
Several radiation mechanisms are likely to
determine the upper temperature limit for these
steels: thermal creep and loss of strength, high
temperature helium (and hydrogen) embrittlement,
void swelling (accelerated by helium and
hydrogen), and corrosion [1]. The objective for
accelerated ion-beam testing of materials is to
define more accurately the operational
temperature limits for specific materials and to
identify any unknown mechanisms for materials
degradation that would put these material(s) out of
specification for nuclear energy design purposes.
Dual and triple multiple simultaneous ion-beam
(MSIB) irradiations were conducted at JANNUS-
Saclay (see Figure 1) followed by TEM and
micromechanical post irradiation examination. Fe-
14Cr alloy and K3-ODS steel coupons that were
irradiated with 24 MeV Fe+8
ions to produce
displacement damage and energy-modulated He
and H ions were implanted simultaneously to
emulate the production of transmutation products
from nuclear reactions. The displacement damage,
in dpa (displacements per atom), from Fe8+
, as a
function of depth into the specimen, and the He
and H implantation profiles were deduced using the
SRIM code. A typical calculated profile of the dual
(Fe+He) and triple (Fe+He+H) beam implant is
shown in Figure 2. As shown, the overlap region for
the dpa, He, and H was chosen to be at a shallower
depth than the implanted Fe to avoid the “added
ion effect”.
The scientific challenge is to understand the
relationship between materials processing of the
nano-dispersed steel and its radiation performance.
Our experiments are thus focusing on helium
management, cavity growth, and mechanical
property changes as they relate to structure of the
nano-particles.
M. J. Fluss1, L. Hsiung
1,
S. Tumey1, B. William Choi
1
and P. Hosemann2
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Figure 2. SRIM Calculation of the implantation profile in
Fe of 24 MeV Fe and energy degraded He and H. The dpa
produced by the Fe is shown and the He and H implants
are given in terms of appm/dpa.
We will report some preliminary measurements of
the mechanical properties as a function of the
depth from the surface into the irradiated volume
of the irradiated materials utilizing FIB extracted
and FIB shaped specimens followed by micro-
mechanical testing; indentation and pillar
compression. These measurements reveal the
robustness of the ODS steel to radiation induced
changes in mechanical properties.
Figure 3. A HRTEM image of helium bubbles in
association with “cluster domains” of various shape.
Here each helium bubble appears as white contrast
surrounded by a dark Fresnel fringe in each
underfocused image. The image shows the trapping of
several individual bubbles at a disordered cluster
domain, which suggests that the appearance of cluster
core/bubble shell is a result of the coalescence of small
bubbles as conceptualized in the illustration on the right.
In earlier work [2] we have characterized the
nature of helium sequestration at the nano-
particle/matrix interface. In these TEM
examinations of the irradiated ODS steel we have
discovered that the nano-particle size distribution
can be heavily biased to sub nano-meter scale
particles. This discovery (see Figure 3) has led us to
explore, in more depth, the processing origin of the
structure of the nano-particles. From this work we
have deduced that a complex chemistry during the
consolidation of the precursor powders influences
crystallization, stoichiometry, and leads to the well-
known core-shell structure observed for the nano-
dispersoids in ODS steels. Controlling these
complex chemical and kinetic processes may well
be a key to optimizing the material microstructure
so as to achieve the best radiation tolerance and
long-term performance.
This work was performed under the auspices of the
U.S. Department of Energy by Lawrence Livermore
National Laboratory under Contract DE-AC52-
07NA27344. This work was funded by the
Laboratory Directed Research and Development
Program at LLNL under project tracking code 12-SI-
002.
References
[1] S.J. Zinkle, and N.M. Ghoniem, Fusion
Engineering and Design 51–52 (2000) 55–71,
and N. Baluc et al, Nucl. Fusion 47 (2007)
S696–S717, and E.E. Bloom, S.J. Zinkle , F.W.
Wiffen, Journal of Nuclear Materials 329–333
(2004), pp. 12–19.
[2] L. L. Hsiung, M. J. Fluss, S. J. Tumey, B. W. Choi,
Y. Serruys, F. Willaime, and A. Kimura, Phys.
Rev. B 82, 184103 2010.
68 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Entropy-driven phase transition in
dense packings of athermal chain
molecules
Institute of Optoelectronics and Microsystems (ISOM) and
ETSII, Universidad Politecnica de Madrid (UPM),
Jose Gutierrez Abascal 2, 28006, Madrid, Spain
The random or ordered packing of objects has been
in the spotlight of research since early times. How
spheres, cubes, disks, whether oranges, candies or
molecules, stack up when poured into a vessel is an
intriguing problem with a wide range of practical
applications in colloids, engineering, biology,
materials and polymer science. Hard spheres
constitute the simplest, nontrivial model which
captures interactions based exclusively on the
concept of excluded volume; as such it is amenable
to analytic approaches. Simulations on
crystallization in monomeric hard-sphere packings
were first presented back in 1950s in the works of
Wood and Jacobson [1] and Alder and Wainwright
[2]. Given that athermal systems do not incur into
energetic gains or penalties upon configurational
transitions, entropy is the driving force for phase
transition (crystallization) [3,4]. It is now well
established that given sufficient time, crystal
nucleation and growth can be naturally observed in
monomeric hard-sphere assemblies at all packing
densities above the melting point [5].
While the disorder-order transition and the
corresponding crystal nucleation and growth are
readily observable in simulations of monoatomic
hard spheres the modeling of the corresponding
process in dense packings of hard-sphere chains
(macromolecules) remained, until recently, elusive.
Whether the chain connectivity and the related
holonomic constraints completely halt, partially
frustrate or even do not affect at all, athermal
crystallization remained a controversial topic.
In the present contribution we employ extensive
Monte Carlo (MC) simulations, based on chain-
connectivity-altering algorithms, to generate and
successively equilibrate random (disordered)
packings of freely-jointed chains of tangent hard
spheres of uniform size [6]. Through this modeling
approach thousands of statistically uncorrelated
configurations of the simulated chain systems are
generated at concentrations ranging from very
dilute up to the close vicinity of the maximally
random jammed (MRJ) state [7] within modest
computational time [8].
The degree of ordering (crystallization) is
monitored by means of the characteristic
crystallographic element (CCE) norm [9], a strictly
monotonic and structure-discriminating measure of
order based on the point symmetry group of the
local environment of a site. The CCE norm has been
shown to sensitively and quantitatively detect
changes in local ordering, while identifying the
emerging ordered structure with high specificity
[9]. Once applied to the athermal polymer packings
the CCE norm revealed that in the absence of any
external influence the hard-sphere chains were
observed to systematically and spontaneously
crystallize at all packing densities above 0.56 [10].
Furthermore, the observed phase transition
appears to be insensitive to variations in chain
length and polydispersity, and the crystallinity of
the established stable phase increases with
increasing concentration [11].
By far the most salient feature of the crystal
polymer structures is the presence of a randomly
stack-faulted, layered morphology with a single
stacking direction (Fig. 1). Thus, incipient nucleus
consists of parallel, two-dimensional layers of
either hexagonal close packed (hcp) or face center
cubic (fcc) character in random alternation.
Katerina Foteinopoulou,
Nikos Ch. Karayiannis,
Manuel Laso
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To understand better the driving mechanism and
the entropic origins of the phase transition we
study the rearrangement of local free volume
around each site. Here, local density is determined
as the reciprocal of the volume of the
corresponding Voronoi polyhedron. It is shown that
local free volume becomes more spherical and
more symmetric through the phase transition. In
turn, ordered sites are able to explore their local
vicinity more efficiently increasing their mobility.
Thus, there is a significant increase in translational
entropy which drives the nucleation and growth of
crystals.
Finally, we discuss some recent simulation findings
on the effect of the intensity of the holonomic
constraints (here in the form of bond lengths) on
the ability of chains to crystallize at packing
densities near the melting transition.
Current insights from athermal polymer
crystallization can shed light on the role of entropy
in chemically more complicated phenomena like
protein folding and crystallization in the bulk and
under confinement.
References
[1] W. W. Wood and J. D. Jacobson, J. Chem. Phys.
27 (1957) 1208.
[2] B. Alder and T. Wainwright, J. Chem. Phys. 27
(1957) 1208.
[3] L. Onsager, Ann. N. Y. Acad Sci. 51 (1949) 627.
[4] D. Frenkel, H. N. W. Lekkerkerker and A.
Stroobants, Nature 332 (1988) 822.
[5] M. D. Rintoul and S. Torquato, Phys. Rev. Lett.
77 (1996) 4198.
[6] N. C. Karayiannis and M. Laso, Macromolecules
41 (2008) 1537.
[7] S. Torquato, T. M. Truskett and P. G.
Debenedetti, Phys. Rev. Lett. 84 (2000) 2064.
[8] N. C. Karayiannis and M. Laso, Phys. Rev. Lett.
100 (2008) 050602.
[9] N. C. Karayiannis, K. Foteinopoulou and M.
Laso, J. Chem. Phys. 130 (2009) 074704.
[10] N. C. Karayiannis, K. Foteinopoulou and M.
Laso, Phys. Rev. Lett. 103 (2009) 045703.
[11] N. C. Karayiannis, K Foteinopoulou, C. F.
Abrams and M. Laso, Soft Matter 6 (2010)
2160.
Figure 1. System configurations at (a) early stage of simulation (amorphous packing), and (b) late stage where the
majority of sites possess a highly ordered local environment. Blue and red colored spheres correspond to sites with fcc-
like and hcp-like local order, respectively (c) and (d) same as in (a) and (b) but all sites are colored according to the
parent chain [10].
70 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Molecular Dynamics simulation of
liquid metals for nuclear fusion
technology
Instituto de Fusión Nuclear, ETSII, Madrid Spain
Liquid metals and alloys could be present in future
nuclear reactors as breeder blankets (coolant and
tritium production system) and/or plasma facing
materials in wet walls, divertors in magnetic
confinement reactors etc [1, 2]. In breeding
blankets tritium and helium will be produced by Li
splitting but tritium extraction and tritium
interaction with helium bubbles is still far from
being well understood. Lithium-Lead eutectic alloy
is one of the most promising candidates because of
its low chemical activity compared to pure lithium
and good breeding ratio [3]. Here we present some
atomistic simulations in hydrogen liquid metal
systems. We have studied H (and its isotopes)
diffusion in two different liquid metals making use
of two different interatomic potentials, namely an
Embedded Atom Method (EAM) potential for Pd-H
system [4] and one more advanced EAM/angular
dependent potential for Al-H system [5]. A full
theory of H behavior in liquid metals is, to date,
lacking and experimental results are scarce. Also we
have developed a Li-Pb EAM interatomic potential
capable to predict LiPb eutectic properties [6] after
careful validation of Li and Pb EAM potentials [7-9].
Capabilities to reproduce database are shown. We
address several features dealing to H diffusion in
liquid metals as well as self diffusion of Li in LiPb
systems.
Figure 1. Diffusivity values for H in Al and Pd (see inset)
compared with host metal self-diffusivity (black
squares). H diffusivity (blue line) is close to the
calculated (red = Theory) just as DH= DM√mM where mM
stands for the mass of the host metal.
Alberto Fraile,
Santiago Cuesta-López,
J. Manuel Perlado,
Roberto Iglesias and
Alfredo Caro
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References
[1] V A Evtikhin1 et al. Lithium divertor concept and results of supporting experiments. 2002 Plasma Phys.
Control. Fusion 44 955
[2] Norajitra P. The EU advanced dual coolant blanket concept, Fusion Eng. Des. 61–62 (2002) 449–453.
[3] Wong C. P. C. An overview of dual coolant Pb–17Li breeder first wall and blanket concept development
for the US ITER-TBM design. Fusion Engineering and Design 81 (2006) 461–467.
[4] X. W. Zhou and J. A. Zimmerman, B. M. Wong and J. J. Hoyt. An embedded-atom method interatomic
potential for Pd–H alloys. J. Mater. Res., Vol. 23, No. 3, Mar 2008
[5] F. Apostol and Y. Mishin. Angular-dependent interatomic potential for the aluminum-hydrogen system.
Phys. Rev. B 82, 144115 (2010).
[6] A. Fraile, S. Cuesta-López, A. Caro, J. M. Perlado. To be published.
[7] Zhou X. W. Atomic scale structure of sputtered metal multylayers. Acta Mater. 49, 4005 (2001).
[8] Belashchenko D. Application of the Embedded Atom Model to Liquid Metals: Liquid Lithium. High
Temperature vol 47 No 2 211-218.(2009).
[9] A. Fraile, S. Cuesta-López, R. Iglesias, A. Caro and J. M. Perlado. Submitted to Journal of Nuclear
Materials.
[10] E. M. Sacris and N. A. D. Parlee. The diffusion of hydrogen in liquid Ni, Cu, Ag, and Sn. Metallurgical and
Materials Transactions B. Vol. 1, No 12 (1970), 3377-3382.
[11] E. Ahmed, J. I. Akhter, M. Ahmad. Molecular dynamics study of thermal properties of noble metals.
Computational Materials Science 31 (2004) 309–316
[12] A. Meyer. Self-diffusion in liquid copper as seen by quasielastic neutron scattering. Phys. Rev. B 81,
012102 (2010)
[13] A. Meyer. Determination of self-diffusion coefficients by quasielastic neutron scattering measurements
of levitated Ni droplets. Phys. Rev. B 77, 092201 (2008).
72 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Light emission statistics as a local
probe for structural phase switching 1Instituto de Estructura de la Materia, CSIC, Serrano 121, 28006 Madrid, Spain
2Departamento de Física de la Materia Condensada, Universidad Autónoma de Madrid,
28049 Madrid, Spain 3Instituto de Microelectrónica de Madrid, CSIC, Isaac Newton 8, Tres Cantos, 28760
Madrid, Spain
The statistical properties of light transport and
emission in disordered media has been a matter of
intense research during the last century. Being the
basis of coherent multiple scattering of waves well
known, the phenomenon itself is not yet fully
explored and understood. These multiple wave
scattering effects are at the heart of emerging
behaviors like Anderson localization of light and
electrons, band structure in crystalline solids or
photonic crystals (PhC), among many others.
Although the limits of perfectly ordered systems on
the one hand, and uncorrelated and relatively
weakly scattering systems on the other hand, are
quite well understood. There is a gap between both
limits which is largely unexplored. In particular, it
has been shown in many different situations that
disordered systems exhibiting certain structural
correlations can share properties of both crystalline
and fully disordered systems. For instance, the
conductivity of liquid metals [1] or the cornea
transparency [2] can be understood in the same
footing: a disordered but correlated system can
present spectral regions of high transparency for
electron or light transport.
The effects of disorder in an initially ordered
structure, such as a PhC, might lead to strong
Anderson localization, as the scattering mean free
path can be severely reduced in the band edges [3].
Also, strongly correlated charged colloids can
scatter light in such a way that the transport mean
free path presents a strong chromatic dispersion
[4]. Even in the absence of practically any long
range correlations, the structure of the scatterers
itself can be used to modify the light emission and
transport properties of a disordered system in such
a way that transport parameters [5], or even the
threshold of a random laser [6], can present
resonances which can be tuned in advance.
The effect of correlations in a disordered structure
regarding light emission properties of single
fluorescent emitter has been a matter of much less
intense research efforts. It is clear that the
structure surrounding a single emitter can largely
alter its emission dynamics [7]. In the last years,
several groups considered such effects in a
statistical way suitable for the description of
disordered systems [7,8,9]. In particular, in ref.[9] it
was shown that several structural properties near a
phase transition can be accessed via fluorescence
intensity fluctuations.
It has been theoretically proven that near field
scattering in random systems alters fluorescence
dynamics in such a way that microscopic
information about the surroundings of a single
emitter can be obtained from lifetime fluctuations
or from the shape of the statistical distribution tails
[10,11].
In this presentation, we theoretically show how, in
the previous context, fluorescence emission rate
statistics are largely altered due to the appearance
of structural correlations in a disordered system.
We have developed a model of point resonant
interacting scatterers which are placed at random.
Emission dynamics of a single emitter is calculated
for each sample of an ensemble of structural
realizations of the system.
While keeping constant the scattering properties of
single scatterers, the global geometry, and
scatterers density, the structural correlations are
Luis S. Froufe-Pérez1,
N. de Sousa2, J.J. Sáenz
2 and
A. García Martín3
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controlled changing the temperature of the
interacting set of scatterers.
It is shown that fluorescence decay rate statistics of
a the single emitter correlates with the structural
phase transitions of the system. In the low
temperature limit, the structure freezes in an face
center cubic lattice. This structure presents a gap
(frequency range of low photonic density of states)
corresponding to a small fluorescence decay rate.
As usual, it also presents narrow frequency
windows of high density of states, corresponding to
band edges of the perfect infinite crystalline
structure, leading to high decay rates.
At frequencies corresponding to both a band gap
and a band edge, we perform decay rate statistics
varying the temperature of the system. It is shown
that, at low temperature, decay rates hardly
fluctuates and its average value corresponds to the
crystalline one. On temperature raising,
fluctuations of decay rate grow, and the averaged
values undergoes a relatively sharp transition to a
different value. This transition can be identified
with a structural phase transition in the system.
Interestingly, there is a narrow range of
temperatures in which a strongly confined system
can switch between two metastable structures
which can be identified with liquid and gas. In this
phase switching region, the statistical properties of
the emission dynamics of a single emitter
immersed in the system is strongly coupled to the
structural phase switching. Hence, performing
lifetime statistics can serve as a tool for monitoring
phase switching and nucleation dynamics in
volumes comparable with the emission wavelength
or smaller.
References
[1] N. W. Aschcroft and J. Lekner, Phys. Rev. 145
(1966) 84.
[2] [2] R. W. Hart and R. A. Farrell, J. Opt. Soc. Am.
59 (1969) 766.
[3] Sajeev John, Phys. Rev. Lett. 58 (1987) 2486.
[4] L. F. Rojas-Ochoa, J. M. Mendez-Alcaraz, J. J.
Sáenz, P. Schurtenberger, and F. Scheffold,
Phys. Rev. Lett. 93 (2004) 073903.
[5] P. D. García, R. Sapienza, A. Blanco, and C.
López, Adv. Mater. 19, 2597 (2007); R.
Sapienza, P.D. García, J. Bertolotti, M.D.
Martín, A. Blanco, L. Viña and C. López, D.S.
Wiersma, Phys. Rev. Lett. 99, (2007) 233902.
[6] S. Gottardo, R. Sapienza, P.D. Garcia, A. Blanco,
D. S. Wiersma and C. Lopez, Nat. Phot. 2
(2008) 429.
[7] Jordi Hernando, Erik M. H. P. van Dijk, Jacob P.
Hoogenboom, Juan-José García-López, David
N. Reinhoudt, Mercedes Crego-Calama, María
F. García-Parajó, and Niek F. van Hulst, Phys.
Rev. Lett. 97 (2006) 216403.
[8] H. Gersen, M. F. García-Parajó, L. Novotny, J. A.
Veerman, L. Kuipers, and N. F. van Hulst, Phys.
Rev. Lett. 85 (2000) 5312.
[9] R. A. L. Vallee, M. Van der Auweraer W. Paul
and K. Binder, Phys. Rev. Lett. 97 (2006)
217801.
[10] L. S. Froufe-Pérez, R. Carminati and J. J. Sáenz,
Phys. Rev. A 76 (2007) 013835.
[11] L. S. Froufe-Pérez and R. Carminati, Phys. Stat.
Sol. (a) 205 (2008) 1258.
74 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Graphene plasmonics
1 IQFR – CSIC, Serrano 119, 28006 Madrid, Spain
2 ICFO, Mediterranean Technology Park, 08860 Castelldefels (Barcelona), Spain
We will discuss the extraordinary optical properties
of highly doped graphene, along with new classical
and quantum phenomena involving plasmons in
this material. Doped graphene can host low-energy
collective plasmon oscillations with unprecedented
levels of spatial confinement, large near-field
enhancement, and long lifetimes, which facilitate
their application to enhanced light-matter
interaction, optical detection, sensing, and
nonlinear optics. Graphene plasmons only exist
when the carbon sheet is electrically charged, as
they involve collective motion of the doping charge
carriers, and their frequencies, which scale up with
the doping density, can be readily controlled
through electrostatic gates, thus opening a realistic
avenue towards electrical modulation of plasmon-
related phenemona. We will start with a tutorial
description of graphene plasmons and a critical
comparison with conventional noble-metal
plasmons. A summary of recent experimental
observations will be presented, including spatial
mapping of confined graphene plasmons and
spectroscopic evidence of plasmon-mediated
resonant absorption [1]. Theoretical descriptions of
graphene plasmons will be examined, ranging from
classical electromagnetic theory to first-principles
quantum-mechanical approaches. We will elucidate
the conditions under which quantum nonlocality
shows up in the optical response of this material.
The interaction with quantum emitters (e.g.,
quantum dots) placed in the vicinity of the carbon
sheet will be shown to reach the strong-coupling
regime and potentially serve as a robust platform
for quantum-optics devices that can achieve
temporal control of plasmon blockade, Rabi
splitting, super-radiance, and other quantum
phenomena via electrostatic doping [2]. Classical
devices for infrared spectroscopy, sensing, and light
modulation will be also discussed [3]. Prospects to
extend these phenomena to the visible and near-
infrared regimes will be examined. These advances
in graphene constitute a viable realization of strong
light-matter interaction, temporal control of
quantum phenomena, and ultrafast electro-optical
tunability in solid-state environments, thus bringing
the expectations raised within the field of
plasmonics closer to reality.
Figure 1. Complete optical absorption (top) and
quantum plasmon blockade (bottom) in graphene.
References
[1] Chen et al., Nature 487, 77 (2012); Fei et al.,
Nature 487, 82 (2012).
[2] Manjavacas, Nordlander, and García de Abajo,
ACS Nano 6, 1724 (2012).
[3] Thongrattanasiri, Koppens, and García de
Abajo, Phys. Phys. Lett. 108, 047401 (2012).
Sukosin Thongrattanasiri1,
Alejandro Manjavacas1,
Frank Koppens2 and
Javier García de Abajo1
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Progress towards a single SWAP
molecule with Ruthenium complexes:
DFT study on a gold surface
CEMES-CNRS
29 rue Jeanne-Marvig
F-31055 Toulouse, France
The idea of embedding molecules in between
electrodes to make an electronic device that could
perform the basic functions of digital electronics
begin in the 70's . Due to the intrinsic difficulties of
connecting one molecule to another to make
complete circuits, it was proposed [1] to use just a
single molecule: “mono-molecular electronics”
which could integrate the hole circuit.
One possibility to arrive to these “mono molecular
circuits” is to divide the molecule in “qubits” in
order to exploit the quantum engineering
developed for several years around quantum
computers [2].
The project to be developped consists in
synthetising a molecule which could be able to
realize a logical function such an inversor (SWAP).
This molecular logic gate would be made of
Ruthenium (III) and (II) metal centers [3,4,5], which
magnetic interaction could be turned on/off by
changing the oxidation state of the central
molecule using an appropiate light radiation.
It is very important to have a good understanding
of the behaviour of the building blocks of the target
molecule. In particular we present a DFT study of
the building blocks (Ru (II) and Ru (III) complexes)
on Au(111) in order to understand the magnetic,
electronic and geometrical properties of this
complexes. Especially how the ligands can affect
the magnetism and transport properties of these
metal complexes when adsorbed on surfaces. Some
recent experimental STM images on these
complexes will also be presented.
This work is part of a collaboration between Univ.
Zaragoza-INA and CEMES-CNRS within the TRAIN2
project (Trans-Pyrenees Action on Advanced
Infrastructures for Nanosciences and Nanotechnology).
References
[1] C. Joachim, J.K. Gimzewski, A. Aviram, Nature, 2000,
408, J41.
[2] M.A. Nielsen, I.L. Chiang, Quantum computation &
quantum information, Cambridge University Press
2000.
[3] Synthesis and characterization of
bis(bipyridine)ruthenium(II) complexes with bromo
and protected ethynyl ß-diketonato ligands. S.
Munery, J. Jaud & J. Bonvoisin. Inorg. Chem.
Commun.(2008)11,975-977.
[4] Synthesis and characterization of ß-diketonato
ruthenium(II) complexes with two 4-bromo or
protected 4-ethynyl-2,2’-bipyridine ligands. C. Viala &
J. Bonvoisin. Inorg. chim. Acta (2010) 363, 1409-1414.
[5] Synthesis and characterization of a series of
ruthenium tris(ß-diketonato) complexes with UHV-
STM investigation and numerical calculations. S.
Munery, N. Ratel-Ramond, Y. Benjalal, L. Vernisse, O.
Guillermet, X. Bouju, R. Coratger & J. Bonvoisin. Eur. J.
Inorg. Chem. (2011), 2698–2705.
[6] UHV-STM Investigations and Numerical Calculations
of a Ruthenium β-Diketonato Complex with Protected
Ethynyl Ligand: [Ru(dbm)2(acac-TIPSA)]Loranne
Vernisse, Sabrina Munery, Nicolas Ratel-Ramond,
Youness Benjalal, Olivier Guillermet, Xavier Bouju,
Roland Coratger, and Jacques Jean BonvoisinJ. Phys.
Chem. C, Just Accepted ManuscriptDOI:
10.1021/jp304523f.
S. García-Gil,
J. Bonvoisin and
X. Bouju
sandra.garcia-gi l @ cemes.fr
76 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Tuning physical properties of
polymers by nanoconfinement
Instituto de Estructura de la Materia, IEM-CSIC, Serrano 121, 28006 Madrid, Spain
Arrays of polymer nanostructures exhibit an
interesting behavior that makes them promising
candidates for use in photonics, electronics,
mechanical, and sensor devices [1-3]. High aspect
ratio (length/diameter) one-dimensional (1D)
nanostructures are also appropriate for studying
size-dependent processes with length scales
comparable to the nanostructures’ size.
Figure 1. SEM image of PVDF nanostructures prepared
by solution template wetting. Side view and top view
(inset) showing the nanorod morphology when the
alumina template has been removed.
Material properties strongly depend upon
molecular order and orientation. Crystallization is
one of the simplest molecular-scale self-
organization processes capable to control spatially
the ordering of molecules and hence to tune the
properties of partially crystalline polymer
nanostructures, as they will largely depend upon
the properties of their crystalline domains. Recent
studies of polymer crystallization in restricted
geometries shed some light on the possibility of
controlling crystallization at the nanoscale. Some of
the methods used allow well-defined
nanostructures to be generated, such as via
nanoimprint lithography (NIL) [2], and template
wetting [1, 3].
Wetting of porous anodic aluminum oxide (AAO)
templates has been used in this work for the
preparation of 1D polymer nanostructures. This
technique is based on the fact that both polymer
melts and solutions tend to wet the walls of
nanoporous templates avidly if the walls exhibit a
high surface energy [4] (see Figure 1).
This contribution will cover recent research on
these phenomena, demonstrating the use of
wetting nanoporous alumina (AAO) template with
polymer solution to produce arrays of
poly(vinylidene fluoride) (PVDF) ferroelectric γ-type
nanorods supported onto a nonpolar α-structure
film (Figure 2). The method is based upon a crystal
phase transition due to PVDF confinement within
alumina nanoporous [5]. Based on the previous
experience, we extended our research to
poly(vinylidene-co-trifluoroethylene) (PVDF-TrFE)
random copolymer nanoarrays. X-ray
microdiffraction using synchrotron radiation has
been performed at ID13 beamline (European
Synchrotron Radiation Facility). Scanning the
sample with 1 µm diameter X-ray beam, from the
residual polymer film (bulk) to the nanorod array,
we have investigated the effects of confinement on
5 µµµµm
200 nm
5 µµµµm
200 nm200 nm
Mari Cruz García-Gutiérrez,
Amelia Linares,
Jaime J. Hernández,
Ignacio Martín-Fabiani,
Daniel R. Rueda and
Tiberio A. Ezquerra
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crystal phase transition, degree of crystallinity and
crystal orientation with the aim of optimizing the
ferroelectric properties of polymer nanostructures
for their application in organic electronics [6].
Acknowledgements: The authors thank the financial
support from the MICINN (grant MAT2011-23455).
Figure 2. Two-dimensional X-ray diffraction patterns
recorded in transmission geometry. (top) Diffraction
pattern of the residual PVDF film and (bottom)
diffraction pattern of PVDF nanorods inside porous
alumina. The SAXS region of the patterns has been
enlarged and presented as insets.
References
[1] C. R. Martin, Science, 266 (1994) 1961.
[2] Z. Hu, M. Tian, B. Nysten, A.M. Jonas, Nat.
Mater., 8 (2009) 62.
[3] M. Steinhart, R.B. Wehrspohn, U. Gösele, J.H.
Wendorff, Angew. Chem. Int. Ed. 43 (2004)
1334.
[4] M. Zhang, P. Dobriyal, J.T. Chen, T.P. Russell, J.
Olmo, A. Merry, Nano Lett., 6 (2006) 1075.
[5] M.C. García-Gutiérrez, A. Linares, J.J.
Hernández, D.R. Rueda, T.A. Ezquerra, P. Poza,
R. Davies, Nano Lett., 10 (2010) 1472.
[6] S.J. Kang, I. Bae, Y.J. Shin, Y.J. Park, J. Huh, S-M.
Park, H-C. Kim, C. Park, Nano Lett., 11 (2011)
138.
α α α α form
78 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Light-matter coupling
mediated by surface plasmons
Departamento de Física Teórica de la Materia Condensada and IFIMAC,
Universidad Autónoma de Madrid, Madrid 28049, Spain
In this talk I will analyze two phenomena associated with light-matter coupling and in which surface plasmon
polaritons (SPPs) play a key role. First I will present a fundamental study on how SPPs in a quasi one-
dimensional plasmonic waveguide can be used to engineer the entanglement between two distant qubits.
This two-qubit entanglement is due to the dissipative part of the effective qubit-qubit coupling provided by
the SPPs. The second part of my talk will be devoted to present the theoretical foundation of the
phenomenon of strong coupling between quantum emitters and propagating SPPs observed in two-
dimensional metal surfaces. The case of a single emitter will be analyzed first, exploring the range of
parameters in which the strong coupling regime could emerge. Then we study an ensemble of N quantum
emitters and incorporate the presence of dephasing mechanisms and external pumping into the theoretical
framework. In the final part of the talk the capabilities of graphene surface plasmons to act as mediators in
different light-matter coupling scenarios will be discussed
.
Francisco J. García-Vidal
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 79
Crack mechanical failure in ceramic
materials under ion irradiation:
case of lithium niobate crystal.
Institute of Nuclear Fusion (UPM)
José Gutiérrez Abascal 2
Madrid, Spain
Swift heavy ion irradiation (ions with mass heavier than 15 and energy exceeding MeV/amu) transfer their
energy mainly to the electronic system with small momentum transfer per collision. Therefore, they produce
linear regions (columnar nano-tracks) around the straight ion trajectory, with marked modifications with
respect to the virgin material, e.g., phase transition, amorphization, compaction, changes in physical or
chemical properties. In the case of crystalline materials the most distinctive feature of swift heavy ion
irradiation is the production of amorphous tracks embedded in the crystal. Lithium niobate is a relevant
optical material that presents birefringence due to its anysotropic trigonal structure. The amorphous phase
is certainly isotropic. In addition, its refractive index exhibits high contrast with those of the crystalline
phase. This allows one to fabricate waveguides by swift ion irradiation with important technological
relevance. From the mechanical point of view, the inclusion of an amorphous nano-track (with a density 15%
lower than that of the crystal) leads to the generation of important stress/strain fields around the track.
Eventually these fields are the origin of crack formation with fatal consequences for the integrity of the
samples and the viability of the method for nano-track formation. For certain crystal cuts (X and Y), these
fields are clearly anisotropic due to the crystal anisotropy.
We have used finite element methods to calculate the stress/strain fields that appear around the
iongenerated amorphous nano-tracks for a variety of ion energies and doses. A very remarkable feature for
X cut-samples is that the maximum shear stress appears on preferential planes that form +/-45º with respect
to the crystallographic planes. This leads to the generation of oriented surface cracks when the dose
increases. The growth of the cracks along the anisotropic crystal has been studied by means of novel
extended finite element methods, which include cracks as discontinuities. In this way we can study how the
length and depth of a crack evolves as function of the ion dose. In this work we will show how the
simulations compare with experiments and their application in materials modification by ion irradiation.
David Garoz,
Antonio Rivera, J. Olivares,
F. Agullo-Lopez and
J. M. Perlado
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Coupling of lattice modes in oxides
superlattices: wedding of three
Theoretical Physics of Materials, University of Liège,
Allée du 6 août 17 (B5a), 4000 Liège, Belgium
Complex transition metal oxides form an important
class of compounds, exhibiting a wide variety of
functional properties exploited in various devices.
Thanks to advances in deposition techniques, these
oxides can nowadays be combined in
heterostructures, with a structural quality
comparable to what is achieved for conventional
semiconductors. Creating such heterostructures
gives not only the possibility to combine the
intrinsic properties of different compounds but also
to induce totally new phenomena at their
interfaces. Recent examples include the metallic
and superconducting interface found at the
boundary between the two band insulators LaAlO3
and SrTiO3 or the emergence of so-called improper
ferroelectricity in ultrashort period PbTiO3/SrTiO3
superlattices. In the latter system, the ferroelectric
polarization is no more the primary driver of the
phase transition but arises from an unexpected
trilinear coupling of one polar and two non-polar
lattice modes, producing a complex structural
ground state and unusual dielectric properties.
Recently, a similar type of coupling was shown by
Benedek and Fennie to be a way to achieve an
unprecedented control of the magnetization by an
electric field in single-phase Ca3Mn2O7, a naturally
occurring layered perovskite of the Ruddlesden-
Popper series. The wedding of lattice modes in
layered perovskites looks like a promizing approach
to achieve enhanced magneto-electric coupling but
the identification of compounds realizing that at
room temperature remains a challenge.
After a brief introduction regarding the emergence
of exotic phenomena at oxide interfaces, I will
explain the concepts of improper and hybrid
improper ferroelectricity. I will discuss the
conditions for the appearance of a trilinear
coupling of polar and non-polar lattice modes in
different types of artificial and naturally-occuring
layered perovskites and emphasize the interest of
such a coupling to generate new and/or enhanced
functional properties. Relying on first-principes
simulations, I will then discuss the specific example
of a 1/1 BiFeO3/LaFeO3 superlattice, showing that
this system appears as a promizing candidate to
realize electric switching of the magnetization at
room temperature.
Works done in collaboration with Z. Zanolli, E.
Bousquet, J. Zhao, H. Djani, A.Safari, A. Prikockyté
and D. Fontaine at ULG, J. Iñiguez and J. C. Wojdel
at ICMAB, P. Hermet at University of Montpellier
and the experimental groups of J.-M. Triscone and
P. Paruch at the University of Geneva. Supported by
the European project OxIDes (EC-FP7), the ARC
project TheMoTher and the Francqui Foundation
(Belgium).
Philippe Ghosez
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Photochemical evidence of electronic
interwall communication in double-
wall carbon nanotubes
a Instituto de Nanociencia, Nanotecnología y Materiales Moleculares (INAMOL),
Universidad de Castilla-La Mancha, 45071-Toledo, Spain. b Instituto de Catálisis y Petroleoquímica, CSIC, Cantoblanco, 28049, Madrid, Spain.
c Instituto Universitario de Tecnología Química CSIC-UPV, Universidad Politécnica de
Valencia, 46022-Valencia, Spain
Double-wall carbon nanotubes (DWCNTs) [1] have
attracted considerable attention when compared
to single-wall CNT (SWCNTs), because show some
advantages like higher thermal and chemical
stability and are mechanically more robust [2]. In
addition, DWCNTs, being the simplest example of
multi-wall carbon nanotubes (MWCNTs), are ideal
structures for studying how the interwall
interactions influence the properties of the CNTs
with two or more walls for chemical [3] and
physical [4,5] applications. The electronic
communication between outer and inner tubes is
observed by in situ Raman spectroelectrochemistry
of unmodified DWCNTs; charge transfer from the
outer tube to the inner tube occurs only if the
electronic states of the outer tube are filled with
electrons or holes and if these filled states are
higher in energy than those of the inner tube [6].
Donor-acceptor nanohybrids prepared by covalent
functionalization of SWCNTs with electron donors
are very actively studied as donor–acceptor
nanohybrid models and as building blocks for
optoelectronic devices [7]. Nevertheless, there are
not examples in the literature where a valid
comparison of the photochemical properties of
DWCNT and SWCNT with identical degree of
functionalization has been provided. Despite the
interest in understand the role of the inner, intact
graphenic wall in the properties of CNTs, there are
scarce examples of functionalization of this kind of
CNTs, but, from the avalible data, it is well
established that the functional moiety is selectively
attached to the sidewall of the outer shell of
DWCNTs without disrupting the properties of inner
tubes.
In the current work, we compare the behaviour of
functionalized SWCNT and DWCNT in photoinduced
electron transfer. Single and double wall carbon
nanotubes (CNTs) having dimethylanilino (DMA)
units covalently attached to the external graphene
wall have been prepared by the reaction of
dimethylaminophenylnitronium ion with the
corresponding CNT. The samples have been
characterized by Raman and XPS spectroscopies,
thermogravimetry and high-resolution transmission
electron microscopy where the integrity of the
single or double wall of the CNT and the percentage
of substitution (one dimethylanilino group every 45
carbons of the wall for the single and double walled
samples) has been determined. Nanosecond laser
flash photolysis has shown the generation of
transients that has been derived from the charge
transfer between the dimethylanilino as electron
donor to the CNT graphene wall as electron
acceptor. Time resolved spectroscopy data indicate
María J. Gómez-
Escalonillaa, María
Vizuetea, Sergio García-
Rodriguezb, José Luis G.
Fierrob, Pedro Atienzar
c,
Hermenegildo Garcíac *
and Fernando Langa a
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that the charge mobility in DWCNT is much higher than in the case of SWCNT, suggesting that DWCNT
should be more appropriate to develop fast response devices for nanoelectronics.
References
[1] R. Pfeeiffer, T. Pichler, Y. A. Kim and H. Kuzmany, Double-Wall Carbon Nanotubes, Carbon Nanotubes:
Advanced Topics in the Synthesis, Structure, Properties and Applications, Ed. A. Jorio, M. S. Dresselhaus
and G. Dresselhaus, Springer, New York, (2008), pp 495-530.
[2] Y. A. Kim, H. Muramatsu, T. Hayashi, M. Endo, M. Terrones and M. S. Dresselhaus, Chem. Phys.
Lett.,398, (2004), 87.
[3] A. H. Brozena, J. Moskowitz, B. Y. Shao, S. L. Deng, H. W. Liao, K. J. Gaskell and Y. H. Wang, J. Am. Chem.
Soc.,132, (2010), 3932.
[4] A. A. Green and M. C. Hersam, Nat. Nanotechnol.,4,(2009),64.
[5] A. A. Green and M. C. Hersam, ACS Nano,5,(2011),1459.
[6] M. Kalbac, A. A. Green, M. C. Hersam and L. Kavan, Chem. Eur. J., 17,(2011),9806.
[7] V. Sgobba and D. M. Guldi, Chem. Soc. Rev.,38,(2009),165.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 83
Negative scattering asymmetry
parameter for dipolar particles:
unusual reduction of the transport
mean free path and radiation
pressure 1 Dpto. Física de la Materia Condensada and Instituto Nicolás Cabrera, Universidad
Autónoma de Madrid, Campus de Cantoblanco, Madrid 28049, Spain 2 Department of Physics, University of Fribourg, Chemin du Muse 3, 1700 Fribourg,
Switzerland 3 Instituto de Ciencia de Materiales de Madrid, Consejo Superior de Investigaciones
Científicas (CSIC), Campus de Cantoblanco, Madrid 28049, Spain
Propagation of light and image formation in turbid
media has long been a subject of great interest [1]
and constitutes the core of powerful techniques
with countless applications including biomedical
imaging [2, 3] and dynamic spectroscopy
techniques [4-6], characterization of composite
materials and complex fluids [7], remote sensing or
telecommunications [8] to mention a few.
Lossless dielectric nanospheres (made of
nonmagnetic materials) with relatively low
refraction index may present strong electric and
magnetic dipolar resonances [9-11].
We establish a relationship between the optical
force [12,13] from a plane wave on small electric
and magnetic dipolar particles, the transport cross
section, and the scattering asymmetry parameter g
[14].
In this way we predict negative g (that minimize the
transport mean free path below values of the
scattering mean free path) for a dilute suspension
of both perfectly reflecting spheres as well as of
lossless dielectric nanospheres made of moderate
permittivity materials, e.g., silicon or germanium
nanospheres in the infrared region. Lossless
dielectric Mie spheres of relatively low refraction
index (as low as 2.2) are shown to present negative
g in specific spectral ranges [14].
Figure 1. (a) Color map of the g factor for spherical
absorptionless particles as a function of their refractive
index m and size parameter y = mka. As seen in the
attached scale, green areas correspond to negative
values of g. (b) Color map of the sphere scattering cross
section. Red corresponds to dominant electric dipole
contributions to the scattering cross section. Green
corresponds to dominant magnetic dipole contributions,
while blue sums up all higher-order multipole terms.
Vertical dashed lines coincide with y parameter for
maximum electric dipole contribution (right vertical line)
and maximum magnetic dipole contribution (left vertical
line). The white horizontal line at m ≈ 3.5 which
corresponds to a silicon sphere. (After Ref.[14]).
R. Gómez-Medina1,
L. S. Froufe-Pérez1,
M. Yépez1, F. Scheffold
2,
M. Nieto-Vesperinas3 and
J. J. Sáenz1
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References
[1] Waves and Imaging through Complex Media, edited by P. Sebbah (Kluwer Academic, Dordrecht,
2001); in Wave Scattering in Complex Media: From Theory to Applications, edited by B. A. van
Tiggelen and S. E. Skipetrov, NATO Science Series II: Mathematics, Physics and Chemistry,Vol. 107
(Kluwer Academic, Dordrecht, 2003).
[2] A. Yodh and B. Chance, Phys. Today 48(3), 34 (1995); S. K. Gayen and R. R. Alfano, Opt. Photon.
News 7 (1996) 17.
[3] J. Ripoll, V. Ntziachristos, J. P. Culver, D. N. Pattanayak, A. G. Yodh, and M. Nieto-Vesperinas, J. Opt.
Soc. Am. A 18 (2001) 821.
[4] D. A. Weitz and D. J. Pine, in Dynamic Light Scattering, edited by W. Brown (Oxford University
Press, New York, 1993).
[5] G. Maret and P. E. Wolf, Z. Phys. B 65 (1987) 409; D. J. Pine, D. A. Weitz, P. M. Chaikin, and E.
Herbolzheimer, Phys. Rev. Lett. 60 (1988) 1134.
[6] R. Lenke and G. Maret, in Multiple Scattering of Light: Coherent Backscattering and Transmission,
edited by W. Brown (Gordon & Breach, Reading, UK, 2000).
[7] F. Scheffold and P. Schurtenberger, Soft Mater. 1 (2003) 139.
[8] A. Derode, A. Tourin, J. de Rosny, M. Tanter, S. Yon, and M. Fink, Phys. Rev. Lett. 90 (2003) 14301;
G. Lerosey, J. de Rosny, A. Tourin, and M. Fink, Science 315 (2007) 1120.
[9] A. García-Etxarri, R. Gómez-Medina, L. S. Froufe-Pérez, C. López, L. Chantada, F. Scheffold, J.
Aizpurua, M. Nieto-Vesperinas and J. J. Sáenz, Opt. Express, 19 (2011) 4815-4826.
[10] R. Gómez-Medina, B. García-Cámara, I. Suárez-Lacalle, F. González, F. Moreno, M. Nieto-Vesperinas
and J. J. Sáenz, J. Nanophoton. 5 (2011) 053512.
[11] M. Nieto-Vesperinas, R. Gómez-Medina, and J. J. Sáenz, J. Opt. Soc. Am. A, 28 (2011) 54-60.
[12] M. Nieto-Vesperinas, J. J. Sáenz, R. Gómez-Medina, and L. Chantada, Opt. Express, 18 (2010)
11428-11443.
[13] R. Gómez-Medina, M. Nieto-Vesperinas and J. J. Sáenz, Phys. Rev. A, 83 (2011) 033825.
[14] R. Gómez-Medina, L. S. Froufe- Pérez, M. Yépez, F. Scheffold, M. Nieto-Vesperinas and J. J. Sáenz,
Phys. Rev. A, 85 (2012) 035802.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 85
Nanostructured tungsten as a first
wall material for the future
nuclear fusion reactors 1Instituto de Fusión Nuclear, ETSI de Industriales, UPM, C/ José Gutierrez Abascal, 2,
E-28006 Madrid, Spain. 2CEI Campus Moncloa, UCM-UPM
3Instituto de Energía Solar (IES), UPM, Avenida Complutense s/n, E-28040 Madrid, Spain
4Instituto de Microelectrónica de Madrid, IMM-CNM-CSIC, Isaac Newton 8 PTM,
E-28760 Tres Cantos, Madrid, Spain. 5Dpto. de Física de Materiales, Facultad de CC. Físicas, UCM, Ciudad Universitaria s/n, E-
28040 Madrid, Spain. 6Dpto. de Física de Materiales, Facultad de CC. Químicas, UCM, Ciudad Universitaria s/n,
E-28040 Madrid, Spain. 7Dpto. de Ciencia de Materiales CISDEM, ETSI de Caminos, UPM, E-28040 Madrid, Spain.
The lack of materials able to withstand the severe
radiation conditions (high thermal loads and
atomistic damage) expected in fusion reactors is the
actual bottle neck for fusion to become a reality.
The main requisite for plasma facing materials
(PFM) is to have excellent structural stability since
severe cracking or mass loss would hamper their
protection role which turns out to be unacceptable.
Additional practical requirements for plasma facing
materials are among others: (i) high thermal shock
resistance, (ii) high thermal conductivity (iii) high
melting point (iv) low physical and chemical
sputtering, and (v) low tritium retention.
W has been proposed to be one of the best
candidates for PFM for both laser (IC) and magnetic
(MC) confinement fusion approaches. However,
works carried out up to know have identified some
limitations for W which have to be defeated in order
to fulfill specifications [1, 2, 3]. Nowadays engineered
3D surfaces are being fabricated to reduce the
thermal loads arriving to the PFM by increasing the
surface area and thus, minimize the energy density
deposited into the material [4]. On the other hand,
ultrafine grain and nanostructured materials are being
developed to facilitate the light species release and to
improve the W mechanical properties [5].
We report on the growth of nanostructured W by
using DC magnetron sputtering and high impulse
power magnetron sputtering (HIPIMS) on different
kind of substrates under different deposition
conditions. X-ray diffraction (XRD) patterns
illustrate that films are polycrystalline and
preferentially oriented along the (110) axes.
Transmission electron microscopy (TEM) and field
emission gun-scanning electron microscopy (FEG-
SEM) evidence that films consists of nanocolumns
perpendicular to the substrate with a diameter in
between 50 and 250 nm depending on the
deposition conditions.
Some of the samples were annealed in an Ar
atmosphere at temperatures in the range from RT
to 1000ºC in order to study their thermal stability.
Cross-sectional FEG-SEM images show no
significant change in the nanocolumn shape but
they point up the poor adhesion between film and
substrate for those samples deposited on steels
and heated at temperatures higher than 800ºC.
References
[1] Takeshi Hirai, Koichiro Ezato and Patrick Majerus,
Materials Transactions, 46, (2005) 412-424.
[2] Kajita S., Sakaguchi W., Ohno N., Yoshida N.,
Saeki T. 2009. Nucl. Fus. 49, 095005.
[3] Sharafat S., Takahashi A., Hu Q., Ghoniem N.M.
2009. J. Nucl. Mat. 386-388, 900.
[4] T. J. Renk, P. P. Provencio, T. J. Tanaka, J. P.
Blanchard, C. Martin , and T. R. Knowles, Fusion
Science and technology 61 (2012) 1-24.
[5] M. Rieth et al. private communication.
N. Gordillo1,2
, R. Gonzalez-
Arrabal1, A. Rivera
1,
I. Fernandez-Martinez3,4
,
F. Briones4, J. Del Río
5,
C. Gomez6, J. Y Pastor
7,
E. Tejado7, M. Panizo-Laiz
1
and J. M. Perlado1
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DNA programmed
assembly of molecules Centre for DNA Nanotechnology (CDNA), iNANO and Department of Chemistry, Aarhus University, 8000 Århus C, Denmark
The idea behind our research is to use DNA as a programmable tool for directing the self-assembly of molecules and materials. The unique specificity of DNA interactions, our ability to code specific DNA sequences and to chemically functionalize DNA, makes it the ideal material for controlling self-assembly of components attached to DNA sequences. We have developed some new approaches in this area such as the use of DNA for self-assembly of organic molecules[1] and position dendrimers. We have used DNA origami to assemble organic molecules, study chemical reactions with single molecule resolution [4]. We have also formed 3D DNA origami structures [5] and dynamic DNA structures [6]. Our recent progress on surface modification of DNA origami structures will also be presented.
References
[1] Ravnsbæk; J. B et al. Angew. Chem. Int. Ed. 2011, 50, 10851–10854.
[3] Liu, H. et al. J. Am. Chem. Soc. 2010, 132, 18054-18056.
[4] Voigt, N. V. et al. Nature Nanotech. 2010, 5, 200-205.
[5] Andersen, E. S. et al. Nature 2009, 459, 73-76. [6] Zhang, Z. et al. Angew. Chem. Int. Ed. 2011, 50,
3983–3987.
Kurt V. Gothelf
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What can AFM tell us about
organic photovoltaic systems?
Physics Dept., McGill University, Montreal (Quebec), Canada
The major challenge in Photovoltaic (PV) is the cost
per kWh. It is also clear that continuous growth of
PV will not be achievable by concentrating on just
one material system (such as Si), due to materials
limitations (Ag, In etc. necessary for electrodes).
Hybrid organic-inorganic systems are low cost, but
also have a low efficiency and lifetimes, so the cost
per kWh of energy is currently not very attractive.
The reason for this is fundamentally not well
understood, as the conversion of photons to
electrical power is a complicated many-step
process.
Organic Photovoltaic (OPV) diodes based on
distributed heterojunctions of organic
semiconductors currently produce solar power
conversion efficiencies approaching 10%.
Photocurrent generation in these devices requires
interfacial charge separation of singlet excitons at
donor-acceptor heterojunctions to produce charge
carriers, and it is now clear that this is a multi-step
process involving dissociation of intermediate
electron and hole pairs that are bound by Coulomb
interactions. This last process competes with
relaxation into charge-transfer-exciton states
localized at the heterojunction. Such interfacial
excitons are central to electronic processes at
organic heterojunctions in two important ways.
Firstly, charge-transfer excitons act as intrinsic traps
that limit photocarrier generation, due to their
large binding energy (~300 meV). Secondly, there is
now phenomenological information establishing
the importance of charge-transfer excitons in
defining the open-circuit voltage and short-circuit
photocurrent in organic solar cells, but
fundamental understanding on molecular length
scales lacks.
Building upon previous morphological studies of
tailoring molecular island size and nucleation site
distribution, I will present preliminary results of our
experimental observation of excitons in a model
OPV system. Thin films of PTDCI (an electron donor)
and copper (II) phthalocyanine (an electron
acceptor) molecular islands were grown under ultra
high vacuum conditions on insulators. Structure
and surface contact potential were simultaneously
mapped using nc-AFM and Kelvin probe force
microscopy on a nm scale. We could clearly detect
changes of surface potentials at molecular
heterojunctions under illumination. This open the
possibility of directly correlating exciton diffusion
length, diffusion anisotropy and trapping sites with
atomic scale structure, allowing us to gain deep
fundamental insights.
Figure 1. 3D rendered NC-AFM topography and
corresponding simultaneous KPFM images, overlayed to
illustrate the correlation between film morphology and
surface work function distribution under on/off
illumination conditions. The change in KPFM signal on
the island indicated by the green arrow suggests that
enhanced charge-carrier separation takes place across
the organic heterojunction under illumination.
J. Topple, Z. Schumacher,
A. Tekiel, and P. Grutter
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Interaction effects in graphene
heterostructures
Instituto de Ciencia de Materiales de Madrid. Consejo Superior de
Investigaciones Científicas Sor Juana Inés de la Cruz 3. 28049 Madrid. Spain
New graphene heterostructures built up of
graphene and boron nitride layers have a high
tunability, and they can be the basis of new
devices[1-3]. They show intriguing new
phenomena, such as electron localization induced
by screening, and large Coulomb drag between
carriers in different graphene layers.
The tunability of these devices allow for sizable
modifications of the interactions between
electrons. We discuss here possible new phases
induced by the electron-electron interaction,
including superconductivity at sufficiently high
carrier density.
References
[1] L. A. Ponomarenko, A. K. Geim, A. A. Zhukov,
R. Jalil, S. V. Morozov, K. S. Novoselov, V. V.
Cheianov, V. I. Fal'ko, K. Watanabe, T.
Taniguchi, et al., Nature Phys.7, 958 (2011).
[2] L. Britnell, R. V. Gorbachev, R. Jalil, B. D. Belle,
F. Schedin, M. I. Katsnelson, L. Eaves, S. V.
Morozov, N. Peres, J. Leist, et al., Science 335,
947 (2012).
[3] R. V. Gorbachev, A. K. Geim, M. I. Katsnelson, K.
S. Novoselov, T. Tudorovskiy, I. V. Grigorieva, A.
H. MacDonald, K. Watanabe, T. Taniguchi, L. A.
Ponomarenko, arXiv:1206.6626 (2012).
Francisco Guinea
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Properties optimisation of
titania microfibers
by direct drawing 1 Institute of Physics, University of Tartu, Riia 142, 51014 Tartu, Estonia
2 Department of Materials Engineering, Tallinn University of Technology,
Ehitajate 5, 19086 Tallinn, Estonia 3 Department of Aerospace Engineering, University of Illinois at Urbana-Champaign,
306 Talbot Lab, 104 South Wright Street, Urbana, Illinois 61801, USA
Ceramic microfibers are interests both in scientific
and technological means. One of the main factors
that is supporting the use of fibres is their edgeless
cylindrical geometry, which for externally applied
mechanical stresses can not localize into specific
spots to easily cause cracks. Nanostructured
polycrystalline titania (TiO2) microfibres, studied in
this work were produced by direct drawing from
visco-elastic alkoxide precursors [1,2]. The fibre
crystallinity and grain size were shown to depend
on applied post-treatment (calcination
temperature) conditions. Single fibre tensile tests
showed a strong sensitivity of the elastic modulus
and the tensile strength to the microstructural
features of the fibres. The elastic modulus of as-
fabricated fibres increased about 10 times after
calcination at 700 °C, while the strain at failure
remained almost of the same percentage of ~1.4%
[3]. The highest tensile strength of more than 800
MPa was exhibited by nanoscale grained fibres with
a bi-modal grain size distribution consisting of rutile
grains embedded into anatase matrix [4]. This
structure is believed to have reduced the critical
defect size and thus increased the tensile strength.
The resultant materials showed properties that
were appropriate for reinforcement of different
matrixes.
(a)
(b)
Figure 1. Changes in modulus of elasticity (a) and tensile
strength (b) with temperature of heat treatment.
Kelli Hanschmidt1,3
,
Tanel Tätte1,
Irina Hussainova2,
Marko Part1,
Hugo Mändar1,
Kaspar Roosalu1 and
Ioannis Chasiotis3
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References
[1] T. Tätte, M. Hussainov, J. Gurauskis, H. Mändar, G. Kelp, K. Hanschmidt, I. Hussainova, Nanotechnology
(2010) 245-248.
[2] T. Tätte, M. Hussainov, M. Paalo, M. Part, R. Talviste, V. Kiisk , H. Mändar, K. Põhako, T. Pehk, K. Reivelt,
M. Natali, J. Gurauskis, A. Lõhmus, U. Mäeorg, Sci Tech Adv Mater. 12 (2011) 1-12.
[3] S. Sakka, K. Kamiya, Mater Sci Res. 17 (1984) 83–94.
[4] H. Gleiter, Prog Mater Sci. 33 (1989) 223-315.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 91
Theoretical study of edge states in
BC2N nanoribbons with zigzag edges 1 Nano-scale Theory Group, NRI, AIST
Higashi 1-1-1, Tsukuba, Ibaraki 305-8565, Japan 2 First-Principles Simulation Group, CMSU, NIMS,
Sengen 1-2-1, Tsukuba, Ibaraki 305-0047, Japan
Graphene is an atomically thin carbon sheet in
which carbon atoms are arranged in a honeycomb
lattice. Due to their outstanding electronic
structure and electron transport properties,
graphene attracts much interest for future
electronic devices. Graphene nanoribbons are finite
width graphene sheets. The electronic properties of
graphene nanoribbons strongly depend on the
edge structures [1]. Graphene nanoribbons with
zigzag edges have the so-called flat bands at the
Fermi level [1]. The states corresponding to the flat
bands are localized at the zigzag edges [1]. For the
so-called edge states, the A- (B-) sublattice
structure plays decisive role, i.e., the distribution of
electronic charge of the edge states becomes finite
only one sublattice sites including the outermost
sublattice. Recently, graphene nanoribbons were
fabricated by e-beam lithography [2] and unzipping
of carbon nanotubes [3], and were synthesized
using bottom-up processes [4]. Furthermore, quite
recently, the edge states in graphene nanoribbons
were confirmed by STM/STS measurement [5].
On the other hand, boron and nitrogen atoms
behave as acceptors and donors, respectively.
Therefore, boron-carbon-nitride, i.e., graphene
sheet doped with B and N, should show interesting
electronic properties with controllability by doping.
BC2N sheet is organic analogous of graphene, which
can be regarded as one of example of boron-
carbon-nitride. Graphite-like BC2N was synthesized
using chemical vapor depositions of boron
trichloride, BCl3, and acetronitrile, CH3CN [6]. The
electronic properties of BC2N sheets depend on the
atomic arrangement [7]. The electronic properties
of nanoribbons made with BC2N were investigated
by several authors [8]. However, there are no
reports on the presence of the flat bands and edge
states in BC2N nanoribbons.
In this paper, we investigate the electronic
properties of BC2N nanoribbons with zigzag edges
using a tight binding model. In the tight-binding
model, B and N atoms are described by higher and
lower site energy, EB and EN, compared with that of
C atom, EC, respectively [9]. Let N be a number of
the zigzag lines. We shall consider three different
structures of BC2N nanoribbons with zigzag edges
as shown in the left part of Fig. 1 (a). In this figure,
B and N atoms are indicated by the black and white
circles, and C atoms are located the empty vertices.
It should be noted that atoms are arranged as B-C-
N-C along the zigzag line in these BC2N
nanoribbons.
Figure 1 (b) shows calculated results of the band
structures of BC2N nanoribbons for N = 10. We
observed the flat bands at E = 0. However, we
confirm that the flat bands are absent if atoms are
not arranged as B-C-N-C along the zigzag lines.
Therefore, we can conclude that B-C-N-C
arrangement along the zigzag line is necessary to
obtain the flat bands. In the right part of Fig. 1 (a),
the local density of states (LDOS) at E = 0 for several
structures are shown by the circles. In this figure,
the radii of the circles are proportional to the
magnitude of the LDOS at each site. The electronic
charge is localized at the BC2N nanoribbons edges,
showing the presence of the edge states. As
discussed below, the edge states in BC2N
nanoribbons is different from those in conventional
graphene nanoribbons.
In the model-1, the charge distributions at the both
edges are different each other, i.e., the charge
Kikuo Harigaya1 and
Tomoaki Kaneko2
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Ab
st
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ct
s
distribution at the edge, where the outermost sites
are occupied with C atoms, is similar to that at the
conventional zigzag edge, while the charge of the
edge states at the edge, where the outermost sites
are occupied with B and N atoms, distributes the
both sublattice sites. Recently, Kaneko et al.
showed that the edge states in zigzag graphene
nanoribbons are robust on the substitution of
outermost C atoms with B and N atoms alternately
[10]. However, such substitution causes change in
charge distribution, i.e., the sublattice structure is
broken [10]. The edge states at the edge, where the
outermost sites are occupied with B and N atoms
alternately, are similar to those discovered by
Kaneko et al. [10]. In the model-2 nanoribbon, the
charge distribution of the edge states is similar to
that of graphene nanoribbons, but the sublattice
structure is broken inside the nanoribbons. In the
model-3 nanoribbon, the charge distributes over
both sublattice sites, showing the similarity of
those discovered by Kaneko et al. [10].
In this paper, we also performed the first-principles
calculations based on the density functional
theories within projector-augmented wave method
and the local density approximation implemented
in VASP code. We shall discuss the comparison of
the results within the tight-binding model with
those within the density functional theories.
References
[1] M. Fujita, et al., J. Phys. Soc. Jpn., 65 (1996)
1920, K. Nakada et al., Phys. Rev. B, 54 (1996)
17954.
[2] M. Y. Han et al., Phys. Rev. Lett., 98 (2007)
206805.
[3] D. V. Kosynkin et al., Nature, 458 (2009) 872; L.
Y. Jiao et al., Nature Nanotech., 5 (2010) 321.
[4] J. M. Cai et al., Nature, 466 (2010) 470.
[5] C. Tao, et al., Nature Nanotech., 7 (2011) 616.
[6] M. Kawaguchi, Adv. Matter., 9 (1997) 615.
[7] A. Y. Liu, R. M. Wentzcovitch, and M. L. Cohen,
Phys. Rev. B, 39 (1989) 1760; H. Nozaki and S.
Itoh, J. Phys. Chem. Solids, 57 (1996) 41.
[8] P. Lu, et al., J. Phys. Chem. C, 115 (2011) 3572;
Appl. Phys. Lett., 96 (2010) 133103; B. Xu, et
al., Phys. Rev. B, 81 (2010) 205419; L. Lai and J.
Lu, Nanoscale, 3 (2011) 2583.
[9] T. Yoshioka, H. Suzuura, and T. Ando, J. Phys.
Soc. Jpn., 72 (2003) 2656.
[10] T. Kaneko, K. Harigaya, and H. Imamura, (in
preparation).
Figure 1. (a) Schematic illustration of BC2N nanoribbons (left side) and corresponding LDOS at E=0 for N=10 (right side).
In this schematic illustration, the black and white circles represent B and N atoms, respectively. (b) The band structures
of BC2N nanoribbons with N=10.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 93
Nanotechnology in Latin America
and the Caribbean:
current situation and perspective
Universidad Simón Bolívar / Red Venezolana de Nanotecnología
Caracas, Venezuela
Through the manipulation of nanosized materials to
create new products and processes,
nanotechnology is being a leading driver for socio-
economic development in emerging countries, in
particular in those technology based business. In
Latin America many countries begin to consider and
implement national strategies in order to lever up
the industrialization and competitiveness of the
manufacturing sectors (1-4). The talk will
summarizes and highlights the behavior of
bibliometric indexes as well the activities organized
in the last decades on Nanoscience and
Nanotechnology in Latin America and the
Caribbean region. The current state and
perspectives of nanotechnology, as well the intra
and inter-regional cooperation, will be discussed.
References
[1] Kay L & Shapira P (2009) “Developing
nanotechnology in Latin America” J. Nanopart.
Res. 11: 259-278.
[2] López MS, Hasmy A & Vessuri H (2011)
“Nanoscience and Nanotechnology in
Venezuela” J. Nanopart. Res. 13: 3101-3106.
[3] Delgado GC & Takeuchi N (Eds.) (2011)
“Divulgación y Formación de la nanotecnología
en Iberoamérica: Informe de la Red ‘José
Roberto Leite’-NanoDyF/Cyted”, Mundo Nano.
4, No. 2.
[4] Foladori G, Invernizzi N & Záyago E (Coords.)
Perspectivas sobre el desarrollo de las
nanotecnologías en América Latina ISBN: 978-
607-401-538-6, ReLANS-UAZ-Porrúa Eds.,
México, 2012.
(a)
(b)
Figure 1. (a) The total Nanotechnology publications in
the three more populated Latin American countries
(Argentina, Brazil and Mexico) are compared with the
total number of publications of the region (CELAC) and
Spain in the last two decades. (b) Distribution of the
international cooperation of nanotechnology
publications in Latin America and the Caribbean region.
Anwar Hasmy
94 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Metallic microwires as
non-reflective microwave systems
Universidad Complutense, Spain
It has been shown that either magnetic or non magnetic metallic microwires, forming composites, attenuate
microwave reflection of metallic surfaces. The frequency of maximum antireflective effect (30dB) can be
tuned through the control of volume fraction and aspect ratio of the microwires. It has been found that the
high conductivity of the microwires enable an outstanding enhancement of the electrical permittivity of the
composite. This increase gives rise to the possibility of achieving the destructive interference condition for
composite thickness much shorter than the vacuum wavelength. Experiments carried out on radar
reflections for a Spanish Navy ship previously painted with a composite of microwires and paint are shown
and discussed.
Antonio Hernando
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 95
Application of nanostructures in
aptamer based biosensors 1 Faculty of Mathematics, Physics and Informatics, Comenius University, Mlynská dolina
F1, 842 48 Bratislava, Slovakia 2 Institute of Animal Biochemistry and Genetics, Slovak Academy of Sciences, 900 28
Ivanka pri Dunaji, Slovakia 3 Analytical Chemistry Department, Kazan Federal University, 18 Kremlevskaya Street,
Kazan, 42008, Russian Federation 4 Institut de Chimie Moléculaire et de Matériaux d’Orsay, Université Paris-Sud, Bâtiment
420, 91405 Orsay, France 5 Biophysics Institute, Johannes Kepler Univ. Linz, Altenbergertrasse 69, 4040 Linz, Austria
DNA and RNA aptamers are single stranded oligonucleotides with high affinity to proteins or other ligands that are similar to those of antibodies. The aptamers are selected in vitro by the SELEX method [1]. In solution, aptamers maintain an unique 3D configuration that contains specific binding site to the ligand. Aptamers can be easily modified by biotin, SH or amino- groups, leading to a variety of immobilization strategies on solid supports. Using simple molecular engineering based on DNA hybridization it is possible to develop aptamer dimers containing two binding sites like antibodies [2,3]. These aptamer dimers (aptabodies) are characterized by enhancing sensitivity to the analyte, for example to thrombin or cellular prions. We have shown that typical guanine quadruplexes that form binding site for thrombin are stable in aptamer dimers [4]. Currently there is increased interest in development of aptamer based biosensors (aptasensors) for detection of proteins and other molecules using various sensing methods, such us optical, acoustical and electrochemical [5,6]. Aptasensors could be used for fast and low cost medical diagnostics. The sensitivity of detection depends not only on the selectivity of binding site, but also on the supporting part added to the aptamer that serves for better immobilisation onto a solid support. Nanostructures such as carbon and ZnO nanotubes, graphenes, molecularly imprinted polymers, and that modified by calixarenes and dendrimers are of great advantage in aptamer immobilisation and also improve detection of ligands especially in combination with electrochemical methods.
In this contribution we report various immobilisation and detection strategies of proteins using nanostructured aptasensors. By means of multiwalled carbon nanotubes (MWCNTs) as an immobilization matrix we developed high sensitive biosensor for detection of human thrombin [2] and cellular prions (PrPC) [7] in biological liquids. We have shown that immobilisation of aptamers and aptamer dimers at MWCNTs improved the sensitivity of the sensor for thrombin and allowed detection in a complex matrix such as blood plasma. By means of electrochemical quartz crystal microbalance method (EQCM) we performed comparative analysis of the sensitivity of DNA aptamers and antibodies specific to PrPC immobilised on a surface of MWCNTs. We found that the limit of detection (LOD) for both aptamers (50 pM) and antibodies (20 pM) was comparable. Most recently we substantially improved the LOD using immobilisation of aptamers onto multilayer surface composed of MWCNTs with covalently attached polyamidoamine dendrimers (PAMAM) of fourth generation (G4) conjugated with ferrocene-1'-(N(3-butylpyrrole)butanamide) (Fe-NHP). Streptavidin-biotin conjugation served as linker with biotin-modified aptamer designed for specific prion recognition (Fig. 1a). Using cyclic voltammetry (CV) it has been possible to record reversible redox currents of the ferrocene with oxidation and reduction peaks corresponding to the potentials 0.24 mV and 0.17 mV (vs. Ag/AgCl reference electrode), respectively. The current decreased with increasing PrPC concentrations form 1 pM to 10 µM and reaches saturation after 1 µM (Fig. 1b). The current decay was due to limitation of the electron exchange in the sensing layer. LOD was
Tibor Hianik1, Gabriela
Castillo1, Maja Šnejdarková2, Alexandra Poturnayová2, Anna Porfireva3, Gennady Evtugyn3, Anna Miodek4, Helene Dorizon4, Hafsa Korri-Youssoufi4 and Andreas Ebner5
96 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
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A
bs
tr
ac
ts
found to be 1.3 pM which is acceptable for practical applications. The sensor was tested also in a human blood serum with satisfactory recovery in average of 74%. The interferences with BSA up to concentrations 10 µM were negligible.
Figure 1. a) The scheme of the biosensor based on MWCNTs-dendrimer- ferrocene-streptavidin layer with immobilised aptamers sensitive to PrP
C (1-MWCNT, 2-
Dendrimer, 3-Fe-NHP, 4-Biotinylated aptamer connected to streptavidin, 5-PrP
C). b) Relative changes of the
current peak corresponding to the ferrocene oxidation vs. concentration of PrP
C or bovine serum albumin (BSA),
respectively (ΔI=I-I0, where I0 and I are amplitudes of the current prior and after addition of the analyte, respectively).
Recently we developed new approach for aptamer immobilisation using electropolymerized layer of Neutral Red (NR) at glassy carbon electrode (GCE) onto which polycarboxylated thiacalix[4]arene has been adsorbed by electrostatic accumulation. NR and aminoterminated thrombin-specific aptamer were then covalently linked to the thiacalixarenes by EDC-NHS chemistry (Fig. 2) [8]. The NR reduction
current recorded after 10 min incubation decayed with increased thrombin concentration due to limitation of the electron exchange in the surface layer. The aptasensor makes it possible to determine thrombin in concentration range 0.1–50 nM (LOD 0.05 nM) in blood serum without any alteration of the response in the presence of 100 fold excess of serum proteins.
Acknowledgements: Financial support of Agency for
Promotion Research and Development under the
project No. APVV-0410-10 and SK-FR-0025-09, Slovak
Academy of Sciences under the project mnt-era.net
(proposal No. 2009-50), VEGA 1/0785/12 by Centre of
Excellence SAS for Functionalized Multiphase
Materials (FUN-MAT) and by the Grant of Education
and research ministry of French government are
gratefully acknowledged. We are grateful to Dr.
Human Rezaei and Dr. Jasmina Vidic from VIM group
of INRA France for generous gift of PrPC proteins.
References
[1] A.D. Ellington, J.W. Szostak, Nature, 346 (1990) 818.
[2] T. Hianik, A. Porfireva, I. Grman, G. Evtugyn, Protein and Peptide Letters, 15 (2008) 799.
[3] T. Hianik, I. Grman, I. Karpišová, Chem. Commun., 41 (2009) 6303.
[4] S. Ponikova, K. Tlučková, M. Antalík, V. Víglaský, T. Hianik, Biophys. Chem., 155 (2011) 29.
[5] T. Hianik, J. Wang, Electroanalysis, 21 (2009) 1223.
[6] M. Mascini (Ed.) Aptamers in Bioanalysis, Wiley, New Jersey, 2009.
[7] T. Hianik, A. Porfireva, I. Grman, G. Evtugyn, Protein and Peptide Letters, 16 (2009) 363.
[8] G. Evtugyn, V. Kostyleva, c R. Sitdikov, A. Porfireva, M. Savelieva, I. Stoikov, I. Antipin, T. Hianik Electroanalysis, 24 (2012) 91.
Figure 2. General scheme of the aptasensor assembling for detection thrombin at glassy carbon electrode. Neutral Red (NR) is the electroactive probe [8].
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 97
Ultrafast X-ray nanowire
single-photon detectors and their
energy-dependent response 1 Physics Institute, University of Zurich, Winterthurerstr. 190, 8057 Zurich, Switzerland
2 Institute for Micro- and Nanoelectronic Systems, Karlsruhe Institute of Technology,
Hertzstr. 16, 76187 Karlsruhe, Germany
More than a decade before the successful
development of superconducting nanowire single-
photon detectors (SNSPD) for the optical and near-
IR wavelength range [1], serious efforts were
undertaken to use this detection principle for the
detection of X-ray photons with keV-energies [2].
However, these preliminary X-ray detectors
struggled with problems regarding the relaxation
back into the superconducting state after photon
detection, called latching, making it difficult to
operate the devices in a continuous detection
mode. Recently, SNSPDs were used in time-of-flight
spectrometry of molecules [3, 4]. For this purpose,
a SNSPD from 5 nm thin NbN was successfully
tested for X-ray detection in a feasibility study [5].
However, the absorptivity of thin NbN films for X-
ray photons and therefore the quantum efficiency
of the detectors were low.
In order to enhance the absorptivity of the
superconducting detector, we fabricated an X-ray
superconducting nanowire single-photon detector
(X-SNSPD) from 100 nm thick niobium (Fig. 1(a)).
The detector geometry was designed for a kinetic
inductance large enough to significantly reduce the
above mentioned problem with continuous photon
detection, and small enough for ultrafast pulse
recovery times.
We report on the detection of X-ray photons [6]
with keV-energies in continuous mode with an
ultrafast pulse recovery time TP of less than 4 ns
(Figs. 1(b) and (c)) and an average pulse rise time of
about 190 ps (Fig.1(d)), the latter being limited by
our electronics setup. In contrast to optical photon-
detection in thin-film SNSPDs, X-ray photon
detection was possible even at bias currents
smaller than 0.4 percent of the critical current (Fig.
2 inset (a)).
Figure 1. (a) Optical image of examined X-SNSPD from
100 nm thick niobium. (b) Typical voltage pulses after
X ray photon absorption, with definition of the pulse
length TP shown schematically. (c) Pulse length TP
histogram. (d) Pulse rise time histogram (time spans
between 15 and 85 percent of pulse amplitude). For (b)
(d) the X SNSPD was irradiated by the X-ray tube with an
acceleration voltage of 49.9 kV.
Most remarkably, we observed that the X-SNSPD
signal amplitude distribution depends significantly
on the acceleration voltage of the photon emitting
X-ray tube. Figure 2 shows the corresponding
normalized pulse amplitude histograms at different
acceleration voltages between 7 kV and 50 kV.
Since the detector operates in a single-photon
detection mode (Fig. 2 inset (b)) the variation of the
signal amplitude distribution can be attributed to
the variation of the photon energy spectrum at
different X ray tube settings. This phenomenon,
which is new for SNSPDs, is explained by the
orders-of-magnitude smaller resistance of the
normal conducting domains as compared to the
Kevin Inderbitzin1,
A. Engel1, A. Schilling
1,
K. Il’in2 and M. Siegel
2
98 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
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Ab
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ct
s
situation in thin-film SNSPDs. For acceleration
voltages of the X-ray tube larger than 12.5 kV, we
observe distinct preferred signal amplitudes (see
arrows in Fig. 2) which we may tentatively ascribe
to the main characteristic emission lines of the
tungsten target at 8.4 kV and 9.7 kV, for which a
minimum excitation energy equal to 10.2 keV or
11.5 keV resp. is necessary. These observations
may hint to a certain energy-resolving capability of
our niobium X-SNSPD.
Figure 2. Histograms of signal amplitudes from photons
emitted by the X-ray tube at different tube acceleration
voltages (indicated in the legend) and from photons
emitted by a radioactive Fe-55 source, which mainly
emits at 5.9 keV. The tube acceleration voltage
determines the maximum energy of the emitted
photons. The histograms use a bin size of 4 mV (5.2 mV
for the Fe-55 data respectively) and are normalized at
79 mV, which lies below the noise level. The two arrows
indicate preferred signal amplitudes which may
tentatively be ascribed to the main characteristic
emission lines of the tungsten target at 8.4 kV and
9.7 kV. Inset (a) shows a plot of the count rate as a
function of the reduced bias current at an acceleration
voltage of 49.9 kV. Inset (b) shows that the X-SNSPD
photon count rate is proportional to the photon flux,
which is varied by the X-ray tube anode current.
Moreover, no dark count events were triggered in
over five hours of measurement, even with bias
currents very close to the critical current. Our
results show that ultrafast dark-count-free X-
SNSPDs can be fabricated which can operate in a
large spectral range. They could find applications
where very high count rates, precise timing, a good
signal-to-noise ratio and response in a wide
spectral range for photon counting are required,
such as experiments with synchrotron X ray
sources, free-electron lasers and hot plasmas (as in
nuclear fusion experiments).
In addition, X-SNSPDs from 100 nm thick TaN have
been fabricated and characterized, which show an
increased X ray absorptivity and reduced sensitivity
for latching compared to the X-SNSPD from Nb.
References
[1] G. N. Gol’tsman, O. Okunev, G. Chulkova, A.
Lipatov, A. Semenov, K. Smirnov, B. Voronov,
A. Dzardanov, C. Williams, and R. Sobolewski,
Appl. Phys. Lett., 79 (2001) 705
[2] A. Gabutti, R. G. Wagner, K. E. Gray, R. T.
Kampwirth, and R. H. Ono, Nucl. Instrum.
Methods A, 278 (1989) 425.
[3] K. Suzuki, K. Suzuki, S. Miki, Z. Wang, Y.
Kobayashi, S. Shiki, and M. Ohkubo, J. Low
Temp. Phys., 151 (2008) 766.
[4] N. Zen, A. Casaburi, S. Shiki, K. Suzuki, M.
Ejrnaes, R. Cristiano, and M. Ohkubo, Appl.
Phys. Letters, 95 (2009) 172508.
[5] D. Perez de Lara, M. Ejrnaes, A. Casaburi, M.
Lisitskiy, R. Cristiano, S. Pagano, A. Gaggero, R.
Leoni, G. Golt’sman, and B. Voronov, J. Low
Temp. Phys., 151 (2008) 771.
[6] K. Inderbitzin, A. Engel, A. Schilling, K. Il’in,
and M. Siegel, to be published
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 99
Nano-probing of the surface
excited by keV photon:
what should we detect for high
spatial resolution?
National Institute for Materials Science (NIMS)
1-2-1 Sengen, Tsukuba, Ibaraki 305-0047, Japan
X rays, keV photons with high transmittance and
low refraction indices, are not easy to focus on
nano-scale area. Meanwhile, scanning probe
microscopy (SPM) detecting physical properties is
not favorable for chemical state mapping. SPM of x
ray excited surface (X-SPM) is expected to
compensate these disadvantages and be profitable
for both of x-ray analyses and surface science: X-
SPM limits its detection area on nano-meter-scale
under the tip and probes x-ray absorption sensitive
to chemical states. Various SPM’s detecting
photoelectrons, tunneling current, chemical
bonding force, optical emission, etc., have been
examined to detect the x-ray absorption for this
technique. Now we confront a problem: What
should we detect in X-SPM?
In spite of considerable efforts by a lot of
researchers on this field, we still have difficulties
with this technique. These are mainly caused by a
little x-ray absorption effect on surface and high
background level owing to x-ray excitation of
deeper and wider region than the probing area
with SPM. In order to solve these difficulties, we
developed X-SPM’s based on two original ideas, (1)
lifetime conversion and (2) AC detection [1-3].
(1) Lifetime conversion
It is well known that the lifetime of inner-shell
excitation by x rays is about femtoseconds, fs. It is
obviously undetectable time for SPM. Therefore,
we focused on specific objects which have meta-
stable excitation states with a long lifetime of
milliseconds, ms. As show in Fig. 1, if a sample has
localized electrons in valence states, a sequential
relaxation after the x-ray excitation finally ionizes
the valence states. The valence states excitation
normally has long lifetime of ~ms detectable with
SPM. The conversion from ~fs to ~ms realizes high
efficient detection equivalently. Generally speaking,
the localized electrons can be found in defects,
surface, interface, etc. These localized electrons
have a great potential to induce functionality and
significant change in material properties. This fact
indicates that we can discuss the scientific interests
with X-SPM using the lifetime conversion
technique.
Figure 1. Lifetime conversion from fs to ms.
(2) AC detection
Basically, DC current (including photocurrent and
tunneling current) detections with SPM receive
significant background of photoelectrons from the
outside of the probing area. Therefore, we
detected AC current or force instead of the DC
current. Since the AC current can be represented
with impedance, capacitance probe, i.e., scanning
capacitance microscope (SCM) is available for the
Masashi Ishii
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Ab
st
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ct
s
X-SPM. Figure 2 shows the first report of x-ray
absorption spectra obtained with SCM [1]. The
successful application of SCM suggests that other
related techniques such as EFM (Electrostatic Force
Microscopy) and KFM (Kelvin Force Microscopy)
can be used for X-SPM. The force detection is more
effective to avoid the photoelectrons. By using
EFM, we achieved chemical mapping with a spatial
resolution of a few nm [2].
Figure 2. X-SCM for the AC detection technique.
Figure 3. Charge confinement using AC frequency tuning.
In spite of these particular successes, application to
general samples is not established. In these
methods, the lifetime of the localized electrons in
the valence states determines the detection
efficiency. Unfortunately, the lifetime strongly
depends on samples and is unknown factor
normally. We recently developed another
technique, (3) charge confinement for the lifetime
control. As shown in the inset of Fig. 3, when AC
electric field is applied to samples, the charges are
confined in trapping levels above some frequency
corresponding to an escape time of the charges.
Figure 3 shows an experimental evidence of the
charge confinement in TiO2. The charges are
confined above 1 kHz with an impedance peak,
resulting in enhancement of luminescence from Sm
dopants as a marker [4]. We conclude that AC
frequency is a key parameter for the lifetime
control for technique (2). EFM with a wider
bandwidth AC oscillator is expected to realize X-
SPM for more general samples.
References
[1] M. Ishii, Jpn. J. Appl. Phys. 41, 4415 (2002).
[2] M. Ishii, B. Hamilton, N. R. J. Poolton, N.
Rigopoulos, Stefan De Gendt, and K. Sakurai,
Appl. Phys. Lett. 90, 063101 (2007).
[3] M. Ishii, B. Hamilton, and N. R. J. Poolton, J.
Appl. Phys. 104, 103535 (2008).
[4] M. Ishii, S. Harako, X. Zhao, S. Komuro, and B.
Hamilton, Appl. Phys. Lett., 99, 101909 (2011).
Surface defects
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 101
On the origin of RTS
noise in nanoFETs
Group of Microsystems and Electronic Materials.
GMME-CEMDATIC
ETSIT. Universidad Politécnica de Madrid.
28040-Madrid. Spain.
Electronic nano-devices are giving rise to new
phenomenological effects, since the high surface to
volume ratio associated to their nano-scale volume
makes superficial effects to predominate over bulk
effects. With the reduction of the size of the
devices to the nano-scale, the modeling of some
phenomena traditionally treated as statistical
effects should be carefully revised. A clear example
of these phenomena is the noise in nano-devices
whose dimensions have been reduced looking for
“zero trap” (or “zero dopant”), and thus “zero
noise” devices.
In this communication we analyze the Random
Telegraph Signal (RTS) noise in a nano-scaled
cylindrical transistor specifically designed to
eliminate the presence of traps that commonly
account for RTS noise in micro-sized devices [1],
such as metal oxide semiconductor field effect
transistors [2] or AsGa heterostructures [3]. We
apply a new Admittance-based noise model [4], in
which the electrical noise arises from Fluctuations
of electrical energy in the susceptance of the device
under test followed by their subsequent
Dissipations by the accompanying conductance.
This model, which complies with the
thermodynamic laws and the principles of the
quantum physics, has interesting repercussions in
many systems, allowing to explain some of the
effects [5,6] that are not well managed by the
common theory in use today. In the field of
electrical noise in field effect transistors, which is
considered in this communication, it explains in a
simple way the RTS instability observed in nano-
scaled cylindrical transistors which are designed
looking for a “zero-trap-device”. Contrary to
common theory where the low–frequency noise in
FETs has been attributed to modulation in mobility
and/or carrier density owing to the trapping and
de-trapping processes taking place at bulk and
interface states, the Admittancebased model shows
that any phenomenon that modulates the space
charge region in the vicinity of the semiconductor
surface causes a modulation of the channel trough
the familiar Field-Effect used in transistors and not
by an unlike (though possible) modulation of the
channel conductivity. In particular, this explains
why trapping effects appear in the “zero-trap”
transistor presented in [1]. In this case, the ungated
(thus uncontrolled) channel portion outside the
controlling gate is the responsible of the excess of
noise. Not only the Admittance-based model
accounts for this excess of noise but also explains
the tunability of this RTS noise with a surface
voltage, which is disregarded in the traditional
model.
In conclusion, the fluctuation-dissipation
phenomena (noise) that take place by individual
particles (electrons, phonons, polarons, etc) in
nano-scaled electronic devices can be totally
explained with the new Admittance-based model of
noise. A correct evaluation of this noise based in
thermodynamics and quantum mechanics
principles is of major interest for designing new
devices.
Jose Ignacio Izpura,
Enrique Iborra and
Marta Clement
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References
[1] T. A. Kramer, R. F. W. Pease, “Low frequency noise in sub-100 nm MOSFETs”, Physica E, 19, (2003),
pp. 13-17.
[2] K.K. Hung, P.K. Ko, Chenming Hu, Yiu Chung Cheng. “Random Telegraph Noise in Deep-
Submicrometer MOSFETSs”, IEEE Electron. Dev. Let., 11 (1990), pp. 90-92.
[3] C. Surya, Sze-Him Ng, E.R. Brown, and P.A. Maki. “Spectral and random telegraph noise
characterizations of low-frequency fluctuations in GaAs/Al0.4Ga0.6As resonant tunneling diodes”
Electron Devices, IEEE Trans. 41 (1994), pp. 2016-2022.
[4] J. I. Izpura, J. Malo, “A Fluctuation-Dissipation model for electrical noise,” Circuits and Systems, Vol.
2, No. 3, 2011, pp. 112-120.
[5] J. I. Izpura, “On the electrical origin of flicker noise in vacuum devices,” IEEE Trans. Instrum. Meas.,
Vol. 58, 2009, pp. 3592-3601.
[6] J. I. Izpura, J. Malo, and E. Iborra, “On the effects of Electronic Feedback in the noise of MEMS and
two-Terminal Devices”. Sensors and Actuators A, To be published.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 103
Design of atom and single molecule
boolean logic gates
Nanoscience Group & MANA Satellite
CEMES-CNRS Toulouse
AtMol (www.atmol.eu)
A*STAR VIP Atom Tech, IMRE Singapore
An atomic scale Boolean logic gate is a single quantum system (a molecule or a surface dangling bond circuit)
electronically interacting with atomic scale metallic electrodes supposed to perform alone an “M inputs - P
outputs” digital logic function. All the known designs of atomic scale logic gates: semi-classical circuits,
quantum Hamiltonian circuits and qubit circuits are different versions of a quantum control. Semi-classical
and quantum circuit design rules will be recalled. They differ in the way the classical input data are encoded
on the quantum system and how the quantum to classical conversion proceeds at the outputs. A quantum
design also can benefit from decoherence coming from the interconnections in a way to be planar implanted
at the surface of a passivated semiconductor as explored in the AtMol Integrated European Project.
C. Joachim
104 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Calibrated nanoscale capacitance
and dopant profile measurements
using a novel nearfield scanning
microwave microscope 1Agilent Technologies Austria, Mooslackengasse 17, 1190 Vienna, Austria
2JKU University of Linz, Institute for Biophysics, Altenbergerstr. 69, 4040 Linz, Austria
3Agilent Technologies Inc., NanoDivision, 4330 W. Chandler Blvd., Chandler, AZ 85226, USA
4National Institute for Standards and Technology (NIST), Electromagnetic Division,
Boulder, CO, USA 5Technical University of Vienna, Institute for Solid State Electronics, Floragasse 7,
1040 Vienna, Austria
A scanning microwave microscope (SMM) for
spatially resolved capacitance measurements in the
attoFarad-to-femtoFarad regime is presented. The
system is based on the combination of an atomic
force microscope (AFM) and a performance
network analyzer (PNA).
Figure 1. SiO2 staircase in 3D-topography view (left) and
corresponding PNA amplitude signal (right) used for
calibrated capacitance measurements.
For the determination of absolute capacitance
values from PNA reflection amplitudes, a calibration
sample of conductive gold pads of various sizes on a
SiO2 staircase structure was used (figure 1). The
thickness of the dielectric SiO2 staircase ranged from
10 nm to 200 nm. The quantitative capacitance
values determined from the PNA reflection
amplitude were compared to control measurements
using an external capacitance bridge [1]. Depending
on the area of the gold top electrode and the SiO2
step height, the corresponding capacitance values,
as measured with the SMM, ranged from 0.1 fF to
22 fF at a noise level of ~2 aF and a relative accuracy
of 20% [2].
For dopant profiling, n- and p-doped reference
samples with densities between 1014
and 1019
atoms/cm3 in 1.5 micron-wide regions were imaged
in dC/dV modulation mode (figure 2). A calibration
curve relating signal levels and dopant densities
was established [3].
Possible applications of an SMM range from quality
control of integrated circuits (ICs), solar cells, and
other semiconductor devices to materials science,
(e.g. measurements of quantum dot dielectric
constants), and to bioscience (e.g. the detection of
viruses, and thickness measurements of protein
layers). Examples shown will include capacitance
and dielectric measurements on organic thin films
(SAMs), graphene, nanotubes and nanowires as
well as magnetic bacteria.
Figure 2. Si Dopant density calibration test sample with
densities ranging from 1014
(left side, yellow) to 1019
Atoms/cm3 (right side, blue.)
Gerald Kada1, Matthias A.
Fenner1, Hans-Peter
Huber2, Hassan
Tanbakuchi3, Manuel
Moertelmaier1, Pavel
Kabos4,5Juergen
Smoliner5, Peter
Hinterdorfer2 and Ferry
Kienberger1
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References
[1] H.P. Huber, M. Moertelmaier, T.M. Wallis, C.J. Chiang, M. Hochleitner, A. Imtiaz, Y.J. Oh, K. Schilcher,
M. Dieudonne, J. Smoliner, P. Hinterdorfer, S.J. Rosner, H. Tanbakuchi, P.Kabos, F. Kienberger, Rev
Sci Instrum, 81 (2010) 113701.
[2] J. Smoliner, H.-P. Huber, M. Hochleitner, M. Moertelmaier, F. Kienberger, J Appl Phys, 108 (2010)
064315.
[3] H. P. Huber, I. Humer, M. Hochleitner, M. Fenner, M. Moertelmaier, C. Rankl,A. Imtiaz, T. M. Wallis,
H. Tanbakuchi, P. Hinterdorfer, P. Kabos, J. Smoliner, J. J. Kopanski, and F. Kienberger. J Applied Phys
111(2012), 014301.
106 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Optical limiting by absorption
bleaching in carbon nanotube
devices: comparison of field-induced
and electrochemically-induced
charge injection
NASA Johnson Space Center
2101 NASA Parkway B13 ES4, Houston, USA
We studied direct charge injection in a heterogeneous film of single-wall carbon nanotubes using the
technique of charge-induced absorption. We found that the injected charges screen the excitons in the
semiconducting tubes, reducing their binding energy and transferring oscillator strength from the exciton
transitions to free carriers. These effects parallel those of the electrochemical doping in the same samples.
Furthermore, we interpret the bleaching bias in the electroabsorption (a chi-3 process) in isolated SWNT as
being due to injected charges, which has implications for a variety of SWNT-based optoelectronic devices. I
will discuss the experiments and some potential methods for using this effect in optoelectronic switches.
References
[1] W. Joshua Kennedy and Z. Valy Vardeny, Applied Physics Letters, 98 (2011) 263110.
[2] Christoph Gadermaier, Enzo Menna, Moreno Meneghetti, W. Joshua Kennedy, Z. Valy Vardeny, and
Guglielmo Lanzani, Nano Letters, 6 (2006) 301-305
W. Joshua Kennedy
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 107
Novel “Carbon Nanotube/Graphene
Layer” nanostructures obtained by
injection CVD method for electronic
applications 1 Belarusian State University of Informatics and Radioelectronics, Brovka Str. 6,
Minsk 220027, Belarus 2 Technological Center, Moscow State Institute of Electronic Technology, K-498,
Moscow 103498, Russia
As it was predicted theoretically, a 3D network
nanostructure, composed of parallel graphene layers
stabilized by vertically aligned CNTs, when doped
with lithium cations can be efficient structure for
hydrogen storage [1], and, moreover, this
nanostructure is considered as a novel material with
tailored multidimensional thermal transport
characteristics [2].
First practical realization of CNT/graphene
nanostructures with vertically aligned CNTs grown in
between the graphene layers by CVD method was
reported in ref. [3]. The exfoliated graphene oxide
was selected as the substrate to grow CNTs. These
nanostructures have been successfully used as the
electrodes in supercapacitors. The existence of CNTs
in these nanostructures significantly enhanced the
graphene property by, as believed, bridging the
defects for electron transfer and increasing the basal
spacing between graphene sheets.
However, the proposed method of CNT/graphene
nanostructures realization is extremely complicated.
The experimental fabrication of such nanostructures
with the low cost processes is challenging.
Present investigation is devoted to the creation of
composite nanostructures of the arrays of vertically
aligned CNTs and the planar graphene (graphite)
layers (PGL) located at the top of the CNT arrays
(CNT-PGL nanostructures) by using the only one-step
process - the most simple and low cost CVD process
with the injected catalyst realized at ambient
conditions. One-layer [4], as well as multi-layer
nanostructures [5] were created. The last
nanostructures we designated as CNT-PGL
nanostacks.
Composite carbon structures were synthesized by
the injection CVD method using xylene/ferrocene
solution, as described in refs [4, 5]. Rate of injection
was varied in the range 0,01-0,2 cm3/min. The
constant flow of Ar (100 cm3/min) through a reactor
was provided during the processes of reactor
heating and cooling and CNTs synthesis. The content
of ferrocene in the feeding solution was 1,0 (wt %).
The process was carried out at the atmospheric
pressure at the working temperatures of 850˚C.
Wafers of n-type Si with 600 nm thermal oxide layer
were used as substrates.
The elemental composition were investigated by
Auger and EDX spectroscopy, structural
characterization was performed using scanning and
transmission electron microscopy, Raman
Spectroscopy.
Figure 1. SEM images of the fragments of the one-layer
CNT-PGL nanostructure: (a) nanostructure formed on
Si/SiO2 substrate, (b) graphene strips detached from the
surface of CNT array at different magnifications, (c) back
side of a strip with the attached CNTs.
Si SiO2
а b
c d
V. Labunov1,
A. Prudnikava1,
I. Komissarov1, B. Shulitski
1,
Y. Shaman2, V. Galperin
2
and A. Basaev2
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The growth mechanism of one- and multi-layer CNT-
PGL nanostructures was proposed.
In Fig. 1 the SEM images of the fragments of one-
layer CNT-PGL nanostructure are presented.
It was proved that the structure consists of carbon,
i.e. represents CNT-PGL structure indeed. What is
particular, PGL can be easily detached from the CNT
array (Fig. 1a-d). The strips of graphene may be used
for the production of different devices or for the
physical experiments.
In Fig. 2 it is shown that by the developed technology
one can produce any number of layers of CNT-PGL
nanostructures. For example, three-layer (Fig. 2a) and
four-layer (Fig. 2b) nanostructures are presented.
Figure 2. SEM images of multi-layer CNT-PGL
nanostructures: (a) three-layer (indicated with arrows)
and (b) four-layer nanostructures.
The CNT-PGL nanostructures presented in Figs. 1,2 are
“ordered” nanostructures, because they demonstrate
strongly organized configuration of CNT-PGL layers.
Another type of CNT/graphene nanostructures,
“disordered”, obtained by the same method, but in
different regimes are presented in Fig. 3.
Figure 3. (a, b). “Disordered” CNT/graphene
nanostructures shown at different magnifications (SEM).
In our approach the high-quality CNT/graphene
nanostructures are produced by a very low cost
process. We expect to observe extraordinary
electrical properties of these structures and
compatible commercialization conditions with any
other approach. Moreover, the used CVD technique
is versatile and scalable. The obtained
nanostructures can enable many applications
including high-performance elastic and flexible
conductors, electrode materials for lithium ion
batteries and supercapacitors, thermal
management, catalyst and biomedical supports,
electrical energy storage devices based on this new
class of carbon material, and so on.
References
[1] Dimitrakakis, G.; Tylianakis, E.; Froudakis, G.,
Nano Letters, 10 (2008) 3166-3170.
[2] Varshney, V.; Patnaik, S.; Roy, A.; Froudakis, G.;
Farmer, B., ACS nano, 2 (2010) 1153-1161.
[3] Fan, Z.; Yan, J.; Zhi, L.; Zhang, Q.; Wei, T.; Feng,
J.; Zhang, M.; Qian, W.; Wei, F., Advanced
Materials, 33 (2010) 3723-3728.
[4] Labunov, V. A.; Shulitski, B. G.; A.L. Prudnikava;
Y.P. Shaman; Basaev, A. S., Semiconductor
Physics, Quantum Electronics &
Optoelectronics, 2 (2010) 137-141.
[5] Labunov, V.; Shulitski, B.; Prudnikava, A.;
Basaev, A., physica status solidi (a) (2010) 1-6.
b
3 μm
a
b
a
0.5 μm
0.4 μm
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 109
Emergent non-scalable behavior in
the nanoscale
School of Physics, Georgia Institute of Technology
Atlanta, GA 30332-0430 USA
Finite materials systems of reduced sizes exhibit
discrete quantized energy level spectra and specific
structures and morphologies, which are manifested
in unique, non-scalable, size-dependent physical
and chemical properties. Indeed, when the scale of
materials structures is reduced to the nanoscale,
emergent behavior often occurs, that is not
commonly expected, or deduced, from knowledge
learned at larger sizes. Characterization and
understanding of the size-dependent evolution of
the properties of materials aggregates, and their
propensities for size (“magic numbers”) and shape
self-selection and for self-assembly, are among the
major challenges of modern materials science.
Using computer-based first-principles quantum
computations and simulations [1], often in
conjunction with laboratory experiments, we
highlight and illustrate such behavior in diverse
nano-scale systems. In particular, we focus on the
following topics: (i) Charging effects in
Nanocatalysis [2], (ii) Pathways of post-ionization
proton-coupled-electron-transfer (PCET) DNA
reactions underlying mutagenesis and malignancy,
and involving a segmented water-wire transport
mechanism [3]; (iii) Coexistence of correlated
electron liquids and weakly-pinned Wigner crystals
under high magnetic fields in the fractional
quantum Hall effect regime, observed recently in
the neighborhood of 1/3 fractional filling in 2D
semiconductor quantum dots, and explained by a
unified microscopic theory [4].
* Supported by the US Department of Energy and
the Air Force Office of Scientific Research.
References
[1] U. Landman, “Materials by Numbers:
Computations as Tools of Discovery”, Proc.
Nat. Acad. Sci. (USA) 102, 6671 (2005).
[2] A. Sanchez, et al., J. Phys. Chem. A 103, 9573
(1999); B. Yoon, et al., Science, 307, 403
(2005); U. Landman, et al., Topics in Catalysis
44, 145 (2007); S. M. Lang, et al., JPC C 115,
6788 (2011); B. Yoon, et al., JPC C 116, 9594
(2012);
[3] R.N. Barnett, et al., Science 294, 567 (2001); J.
Am. Chem. Soc. 128, 10798 (2006); Acct.
Chem. Res., 43, 280 (2010); J.J Joseph et. al.,
Am. Chem. Soc. (2012).
[4] C. Yannouleas and U. Landman, Phys. Rev. B
84, 165327 (2011).
Uzi Landman
110 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Fabrication and characterization
of nanopores in
Si based materials Ben-Gurion University of the Negev, P. O. Box 653, Beer-Sheva, Israel
The use of single nanopores (NPs) as biomolecule
sensing elements has gained a lot of interest in
recent years. In such biosensors the change in ionic
current when the analyte molecule translocates
through the NP is monitored, providing both
quantitative and qualitative analytical information.
The membrane’s material is important factor for
determining the resulting shape and surface properties that are extremely important for the
sensing process, and also affects fabrication
conditions. Thus, there is a constant quest for novel
techniques allowing the fabrication of NPs tunable,
in both size and materials properties. Herein, we
present fabrication, electrical and shape
characterization methodologies of NPs drilled in
silicon based membranes, including Si3N4,
crystalline Si and multilayered SiO2/Si/SiO2
membranes.
A novel method for the fabrication of NPs using
focused electron beam induced etching (FEBIE) will
be presented [1-3]. In this technique, pores are
etched by a cyclic process of reducing either nitride
or oxide membrane to elementary oxide followed
by spontaneous etching of the Si by XeF2. NPs can
be drilled with high precision with diameter in the
range of 10–200 nm, depending on electron
exposure time and acceleration voltage, and XeF2 pressure. The 3D shape of the NP is shown to
depend on the type of membrane used. Forming
NPs in both Si3N4 and SiO2/Si/SiO2 multilayers
membranes results in a funnel-like shape NPs [2, 3].
However, in the latter case cylindrical shape can be
obtained, depending on the post exposure time to
XeF2. This method facilitates the formation of high
aspect-ratio structures in rather thick membranes,
for which other the traditional NP drilling by
transmission electron microscope (TEM) fails. Additionally, due to the chemical nature of the
method, the chemical structure of the NP rims is
identical to that of the bulk material. This single
step process opens the way to fast integration with
silicon technology, making the suggested devices
especially suited for lab-on-chip applications.
I will further present a model we developed to
extract the 3D shape of the NPs from the
dependence of the ionic conductance of NPs on the
ionic strength of the electrolyte used in the
experiments [4], eliminating the need for
elaborated and expensive electron microscope analysis. The suggested methodology can be used
to monitor changes in the NP shape after
manufacture and during electrical characterizations
with high precision.
References
[1] Yemini M, Hadad B, Liebes Y, Goldner A and
Ashkenasy Nanotechnology, 20 (2009) 245302.
[2] Liebes Y, Hadad B and Ashkenasy N,
Nanotechnology 22 (2011) 285303.
[3] Liebes Y., Bandalo V., Sökmen Ü., Tornow Marc
and Ashkenasy N., (submitted).
[4] Liebes Y, Drozdov M, Avital Y Y, Kauffmann Y,
Rapaport H, Kaplan W D and Ashkenasy N,
Appl. Phys. Lett. 97 (2010) 223105.
Liebes Yael,
Rapaport Hanna and
Ashkenasy Nurit
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 111
Rapid conversion from protein-caged
nanomaterials to microbubbles:
a sonochemical route toward
bimodal imaging agents † Departments of Biomedical Engineering,
‡ Physics,
¶Bioscience Technology,
§ Center for
Nano Bioengineering, and Center for Nano-Technology, Chung Yuan Christian University,
Chung-Li 32023, Taiwan; + Department of Biomedical Engineering and Environmental Sciences, National Tsing Hua
University, Hsinchu 30013, Taiwan; ┴ Departments of Medical Research and Internal Medicine, Mackay Memorial Hospital, and
Department of Medicine, Mackay Medical College, Taipei 10449, Taiwan; #Department of Health Developing and Health Marketing, Kainan University, Taoyuan 33857,
Taiwan; ║Graduate Institute of Clinical Medicine, Graduate Institute of Medical Sciences, and
Graduate Institute of Biomaterials, Taipei Medical University, Taipei 110, Taiwan
We report a facile method for nanoparticle (NP)-
coated microbubbles (MBs), which can be used for
bimodal ultrasound contrast agent. Based on our
previous reported amphiphilic polymer [1],
hydrophobic NPs not only can be transferred to
aqueous solution, but can offer a universal surface
for proteins assembly as core-shell complex of
NP/protein corona. The polycarboxylate polymer was
used successfully for linking inorganic colloidal NPs of
different materials (Au, CdSe/ZnS, Fe3O4) to BSA
protein corona. A second type of protein-caged
nanomaterials, protein-caged gold nanoclusters
(AuNCs) can be synthesized by intra-protein
“biomineralization” or self-assembly of AuNCs with
proteins, thus resulting in high photoluminescence in
red to near-infrared emission. Both types of protein-
caged nanomaterials can be rapidly converted into
MBs by introducing sonochemical route, which
promote disulfide crosslinking of cysteine residues
between protein-caged nanomaterials and free
albumin during acoustic cavitation. Further, the
functionalization of MBs can be easily achieved by
adjusting the original NP/protein mixture. We also
demonstrated different imaging modalities with
biocompatible AuNC-coated MBs, used in
conjunction with both in vitro/ in vivo ultrasound and
fluorescent imaging, which can held many potential
applications in medical diagnostics and therapy [2].
Figure 1. Scheme of synthesis of protein-caged
nanomaterials toward dual-functional MBs.
References
[1] Lin, C.-A. J.; Sperling, R. A.; Li, J. K.; Yang, T. Y.; Li,
P. Y.; Zanella, M.; Chang, W. H.; Parak, W. G. J.,
Design of an amphiphilic polymer for
nanoparticle coating and functionalization.
SMALL 2008, 4, (3), 334-341.
[2] Lin C. A. J., Chuang W.K., Huang Z.Y., Kang S.T.,
Chang C.Y., Chen C.T., Li J.L., Li J.K., Wang H.H.,
Kung F.C., Shen J.L., Chan W.H., Yeh C.K., Yeh H.I.,
Lai W.F.T., and Chang W.H., Rapid
Transformation of Protein-Caged Nanomaterials
into Microbubbles As Bimodal Imaging Agents,
ACS Nano, ASAP, 2012. DOI:
10.1021/nn300768d.
Cheng-An J. Lin†§
, Wen-Kai
Chuang†, Zih-Yun Huang
†,
Shih-Tsung Kang+, Ching-Yi
Chang†, Ching-Ta Chen
†,
Jhih-Liang Li†, Jimmy K. Li
†,
Hsueh-Hsiao Wang┴, Fu-
Chen Kung#, Ji-Lin Shen
‡§,
Wen-Hsiung Chan¶§
, Chih-
Kuang Yeh+, Hung-I Yeh
┴,
Wen-Fu T. Lai║ and Walter
H. Chang†§
112 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Nanopillars as plasmonic platform to
enhance nonlinear vibrational sum-
frequency generation spectroscopy 1Lasers and Spectroscopies Laboratory (LLS), Research Centre in Physics of Matter and
Radiation (PMR), University of Namur (FUNDP), Belgium 2Institute of Condensed Matter and Nanosciences - Bio & Soft Matter (IMCN/BSMA),
Université catholique de Louvain (UCL), Belgium 3it4ip, Seneffe, Belgium
Metallic nanostructures such as nanopillars and
nanoantennas are able to confine the energy of an
incident radiation into volumes much smaller than
the wavelength of incoming waves through
localized surface plasmon resonance (LSPR) [1]. This
electromagnetic-field enhancement, attributed to
the collective motion of free electrons, has been
extensively used for surface-enhanced Raman
scattering (SERS) and other surface-enhanced
spectroscopic processes. This has driven metal
nanostructures to become a powerful tool for
chemical and biological optical sensing
experiments[2].
In this work, we coupled such localized
electromagnetic-field enhancement effect to a
nonlinear second-order optical spectroscopy to
obtain high molecular signal intensity and
sensitivity. The technique is based on a three waves
mixing process in which one infrared (ω1) and one
visible (ω2) photon interact together with matter to
generate a new coherent photon at the sum
frequency (ωsfg = ω1 +ω2). The whole process relying
on the second order nonlinear susceptibility χ(2)
,
the sum frequency generation (SFG) signal can be
emitted only where the centrosymmetry is broken,
that is at surfaces and interfaces separating two
bulk media[3,4]. In fine, SFG spectroscopy is a
background free vibrational surface-sensitive
spectroscopy able to retrieve accurate information
on molecular thin films properties, such as
conformation, orientation, dynamics, bio-
recognition processes, phase transitions.
Here, we report a strong enhancement of the
vibrational SFG signal from molecules adsorbed on
metallic nanopillars when those latter are excited
at their localized plasmon resonance frequencies.
In detail, gold nanopillars, sizing around 100 nm in
height and 60 nm in diameter, stand vertically on a
substrate of gold or platinum. The nanopillars
exhibit two plasmon modes that can be selectively
excited by the incident visible laser beam or by the
generated SFG beam itself. Until now, for a density
of 109 nanopillars/cm
2, the molecular SFG signal
obtained on such nanostructured surfaces is more
than 100 times larger that what can be achieved on
unstructured flat surfaces. Besides, because of the
directional profile of the two plasmon modes, an
adequate choice of the beams polarizations and
frequencies leads to a spatial selectivity of the SFG
emission. It is indeed likely possible to selectively
probe the molecules adsorbed onto the nanopillar
side wall, the nanopillar top part (as shown on
Figure 1), or the flat region of the substrate in-
between the pillars. This gives promising issues to
set up label free vibrational bio-recognition
platforms with “multi-zone” enhanced sensitivity.
References
[1] L. Novotny and N. van Hulst, Nat. Photon. 5
(2011) 83
[2] Willets, K. A.; Van Duyne, R. P., Annu. Rev. Phys.
Chem., 58 (2007) 267-297.
[3] Shen, Y. R., Nature, 337 (1989) 519-525.
[4] Vidal, F.; Tadjeddine, A., Rep. Prog. Phys. 68
(2005) 1095-1127.
Dan Lis1, Yves Caudano
1,
Marie Henry2,
Sophie Demoustier-
Champagne2,
Etienne Ferain3 and
Francesca Cecchet1
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Figure 1. The left figure shows SFG spectra in ppp polarization (in the order SFG, Vis and IR beam) of a dodecanethiol
(DDT) molecular film adsorbed over the sample surfaces. The red curve corresponds to the spectra of the DDT layer
adsorbed over a flat platinum surface, while the blue curve is the spectra recorded on the gold nanopillar region when
those latter have their longitudinal LSPR mode excited at 650 nm by the visible laser beam. A schematic representation
of the the experimental conditions is shown in the right figure. An important SFG intensity increase (blue curve) is
observed thanks to the excitation of the LSPR mode of the nanopillar.
114 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Nanoscale metallic and
metal-ceramic multilayers for
radiation-resistant applications
IMDEA Materials Institute, C/Erik Kandel 2, Tecnogetafe, 28906 Getafe (Madrid), Spain
Depart. of Materials Science, Polytechnic University of Madrid, 28040 Madrid, Spain
High energy neutron and proton radiation can
induce serious damage in structural metals,
including void swelling and embrittlement. Hence
the design of advanced metallic materials with
significantly enhanced radiation tolerance is critical
for the application of advanced nuclear energy
systems. Nanoscale metallic and metal-ceramic
multilayers are currently under consideration as
potential candidates to overcome this problem as a
result of their unique mechanical properties and of
their ability to withstand radiation without
degradation of the mechanical performance. Both
behaviors come about as a result of the large area
fraction of interfaces which control the multilayer
mechanical properties and radiation resistance
when the layer thickness is below 100 nm.
In this presentation, the mechanical behavior of
two nanoscale multilayer systems (Cu/Nb and
Al/SiC) is analyzed as a function of processing route
(magnetron sputtering or accumulated roll
bonding), layer thickness (in the range 5 nm to 50
nm) and temperature (from room temperature up
to 400ºC). Results form novel nanoindentation and
micropillar compression tests at different
temperatures, combined with transmission
electron microscopy and numerical modeling,
together with current theoretical models are used
to understand the dominant deformation and
fracture micromechanisms of this novel
nanostructured materials.
Javier LLorca
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Hierarchical micro-nano-structures
for cell adhesion studies a Nanotechnology Platform, Parc Científic Barcelona, 08028 Barcelona, Spain
b Advanced Digital Microscopy Core Facility, Inst. for Research in Biomedicine,
08028 Barcelona, Spain c Institut de Bioenginyeria de Catalunya, 08028 Barcelona, Spain
Introduction
The capacity to fabricate materials exhibiting well-
defined features able to selectively interact with
biology at cellular and subcellular levels has had
tremendous implications in the field of tissue
engineering. It is now well established that cell
behaviors can be controlled, enhanced, or
diminished by interacting with surface
topographies of different size scales (1-3).
However, the reasons behind these effects are not
well understood and motivate the development of
materials that facilitate the systematic study of cell-
topography interactions. With this in mind, we
report two different fabrication processes to build
hierarchical structures in a variety of different
materials in order to investigate the competitive
effects of micro and nanotopographies on cell
adhesion, spreading, and morphology.
Materials and Methods
Micro and nanofabrication techniques such as ion
beam lithography (FIB), electron beam lithography
(EBL), photolithography, and reactive ion etching
(RIE) were combined to create micro/nano
hierarchical structures on silicon. Two distinct
strategies were developed in order to create high
resolution surface topographies with the chance to
build versatile designs. Then, these structures were
transferred to a number of biocompatible polymers
including polydimethylsiloxane (PDMS),
polymethylmethacrylate (PMMA), low density
polyethylene (LDPE), and recombinant elastin-like
polypeptides (ELP). PMMA samples consisted on
four different patterned areas with microchannels,
nanochannels and perpendicular and parallel
micro/nanochannels were fabricated in order to
determine the competitive and synergetic effect of
the micro- and nano-scale topographies in rat
mesenchymal stem cells adhesion and morphology.
Results and Discussion
Scanning electron microscopy (SEM) and atomic
force microscopy (AFM) observations revealed that
hierarchical topographical patterns consisting of
perpendicular and parallel micro/nanochannels
were fabricated in silicon and then these structures
were successfully transferred to the different
polymeric materials. Optical, widefield
epifluorescence, confocal, and SEM observations
revealed that the cells changed their morphology,
alignment and elongation, depending on the
different surface topographies (Fig. 1). Cell
alignment and elongation significantly increased on
parallel nano/microchannels (Figs. 1, 2). However,
cells did not have a significant preference for micro
or nanochannels in perpendicular region (Fig. 2).
Conclusions
We have developed two distinct methods to
fabricate hierarchical structures with high
resolution and accurate topography control in
silicon and biocompatible polymers. Due to the
opportunity to interact with biology at both the
nano and microscale, these types of hierarchical
structures could be used for a variety of
applications in tissue engineering and regenerative
medicine. Surface topographies with hierarchical
features expanding from the nano to the
macroscale offer the possibility to synergistically
improve the bioactivity of materials and control
biological processes.
María Jesús López-Bosquea,
Marina Cazorlaa, Judith
Linaceroa, Esther Tejeda-
Montesa, Yolanda Atienza
a,
Anna Lladob, Julien
Colombellib, Elizabeth
Engelc, Alvaro Mata
a
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Figure 1. Representative fluorescence images of cells on (a) micro- (b) perpendicular (c) parallel and (d) nano-channels.
(e-f) SEM and (g) fluorescence images (red=vinculin, green=actin cytoskeleton) of cells growing on perpendicular
channels. Direction of nanochannels is schematically shown by white lines (b-d, g).
Figure 2. (a) Quantification of cell alignment revealing that cells are aligned preferentially along the micro-, nano- and
parallel channels. However, cells sense the competitive effect of the micro- and nano- scale topographies, interacting
with both micro- and nano-channels when perpendicular to each other. (b) Quantification of cell elongation revealing
that cells sense the synergistic effect of the micro- and nano-topographies on parallel channels. The cells are
significantly more elongated on parallel channels compared to the micro- and nano-channels individually.
References
[1] M.J. Dalby, N. Gadegaard, R. Tare, A. Andar, M.O. Riehle, P. Herzyk, C. D. W. Wilkinson, R. O. C. Oreffo,
Nature Materials 6 (2007) 997–1003
[2] R. J. McMurray, N. Gadegaard, P. M. Tsimbouri, K. V. Burgess, L. E. McNamara, R.Tare, K. Murawski,
E.Kingham, R. O. C. Oreffo, M. J. Dalby, Nature Materials 10 (2011) 637–644
[3] A. Mata, L. Hsu, R. Capito, C. Aparicio, K. Henrikson, S. I. Stupp, Soft Matter 5(6) (2009) 1228–1236
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 117
Refractive index sensing based on
plasmonic fano-like interference
Instituto de Estructura de la Materia (IEM-CSIC)
Serrano 121
E-28006 Madrid, Spain
As Unlike those propagating at metal/dielectric
interfaces, localized collective oscillations of charges
confined to the surface of metal nanoparticles can
be directly excited by external illumination without
the need of any additional coupling-in technique,
provided that particles are much smaller than the
incident wavelength. These oscillations, which can
be pictured as a “wave” of electrons moving across
the surface of the particle, are referred to as
localized surface plasmon resonances (LSPRs) and
they are responsible of nanoparticles' bright colors
when in colloidal suspension, as a result of their
intense absorbing and scattering of light in the
visible range.
One of the most appealing properties of LSPRs is
that their resonant frequency strongly depends on
nanoparticles's size, shape and composition, as well
as on the refractive index of the surrounding
medium. Given that present technological advances
allows one to control particle geometry down to
nanometer scale, spectral shift of LSPRs can then be
used to detect extremely small changes of the
immediate dielectric environment. For instance,
such as those produced by the binding of some
biological molecules with a higher refractive index
than that of their aqueous solvent.
When assessing the actual performance of a
refractive index sensing scheme based on the
spectral shift of a given plasmon resonance, we have
to first consider its refractive index sensitivity, which
is defined as the linear regression slope within a
given range for the position of the resonance (either
a peak or a dip) as a function of refractive index. This
magnitude is usually expressed in terms of
wavelength or energy shifts per refractive index unit
and it provides a preliminary measure of the sensor
quality. However, sensitivity alone cannot
characterize the sensor performance but in an ideal
scenario of infinitely high spectral resolution and no
system noise. Sherry et al. [1] therefore proposed
the so-called figure of merit (FoM), which is defined
as the plasmon resonance sensitivity divided by its
“Full Width at Half Maximum” (FWHM), as the most
meaningful indicator for evaluating the performance
of LSPR-based sensors. Such dimensionless quantity
allows one to directly compare the sensing
properties of different systems irrespective of their
shape, size and operating wavelength.
According to its very definition, the optimal FoM
would then be obtained from those resonances
exhibiting both high sensitivity to environment and
narrow FWHM, which are precisely the main
features of spectral line profiles arising from Fano
interference [2]. Such an interaction of discrete- and
continuum-like states (often labeled as “dark” and
“bright” modes) has already been employed for
refractive index sensing by means of either
propagating or localized plasmon resonances. In this
work [3], we propose that the Fano-like interference
of longitudinal plasmon resonances occurring at a
single nanorod [4] can be employed for refractive
index sensing in two different configurations that are
reasonably attainable. We also discuss their
expected performance in terms of their FoMs, which
are calculated under realistic conditions by means of
the separation of variables (SVM) and the finite
element (FEM) methods [5, 6].
References
[1] L. J. Sherry et al., Nano Lett., 5 (2005) 2034.
[2] B. Luk’yanchuk et al., Nat. Mater., 9 (2010) 707.
[3] F. López-Tejeira, R. Paniagua-Domínguez and J.
A. Sánchez-Gil, submitted.
[4] F. López-Tejeira et al., New J. Phys., 14 (2012)
023035.
[5] N. V. Voshchinnikov and V.G. Farafonov,
Astrophys. Space Sci., 204 (1993) 19.
[6] COMSOL Multiphysics version 4.2.
F. López-Tejeira,
R. Paniagua-Domínguez and
J. A. Sánchez-Gil
118 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
New intermediate band sulphide
nanoparticles acting in the full
visible light range spectra as an
active photocatalyst 1 Instituto de Catálisis y Petroleoquímica, CSIC, Marie Curie 2, 28049 Madrid, Spain.
2 Instituto de Energía Solar, Universidad Politécnica de Madrid,
Ciudad Universitaria s/n, 28040 Madrid, Spain.
Nowadays one of the challenges of materials
science is to find new technologies that will be able
to make the most of renewable energies. An
example of new proposals in this field are the
intermediate-band (IB) materials, which promise
higher efficiencies in photovoltaic applications
(through the intermediate band solar cells), or in
heterogeneous photocatalysis (using nanoparticles
of them, for the light-induced degradation of
pollutants or for the efficient photoevolution of
hydrogen from water).
Figure 1. IB working principle: (a) photons of different
energies excite electrons from the VB directly to the CB
and also from the VB to the IB and from the IB to the CB.
(b) A wider photon energy range is thus used.
Figure 2. Density of states (computed with DFT) of In2S3
with octahedral In partially substituted by V.
An IB material consists in a semiconductor in which
gap a new level is introduced [1], the intermediate
band (IB), which should be partially filled by
electrons and completely separated of the valence
band (VB) and of the conduction band (CB). This
scheme (figure 1) allows an electron from the VB to
be promoted to the IB, and from the latter to the
CB, upon absorption of photons with energy below
the band gap Eg, so that energy can be absorbed in
a wider range of the solar spectrum and a higher
current can be obtained without sacrificing the
photovoltage (or the chemical driving force)
corresponding to the full bandgap Eg, thus
increasing the overall efficiency.
This concept, applied to photocatalysis, would
allow using photons of a wider visible range while
keeping the same redox capacity. It is important to
note that this concept differs from the classic
photocatalyst doping principle, which essentially
tries just to decrease the bandgap. This new type of
materials would keep the full bandgap potential but
would use also lower energy photons.
In our group several IB materials have been
proposed, mainly for the photovoltaic application,
based on extensively doping known
semiconductors with transition metals [2],
examining with DFT calculations their electronic
structures. Here we refer to In2S3 and SnS2, which
contain octahedral cations; when doped with Ti or
V an IB is formed according to quantum
calculations (see e.g. figure 2).
We have used a solvotermal synthesis method to
prepare in nanocrystalline form the In2S3 thiospinel
and the layered compound SnS2 (which when
undoped have bandgaps of 2.0 and 2.2 eV
Raquel Lucena1, José Carlos
Conesa1, Fernando Fresno
1,
Perla Wahnón2, Pablo
Palacios2 and Yohanna
Seminovski2
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respectively) where the cation is substituted by
vanadium at a ≈10% level. This substitution has
been studied, characterizing the materials by
different physical and chemical techniques (TXRF,
XRD, HR-TEM/EDS) (see e.g. figure 3) and verifying
with UV spectrometry that this substitution
introduces in the spectrum the sub-bandgap
features predicted by the calculations (figure 4).
Figure 3. a) XRD diagram of SnS2 and V:SnS2 synthesized
materials, indicating the nanocrystal size deduced from
linewidths. b) V:In2S3 HR-TEM image of In2S3 with EDS
measurement of the composition at the In2S3
nanocrystals.
Figure 4. Experimental diffuse reflectance spectrum of
pure and V-doped nanocrystalline In2S3.
For both sulphide type nanoparticles (doped and
undoped) the photocatalytic activity was studied by
following at room temperature the oxidation of
formic acid in aqueous suspension, a simple
reaction which is easily monitored by UV-Vis
spectroscopy. The spectral response of the process
is measured using a collection of band pass filters
that allow only some wavelengths into the reaction
system. Thanks to this method the spectral range in
which the materials are active in the
photodecomposition (which coincides with the
band gap for the undoped samples) can be
checked, proving that for the vanadium substituted
samples this range is increased, making possible to
cover all the visible light range. Furthermore it is
checked that these new materials are more
photocorrosion resistant than the toxic CdS witch is
a well know compound frequently used in tests of
visible light photocatalysis.
Figure 5. Rate constant k measured for aqueous HCOOH
photooxidation under light of different wavelengths on
In2S3 with and without ≈10% V doping, compared with
the respective DR Vis-NIR spectra.
These materials are thus promising not only for
degradation of pollutants (or for photovoltaic cells)
but also for efficient photoevolution of hydrogen
from water; work in this direction is now being
pursued.
References
[1] A. Luque, A. Martí, Phys. Rev. Lett. 78, 1977,
5014.
[2] a) P.Palacios et al. Phys. Rev. B 73 (2006)
085206; ibid. J. Chem. Phys. 124 (2006)
014711.
b) P. Palacios et al. Thin Solid Films 515 (2007)
6280; ibid. J. Phys. Chem. C 112 (2008) 9525.
c) P. Palacios et al. Phys. Rev. Lett. 101 (2008)
046403.
[3] a) R. Lucena et al. Chem. Maters. 20 (2008) 5125.
b) P. Wahnón et al. Phys. Chem. Chem. Phys.13
(2011) 20401.
0 10 20 30 40 50 60 70 80 90 100
V:SnS2 30nm
SnS2 23nm
2 θθθθ / º
a)
0.5 1.0 1.5 2.0 2.5 3.0 3.5
0
2
4
6
8
10
12
k/s
(K
M function)
E (eV)
V:In2S
3
In2S
3
Kubelka-Munk transform:KM=(1-R)2/2R
0.5 1.0 1.5 2.0 2.5 3.0 3.5
0
2
4
6
8
10
12
k/s
(K
M function)
E (eV)
V:In2S
3
In2S
3
Kubelka-Munk transform:KM=(1-R)2/2R
400 500 600 700 800 9000.000
0.002
0.004
0.006
0.008
0.010
0.012
0.014
0.016
0.018
0.020
0.0
0.5
1.0
1.5
2.0
2.5
3.0
3.5
K / M
in-1
λλλλ / nm
Absorption
spectra of In2S3
Absorption
spectra of In1,8V0,2S3
In2S
3
In1,8
V0,2
S3
absorp
tion (αα αα)
120 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Quantum dot intermediate band
solar cells:
issues for an attractive concept
Instituto de Energía Solar, Universidad Politécnica de Madrid, Spain
The Intermediate Band Solar Cell [1] is formed by
sandwiching and Intermediate Band (IB) material
between two ordinary semiconductors p- and n-
doped. The IB material has an energy band or set of
levels (the IB) situated within the bandgap of a
semiconductor. In this way, besides the
photocurrent generation by photons with enough
energy as to pump electrons form the valence band
(VB) to the conduction band (CB) a second path of
current appears with two photons of less energy
that completes the pumping using the IB as
stepping stone. The concept is very attractive
because this cell is potentially able to increase the
photocurrent without decreasing the photovoltage.
In this way the detailed balance [1] top efficiency is
63% to compare to the 41% of a single bandgap
solar cell.
IBSCs can be made with alloys presenting an IB [2]
and with IB materials containing Quantum Dot (QD)
arrays [3, 4]. In the first case we have to deal with
relatively exotic materials in which the device
technology is incipient and therefore the cell
efficiency measured so far is very small. In the
second case, which is the one to present in this talk
the device technology is rather developed. Most of
the work so far has been done with Stranski-
Krastanov InAs QDs in GaAs, grown by MBE [4].
IBSCs of 18% efficiency [5] have been presented,
reasonable but below the expectations.
The reason for this is that the voltage is usually
strongly reduced and the current is increased only
slightly. In IBSC the voltage is believed to be
controlled [6, 7], like in most devices, by SRH
recombination through the ordinary impurities of
the solar cell (not the IB levels) but the presence of
the IB increases the minority carriers and the cell
behaves as with a reduced bandgap. More
perfection in the material quality may prevent this
reduction and this has actually been attained [8] in
InAs/GaAs QD IBSCs made by MOCVD.
The reduced current is an intrinsic property of the
QDs. VB→IB absorption requires that the initial and
final eigenfunctions have strong projection in both
the CB and the VB [7, 9]; unfortunately the IB
eigenfunctions are almost fully projected on the CB
and all the VB eigenfunctions have no or negligible
projection on the CB. Controlling the shape and
density of the QDs might be a way to overcoming
this issue.
In summary, the IBSC has become a hot subject in
photovoltaics. The concept is very attractive but
bringing it into practice will still require efforts.
Antonio Luque
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References
[1] A. Luque, A. Martí, Physical Review Letters 1997, 78, 5014.
[2] N. Lopez, L. A. Reichertz, K. M. Yu, K. Campman, W. Walukiewic, Physical Review Letters 2011, 106,
028701.
[3] A. Martí, L. Cuadra, A. Luque, in Proc. 28th IEEE Photovoltaics Specialists Conference, IEEE, New York
2000, 940.
[4] A. Luque, A. Martí, C. Stanley, N. López, L. Cuadra, D. Zhou, A. Mc-Kee, Journal of Applied Physics 2004,
96, 903.
[5] S. A. Blokhin, A. V. Sakharov, A. M. Nadtochy, A. S. Pauysov, M. V. Maximov, N. N. Ledentsov, A. R.
Kovsh, S. S. Mikhrin, V. M. Lantratov, S. A. Mintairov, N. A. Kaluzhniy, M. Z. Shvarts, Semiconductors
2009, 43, 514.
[6] A. Luque, P. G. Linares, E. Antolín, I. Ramiro, C. D. Farmer, E. Hernández, I. Tobías, C. R. Stanley, A. Martí,
Journal of Applied Physics 2012, 111, 044502.
[7] A. Luque, A. Marti, C. Stanley, Nature Photonics 2012, 6, 142.
[8] C. G. Bailey, D. V. Forbes, S. J. Polly, Z. S. B. IEEE, Y. Dai, Chelsea Mackos, R. P. Raffaelle, S. M. Hubbard,
IEEE Journal on Photovoltaics 2012, DOI 10.1109/JPHOTOV.2012.2189047.
[9] A. Luque, A. Mellor, E. Antolin, P. G. Linares, I. Ramiro, I. Tobias, A. Marti, Solar Energy Materials and
Solar Cells 2012, 103, 171.
122 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Silica nanostructures toxicity
assessment and their potential for
biomedical applications
Italian Institute of Technology
Center for Bio-Molecular Nanotechnologies@Unile
Via Barsanti, 73010 Arnesano, Lecce, Italy
Silica nanoparticles are widely used in various
industrial fields and recently, they have been
exploited also for biomedical research. The impact
of SiO2NPs on human health and the environment
is thus of great interest. Nowadays, the overall
evaluation of the toxicity/biocompatibility of
SiO2NPs is extremely difficult, owing to
controversial results in the literature and to the lack
of standard procedures and/or insufficient
characterization of the nanomaterials in biological
systems. Therefore the biocompatibility needs to
be documented in greater detail. In this study we
evaluated the toxicity of different silica
nanostructures, both pure and quantum dots
(QDs)- or iron oxide-doped, and studied their
potential applications in gene delivery. We
performed a systematic in vitro study to assess the
biological impact of pure SiO2NPs, by investigating 3
different sizes (Fig.1) and 2 surface charges in 5 cell
lines. We analyzed the cellular uptake and
distribution of the NPs along with their possible
effects on cell viability, membrane integrity and
generation of reactive oxygen species (ROS). We
observed that all the investigated SiO2NPs do not
induce detectable cytotoxic effects (up to 2.5 nM
concentration) in all cell lines (Fig.2a). Once having
assessed the biocompatibility of SiO2NPs we
evaluated their potential in gene delivery, showing
their ability to bind, transport and release DNA,
allowing the silencing of a specific protein
expression (Fig.2b) [1]. The biocompatibility of
SiO2NPs and their gene carrier performance were
also evaluated and confirmed in primary neuronal
cells [2]. Finally, we investigated the toxicity of
silica nanoparticles doped with iron oxide
nanocrystals. We tested nanoparticles with two
surface charges in two cell lines by evaluating their
effect on cell viability, cell membrane integrity and
induction of ROS. We found that SiO2NPs doped with
iron oxide nanoparticles do not induce detectable
cytotoxic effects up to 1 nM concentration (Fig.3b)
with negatively charged NPs exerting the higher
toxicity. This is likely associated to the nanoparticles
degradation in lysosomal environment.
Overall, we demonstrate that SiO2 nanostructures
are quite safe in vitro and have promising potential
in biomedical applications.
References
[1] M.A. Malvindi et al., Nanoscale, 2012, 4; 4(2),
486-495.
[2] G. Bardi et al., Biomaterials, 2010, 31, 6555-
6566.
Maria Ada Malvindi,
Virgilio Brunetti,
Giuseppe Vecchio,
Antonio Galeone,
Valeria De Matteis,
Roberto Cingolani and
Pier Paolo Pompa
Figure 1.
Representative
TEM images of
three sizes of
SiO2NPs: 25, 60 and
115 nm.
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a) b)
Figure 2. a) Viability of A549 cells 48 and 96 h after the exposure to increasing doses evaluated of 25 nm SiO2NPs by the
WST-8 assay; b) In vitro silencing of tGFP expression.
Figure 3. a) SiO2NPs doped with iron oxide NPs; b) Viability of A549 cells 48 and 96 h after the exposure to increasing
doses of SiO2NP doped with iron oxide NPs evaluated by the WST-8 assay; c) Iron release in lysosomal environment.
124 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Plasmonic nanoparticle chain in a
light field: a resonant optical sail 1Departamento de Física de la Materia Condensada and Instituto “Nicolás Cabrera”,
Universidad Autónoma de Madrid, 28049 Madrid, Spain. 2Departamento de Física de Materiales and Instituto “Nicolás Cabrera”, Universidad
Autónoma de Madrid, 28049 Madrid, Spain.
Metallic Optical trapping and driving of small
objects has become a topic of increasing interest in
multidisciplinary sciences. We propose [1] to use a
chain made of metallic nanoparticles as a resonant
light sail, attached by one end point to a
transparent object and propelling it by the use of
electromagnetic radiation. Driving forces exerted
on the chain are theoretically studied as a function
of radiation’s wavelength and chain’s alignments
with respect to the direction of radiation.
Interestingly, there is a window in the frequency
spectrum in which null torque equilibrium
configuration, with minimum geometric cross
section, corresponds to a maximum in the driving
force.
References
[1] S. Albaladejo, J. J. Sáenz and M. I. Marqués,
Nanoletters 11, 4597 (2011)
Silvia Albaladejo1,
Juan José Sáenz1 and
Manuel I. Marqués2
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 125
Imaging the carrier confinement
within a single nanowire
1European Synchrotron Radiation Facility, 38043-Grenoble, France
2IMM, Instituto de Microelectrónica de Madrid (CNM, CSIC), 28760-Tres Cantos, Spain
3Department of Applied Physics, Valencia University, 46100-Burjasot, Spain
4Institute for Electronics, Microelectronics, and Nanotechnology, CNRS-UMR 8520,
Department ISEN, F-59652 Villeneuve d’Ascq, France 5National CRI Center for Semiconductor Nanorods, Department of Physics and
Astronomy, Seoul National University, Seoul 151747, Republic of Korea
The assembly of group-III nitride nanowires into optoelectronics offers a promising approach to improve the
performance of light-emitting devices. Two dimensional quantum confinement effects, created by coaxial
band structure engineering, lead large spectral tunability and high luminescence quantum yields.
Sophisticated core/multishell nanowires have already been designed to produce a large variety of size-
dependent phenomena for advanced light-emitting diodes. Although theory suggests that the carrier
distributions in nanowires exhibit two dimensional confinement under a cross-section of hexagonal
geometry, its direct observation has never been addressed. By combining synchrotron excited optical
luminescence with simultaneous energy-disperse X-ray spectroscopy using a nanometre-sized hard X-ray
beam, here we show experimental evidence for these carrier localization effects. Applied to single coaxial n-
GaN/InGaN multiquantum-well/p-GaN nanowires, our hyperspectral imaging method reveals a stronger
transition at the hexagon corners, matching theoretical predictions. Based on core-level excitation
processes, our experiment opens new avenues for further local structure, and time-resolved studies with
both nanometre resolution and optical sensitivity. We anticipate that this methodology will contribute to a
greater understanding of the underlying design concepts of photonic nanodevices.
Gema Martínez-Criado1 ,
A. Homs1, B. Alén
2,
J. A. Sans3, J. Segura-Ruiz
1,
A. Molina-Sánchez4,
J. Susini1, J. Yoo
5 and
G.-C. Yi5
126 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Reciprocal space and transmission
electron microscopy study of
heterogeneous GaP: MnP magnetic
epilayers containing MnP
nanoclusters Regroupement québécois sur les matériaux de pointe (RQMP) and Département de génie physique, École Polytechnique de Montréal P.O. Box 6079, Station Centre-Ville, Montréal, Québec H3C 3A7, Canada Work done in collaboration with: C. Lavoie, IBM T.J. Watson Research Center, Yorktown Heights, NY 10598, USA; C. Lacroix and D. Ménard, Département de génie physique, École Polytechnique de Montréal; M. Garcia-Hernandez, and A. de Andres, Instituto de Ciencia de Materiales de Madrid, CSIC, Cantoblanco, 28049 Madrid, Spain.
The integration of magnetic nanoclusters in thin III-V semiconductor films can enhance magneto-resistance and magneto-optic effects with the potential to be integrated in novel devices for room temperature applications [1-3]. The magnetic properties of heterogeneous films strongly depend on the structural properties of the clusters and film matrix, which are in turn determined by the growth conditions. We show how a three dimensional mapping of reciprocal space by X-ray diffraction combined with transmission electron microscopy measurements can determine the texture of GaP epilayers containing embedded MnxP nanoclusters grown on GaP substrates by metal organic vapor phase epitaxy [4-5]. This systematic approach allows identification of all phases present in the heterogeneous films, in particular showing traces of hexagonal Mn2P precipitates, whose formation can be avoided by lowering the film growth temperature. Growth at 650 oC produces mostly orthorhombic MnP nanoclusters, responsible for the magnetic properties, which are oriented along specific GaP crystallographic directions, forming six well defined families. The population of these families can be quantified and is influenced by the growth temperature and the film thickness. The MnP clusters principally grow on GaP(001) and GaP{111} facets with a small fraction of clusters nucleating on higher-index GaP{hhl} facets. Most epitaxial alignments share a similar component: the
MnP(001) plane (c-axis plane) is parallel to the GaP{110} plane family. Axiotaxial ordering between the MnP clusters and the GaP matrix has also been observed [5].
Figure 1. The TEM image on the left shows a plan view of a heterogeneous GaP:MnP epilayer containing MnP nanoclusters grown at a substrate temperature of 650
oC
[ref. 4]. The heterogeneous films are grown on semi-insulating GaP(001) substrates in a low-pressure cold-wall MOVPE reactor, using trimethylgallium, tertiary-butylphosphine, and methyl cyclopentadienyl manganese tricarbonyl as precursors for Ga, P and Mn respectively, and Pd-purified hydrogen as the carrier gas. The reactor pressure was set at 40 Torr with a total flow rate maintained at 4000 sccm. Growth rate is 1.2 μm/ h for GaP(001) at a growth temperature of 650 oC C
S. Lambert-Milot, S. Gaudet, P. Desjardins, and R.A.
Masut
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Acknowledgements The authors acknowledge J. Bouchard for technical support, J.-P. Massé for assistance with TEM measurements, and J. Jordan-Sweet and E. Dimasi for technical assistance at the NSLS X20 and X6B beamlines. This research was supported by the Natural Sciences and Engineering Research Council of Canada (NSERC), the Canada Research Chair Program, and the Fonds Québécois de la Recherche sur la Nature et les Technologies (FQRNT). The research was carried in part at the NSLS, Brookhaven National Laboratory, supported by the U.S. D.O.E., Division of Materials Sciences and Division of Chemical Sciences, under Contract No. DE-AC02-98CH10886.
References
[1] G. Monette, C. Lacroix, S. Lambert-Milot, V. Boucher, D. Ménard and S. Francoeur, J. Appl. Phys. 107 (2010) 09A949.
[2] C. Lacroix, S. Lambert-Milot, P. Desjardins, R.A. Masut and D. Ménard J. Appl. Phys. 103 (2008) 07D531.
[3] C. Lacroix, S. Lambert-Milot, P. Desjardins, R.A. Masut and D. Ménard, J. Appl. Phys. 105 (2009) 07C119.
[4] S. Lambert-Milot, C. Lacroix, D. Ménard, R. A. Masut, P. Desjardins, M. Garcia-Hernandez and A. de Andres, J. Appl. Phys. 104 (2008) 083501.
[5] S. Lambert-Milot, S. Gaudet, C. Lacroix, D. Ménard, R.A. Masut, P. Desjardins, and C. Lavoie, J.Vac. Sci. & Tech., submitted.
Figure 2. Reciprocal space measurements: were carried out at the National Synchrotron Light Source (NSLS) (Brookhaven National Laboratory) X20A and X6B beam lines. The figure below illustrates the large photon flux provided by the synchrotron source, a key feature to obtain a full 3D reciprocal space map which will allow texture determination.
Figure 3. Texture and phase quantification: is obtained from X-ray diffraction (a set of more than 600 pole figures, as the example illustrated below) combined with transmission electron microscopy (TEM) analysis
128 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Spatial and temporal control of
osteoblastic cells proliferation on
electroconductive carbon
nanotube-based bone grafts 1 CICECO, Dept. of Materials and Ceramic Eng., Univ. of Aveiro, 3810-193 Aveiro, Portugal
2 I3N, Physics Dept., Univ. of Aveiro, 3810-193 Aveiro, Portugal
3 CEMUC, Dept. of Metallurgical and Materials Eng., Univ. of Porto,
4200-465 Porto, Portugal 4 Faculty of Dental Medicine, Univ. of Porto, 4200-393 Porto, Portugal
Biomaterials can still be reinvented to become
simple and universal bone regeneration solutions.
Following this roadmap, "smart" bone grafts have
been designed with new functionalities able to
stimulate specific bone cells responses. Regarding
the beneficial effects of endogenous electrical
signals in natural bone, electron conductivity
emerge as an exciting functionality. As opposed to
natural piezoelectric bone, electroconductive bone
grafts have key advantages: external control over
the level and duration of stimulation; confinement
of exogenous electrical fields on their surface
leading to spatial and temporal control of bone
tissue regeneration. Following this, the present
work aims to: (1) process MWCNTs-based bone
grafts; (2) assess the α-MEM-conductive bone
grafts interactions under (or not) electrical fields;
(3) evaluate in vitro the efficiency of conductive
bone grafts in delivering electrical stimulus to
osteoblastic cells.
Biologically safer carbon nanotubes (CNT) [1-3]
presenting outstanding characteristics - non-
metallic phases, bioactive, high aspect-ratio and
ultimate electrical conductivity - were used here as
fillers to obtain highly conductive biomaterials.
Calcium phosphate (CaP)/CNT powders show high
interaction being the CNTs decorated with CaP
particles (Fig. 1a). Microstructures of fracture (Fig.
1b) and polished surfaces (Fig. 1c) show that CNT
are well dispersed combining individual CNT (Fig.
1d) and controlled sized agglomerates (<10 Dm)
(Fig. 1c). This CNT 3D network gives an electrical
percolation threshold (Pc) in the range of 0.9-1.8
vol.% (Fig. 1e). Pursuing the main goal of this work,
the selection of the CNT loading should be: low to
preserve the biological profile of the matrix; high to
give composites with higher conductivity than the
biological milieus. The 2.5 wt.% loading is the one
that matches this two requisites (Figs. 1e,f).
Figure 1. Microstructure and electrical conductivity of
CNT-based composites.
In an in vivo scenario, it is expected that this
composite formulation induces the locally increase
of the conductivity and confines the exogenous
electrical fields on its surface. To evaluate this, two
set of experiments were performed in α-MEM
(12 ml). The presence of six CaP samples show an
increase of 0.15 % of the impedance of the medium
(Figs. 2a,c). Conversely, six CaP/CNT (2.5 wt.%)
samples decrease the impedance in 1.26 % (Figs.
2b,c). Scanning vibrating electrode (SVET)
measurements were accomplished under a
constant electrical field Exx of 3 mV.cm-1
/100 DA,
accordingly to the configuration of Fig. 2d. At the
D. Mata1, M. Amaral
1,2,
A.C. Bastos1, M.A. Neto
1,
F.J. Oliveira1, M.A. Lopes
3,
M.H. Fernandes4 and
R.F. Silva1
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borders, it can be seen that the conductive sample
induces less distortion of the E lines than the
dielectric one (Figs. 2e,f). Also, the Eyy component,
perpendicular to the sample surface, is maximized
for the conductive sample (Figs. 2 g-j).
The current-voltage response of ion channels in
osteoblastic cells is shown in Fig. 3a. An action
potential of +10 mV for 5 ms is enough to induce a
maximum peak of current in the cell. This is
followed by a depolarization to the resting state
during 20 ms (red line in Fig. 3a). This biological
data was used as reference to select the AC
electrical signal parameters for the stimulation
experiments (Fig. 3b). In vitro stimulation of MG63
osteoblastic cells was accomplished in a home-
made apparatus (Fig. 3c, current circuit highlighted
by blue arrows) using 12 ml of α-MEM solution and
six samples per culture plate (same conditions seen
in Fig. 2). The frequency was kept constant at 40Hz
and the electrical field (5.6 and 15.3 mV.cm-
1)/current density (91 and 167 DA.cm
-2)/current
(100 DA and 200 DA) and time (15 and 30 min)
were varied. Potential and density current
distributions of the stimulation area of the culture
plate (Figs. 3c,d) are presented for the 200 DA
stimulus condition in Figs. 3e,f. It can be seen that
the samples (black dotted line in Figs. 3e,f) were
uniformly stimulated. MTT assay in Fig. 4g shows
that electroconductive CaP/CNTs templates under
electrical stimulus accelerate the proliferation of
osteoblastic cells. For all the stimulation conditions
the cell population is higher than the control
(nonstimulated material) (Fig. 3g). Conversely, for
the dielectric materials the stimulus delivering is
less efficient, showing responses equal or lower
than the control (Figs. 3h,i). Interestingly, these
observations corroborate the results of Fig. 2. SEM
and CLSM microscopy images (Figs. 3j,k) show no
evident differences in cells morphology between
the two conditions and for the three materials.
In conclusion, osteoblastic cells were efficiently
stimulated on CNT-based bone grafts. MTT assays
showed almost 300% increase in cell proliferation,
relatively to the non-stimulated condition, after
only 3 days of daily stimulation time of 15 min.
These exciting observations are intimately related
with the locally increase of the conductivity and the
confinement of electrical fields on the surface of
the conductive material.
References
[1] Mata D, Ferro M, Fernandes AJS, Amaral M,
Oliveira FJ, Costa PMFJ, Silva RF. Carbon 48
(2010) 2839-54.
[2] Mata D, Amaral M, Fernandes AJS, Oliveira FJ,
Costa PMFJ, Silva RF. Carbon 49 (2011) 2181-
96.
[3] Mata D, Silva RM, Fernandes AJS, Oliveira FJ,
Costa PMFJ, Silva RF. Carbon 50 (2012) 3585-
06.
Figure 2. α-MEM-
MWCNTs-based bone
grafts interactions under
(or not) electrical fields.
Figure 3. In vitro
evaluation of the
efficiency of CNT-based
bone grafts in delivering
electrical stimulus to
osteoblastic cells.
130 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Recent advances in fast imaging
Raman technology for nano
materials characterisation
Renishaw Ibérica S.A.U,
Gavà Park, C. Imaginació, 3, 08850 Gavà,
Barcelona, Spain
Raman spectroscopy continues to provide
analytical solutions in a variety of material science
applications offering chemical specificity on a
micrometer scale.
The ability to create chemical and stress images by
acquiring Raman spectra from an array of positions
and then processing them to reveal the parameter
of interest is a powerful technique. Traditionally,
these spatially-related data have been collected by
raster scanning the sample beneath the incident
laser spot, typically in micrometer intervals. New
approaches to Raman imaging have been
developed that enhance the capabilities of modern
Raman instruments that now have the ability to
produce images on the nano scale.
The use of either high precision motorised stages or
piezoelectric-controlled sample stages permits
accurate and repeatable sample movements in
intervals significantly smaller than the diffraction
limited laser spot size. When used in conjunction
with an atomic force microscope tip, feedback can
be applied to ensure the sample’s surface remains
in the plane of the laser focus, optimising
efficiency. Topographic images of the surface can
be correlated with Raman images as the data are
acquired simultaneously. This approach is proving
to be most useful in materials research and the
study of semiconductor materials, particularly in
assessing carbon nanotube structures, graphene
film properties and in stress in silicon devices.
Other application areas include biological
intracellular structure and tissue imaging.
Additionally, a new method of acquiring both 2D
and 3D confocal Raman images has been developed
– ‘Streamline’. Spectra are collected in parallel,
rather than in series using the traditional methods.
Shorter total acquisition times result, with high
quality individual spectra recorded in the order of
fifty milliseconds. The method also benefits from
‘on the fly’ data analysis resulting in real time
image creation. This innovative approach allows the
technique to succeed where others have failed:
producing uncompromised data and images for
small or large areas at speeds much greater than
possible with competing methods. A number of
materials examples will be shown to illustrate the
benefits of this method and will demonstrate how
information can be achieved on the nanometre
scale.
Sébastien Maussang
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 131
Unusual nucleic acid structures for
DNA-based nanotechnologies
Univ. Bordeaux, IECB, INSERM U869, France
Nucleic acids are prone to structural polymorphism:
in addition to the classical DNA double-helix, a
number of alternative structures may be formed.
Important biological processes require melting of
the DNA double-helix and several genetic diseases
are mediated by the formation of non B-DNA
structures. Among these, G-quadruplexes (G4)
represent an exceptional polymorphic class of
higher-order nucleic acid structures in which the
structural unit is formed by a planar arrangement
of four Hoogsteen-bonded guanines known as
Gquartets (Fig.1). A vertical π-stacking arrangement
of several G-quartets and the presence of
monovalent cations provide these structures with
remarkable stabilities.
Nucleic acids are gaining in popularity and utility for
creating new nanomaterials due to their ability to
self-assemble. Pairing of double-stranded DNA is
being explored by a growing number of researchers
to construct extremely sophisticated
nanostructures and nanodevices. We believe that
G4 offer interesting possibilities for
nanotechnology and biotechnology and we are
currently seeking new properties for DNA-based
logic gates and nanomaterials.
Figure 1. Presentation of a G-quartet with four coplanar
guanines
This work is supported by INSERM, Fondation pour
la Recherche Médicale (FRM), University of
Bordeaux, Agence Nationale de la Recherche (ANR
grants F-DNA, G4-Toolbox & QuantADN), and
Région Aquitaine grants. I thank all members of
ARNA laboratory as well as L. Yatsunyk
(Swarthmore College), P. Alberti (MNHN, Paris) D.
Monchaud (Dijon) M.P. Teulade-Fichou (Curie,
Orsay) R. Eritja (Barcelona), A. Galeone (Naples)
and L. Lacroix (Toulouse) for helpful discussions.
Jean-Louis Mergny
132 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Evidence for magnetic order in a
purely organic 2D layer adsorbed on
epitaxial graphene 1 Dep. Física de la Materia Condensada, Universidad Autónoma de Madrid,
Cantoblanco 28049, Madrid, Spain 2 Instituto Madrileño de Estudios Avanzados en Nanociencia (IMDEA-Nanociencia),
Cantoblanco 28049, Madrid, Spain
Collective magnetic properties are usually
associated to d or f electrons which carry the
individual magnetic moments. Band magnetism in
organic materials based on π electrons has
remained an experimental challenge, in spite of
rigorous predictions of a fully spin polarized ground
state in half-filled flat band organic systems [1].
Figure 1. Above: STM image of TCNQ/graphene/Ru(0001)
at 4.6 K; Belowleft: spin polarized PDOS on different
molecules and right: local spin polarized tunnelling
spectroscopy on the two molecular domains.
Cryogenic Scanning Tunneling Microscopy (STM)
and Spectroscopy in UHV and accurate Density
Functional Theory (DFT) simulations show [2] that
isolated TCNQ molecules deposited on a monolayer
of graphene epitaxially grown on Ru(0001) acquire
charge from the substrate and develop a sizeable
magnetic moment, which is revealed by a
prominent Kondo resonance. The magnetic
moment is preserved upon dimer and monolayer
formation.
The self-assembled 2D monolayer of magnetic
molecules develops spatially extended spin-split
electronic bands visualized in the real space by
STM, where only the majority band is filled, thus
becoming a 2D, purely-organic magnet whose
predicted spin alignment in the ground state is
visualized by spin-polarized STM at 4.6 K.
References
[1] Y. Nagaoka, “Ferromagnetism in a narrow,
half-filled band”, Phys. Rev. 147, 392 (1966).
[2] Manuela Garnica, Daniele Stradi, Sara Barja,
Cristina Díaz, Fabian Calleja, Manuel Alcamí,
Nazario Martín, Amadeo L. Vázquez de Parga,
Fernando Martín, and Rodolfo Miranda (to be
published).
Rodolfo Miranda1,2
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 133
Dirac fermions in HgTe
quantum wells
Physics Institute, EP3, Wuerzburg University,
Am Hubland, 97074 Wuerzburg, Germany
HgTe quantum wells have a linear band dispersion at low energies and thus mimic the Dirac Hamiltonian.
Changing the well width tunes the band gap (i.e., the Dirac mass) from positive, through zero, to negative.
Wells with a negative Dirac mass are 2-dimensional topological insulators and exhibit the quantum spin Hall
effect, where a pair of spin polarized helical edge channels develops when the bulk of the material is
insulating.
Our transport data provide very direct evidence for the existence of this third quantum Hall effect.
Wells with a thickness of 6.3 nm are zero gap Dirac systems, similar to grapheme. However, zero gap HgTe
wells possess only a single Dirac valley, which avoids inter-valley scattering.
L. W. Molenkamp
laurens.molenkamp@
physik.uni-wuerzburg.de
134 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Three dimensional electrodes base
on core/shell nanowires for
photoelectrochemical cells
Departament Electronica, Universitat de Barcelona,
Barcelona, 08028, Spain
Catalonia Institute for Energy Research, IREC,
Sant Adria del Besos, 08930, Spain.
Three dimensional array’s offer an increased active
surface area for all type of electrodes, in general,
and, in particularly, for higher efficiency in photo
electrochemistry devices. In this scenario, core-
shell nano hetero or homo structures are the
essential brick for built-in these electrodes and they
become essential to define advanced photo
electrochemistry elements or, even, for a more
complex and promising artificial photosynthesis
systems that require frontal or back illumination
according to the photo reactor design related to
the production of sun fuels.
However, all their outstanding properties depend
on the adequate capability for photon capture and
the consequent control of the charge separation.
Under these conditions, doping of the inner part of
the structure becomes basic for the charge
extraction associated with a high transport facility,
low internal resistance, as well as the surface
conditions are determining for the charge transfer
of the other type of carriers. As a consequence,
doping management becomes an essential point
for energy band engineering and, so, a fundamental
key for controlling the overall nanostructure
performances.
In this contribution, we report on the growth on
electrodes of nanowires with controlled doping and
how they can be coated for selected shell material
with controlled thickness for having homo and
hetero structures with modified surface properties
and varied electrical field values at the surface. It
contributes to enhance the charge carrier transfer
as well as it presents also excellent transport
properties. As demonstration, examples of
vertically aligned homostructures ZnO:ZnO and
heterostructures ZnO/ZnS or ZnO/TiO2,… among
others core /shell nanowires will be presented like
for discussing the functional matching in these
coaxial heterojunction including electrical, optical
crystallographic and thermo chemical
performances related to their degradation and
stability.
In general, these core/shell nanowires have been
grown by a facile and low cost electrodeposition
two-step process. In this way, due to the controlled
surface electrical field, photoelectrochemical
properties of these nanowires have been found to
be highly enhanced with the presence of these shell
layers and an experimental study as function of
their thicknesses will be presented and modelized
to explain the promotion the surface-related
radiative recombination processes. The
enhancement factor is proved to depend on the
shell thickness. These performances are associated
with the improvement of the photogenerated
charge carrier separation and surface to neutral
inner part transfer capability achieved when
increasing the space charge area within the
nanowires with a built-in electric field introduced
by the doping profile. These features allow the
deduction of practical rules for the design and
optimization of these three dimensional
photoelectrodes for the production of sun fuels.
Jiandong Fan, C. Fábrega,
T. Andreu, Andreu Cabot
and Joan Ramon Morante
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Metal-Carbon Nanohybrid Foams:
from Laser Chemistry to
Nanochemistry 1 Instituto de Carboquímica ICB-CSIC, Miguel Luesma Castán 4, 50018 Zaragoza, Spain
2 Instituto de Síntesis Química y Catálisis Homogénea, Universidad de Zaragoza-CSIC,
Zaragoza, Spain 3 Instituto de Ciencia de Materiales de Aragón, Universidad de Zaragoza-CSIC, Zaragoza,
Spain 4 Departamento de Química Física, Universidad de Zaragoza, 50009 Zaragoza, Spain
Metal-carbon nanohybrid foams have been
produced by laser irradiation of organometallic
precursors [1]. The laser irradiation of aromatic
organometallic precursors resulted in milligram
quantities of soot exhibiting a fibrous appearance.
Scanning electron microscopy (SEM)
characterization showed that the microstructure of
this material exhibited the porous, foam-like
texture which results from the aggregation of
‘‘necklace’’-like ensembles of nanobeads, similar to
that observed in other ‘‘spongy’’ carbon materials,
such as carbon aerogels [2,3] and carbon nanofoam
[4]. Transmission electron microscopy (TEM)
studies reveals that these metal-carbon
nanohybrids are multi-component materials that
consist of metal nanoparticles embedded in
amorphous carbon aggregates, amorphous carbon
nanoparticles, and graphitic nanostructures, which
can be eventually observed as independent,
separate components in the produced soots (Fig. 1)
[5].
The present work also reports on important
experimental parameters toward the controlled
synthesis of these carbon foams. Thus,
characterization studies indicate that the
composition, metal nanoparticle dilution and
crystallite size, and structure of the metal-carbon
foams can be tailored by suitably tuning the laser
parameters used and by choosing the metals and
ligands of the irradiated targets [5,6]. It is also
demonstrated here that, contrary to carbon
aerogels, the employed metals are not required for
the growth of the observed graphitic
nanostructures [2,3,5] .
Figure 1. SEM-(left, scale bar: 100 nm) and TEM (right,
scale bar: 10 nm) micrographs of laser-ablation
produced Au-carbon foams [1].
This “laser chemistry”, based on the use of
molecular precursors, would enable the facile
production of multifunctional nanostructured
carbon materials with a range of tunable
properties. Alternatively to this “laser chemistry”
approach, wet chemistry strategies have been
designed for the synthesis of metal-carbon
nanohybrids based on the in-situ reduction of
noble-metal salts in presence of carbon foams
produced by laser ablation of metal-free organic
compounds. Further physical-chemical
characterization studies, chemical processing, and
potential technological applications of these metal-
carbon nanohybrid foams will be also discussed [6].
Andrés Seral-Ascaso1,
Asunción Luquin2, María
Luisa Sanjuán3, Rosa
Garriga4, Mariano Laguna
2,
Germán F. de la Fuente3,
and Edgar Muñoz1
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References
[1] E. Muñoz, M. de Val, M. L. Ruiz-González, C. López-Gascón, M. L. Sanjuán, M. T. Martínez, J. M.
González-Calbet, G. F. de la Fuente, M. Laguna, Chem. Phys. Letters 420 (2006) 86.
[2] R.W. Fu, G. Dresselhaus, M.S. Dresselhaus et al., Langmuir 21 (2005) 2647.
[3] F.J. Maldonado-Hódar, C. Moreno-Castilla et al., Langmuir 16 (2000) 4367.
[4] A.V. Rode et al., Appl. Phys. A 69 (1999) S755.
[5] E. Muñoz, M. L. Ruiz-González, A. Seral-Ascaso, M. L. Sanjuán, J. M. González-Calbet, M. Laguna, G. F.
de la Fuente Carbon 48 (2010) 1807.
[6] A. Seral-Ascaso et al., submitted.
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Understanding Electronic Structure
and Charge Transport in
Single-Molecule Junctions
Molecular Foundry
Lawrence Berkeley National Laboratory, USA
Interfaces are pervasive in nanostructured
materials, and the details of their atomic-scale
morphology, electronic structure, and environment
dictate the flow of matter, charge, and energy,
ultimately determining function. Single-molecule
junctions represent the molecular limit of a hybrid
interface, and recent transport measurements of
well-defined junctions have provided new
opportunities to quantitatively understand how
interfacial composition and structure is connected
to conductance, thermopower, current-voltage (IV)
characteristics, and rectifying behavior. In this talk,
I will summarize predictive fundamental studies [1-
4], using density functional theory and many-body
perturbation theory, of the electronic structure and
transport properties of single-molecule junctions.
Advantages and limitations of our approaches will
be discussed in the context of recent calculations
and experiments.
References
[1] H. J. Choi et al, Phys. Rev. B 76, 155420 (2007)
[2] S. Y. Quek et al, Nano. Lett. 9, 3949 (2009)
[3] J. B. Neaton et al, Phys. Rev. Lett. 97, 216405
(2006); M. DellAngela et al, Nano Lett. 10,
2470 (2010); I. Tamblyn et al, Phys. Rev. B 84,
201402 (2011); S. Sharifzadeh et al,
arXiv:1204.0509
[4] S. Y. Quek et al, ACS Nano 5, 551 (2011); V.
Fatemi et al, Nano Lett 11, 1988 (2011); J.
Widawsky et al, Nano Lett. 12, 354 (2012); P.
Darancet et al, in preparation (2012)
Jeffrey B. Neaton
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Measurement of the capacitance
across a tunnel barrier 1 LT-NanoLab, Department of Applied Physics, University of Alicante, Alicante, Spain
2 Institut für experimentalphysik, Freie Universität Berlin, Berlin, Germany
Electronic transport in the process of the formation
of nanocontacts between two metallic electrodes
can be measured by bringing together two metallic
wires made of the same material using different
techniques such the Scanning Tunneling
Microscope (STM) [1]. Most of the experiments
have been focused to measure the conductance of
the junctions, however until now very little
attention has been paid to other electronic
characteristics of this system such as the
capacitance[2].
Here we report the measurement of the whole
impedance characteristics of a controlled vacuum
gap in between two metallic electrodes using a
homemade STM. High vacuum and cryogenic
conditions are necessary to achieve the desired low
mechanic (below 10pm) and thermal noise.
Electronics is carefully implemented taking care to
reach low electronic noise too. In order to measure
the impedance of the atomic junctions, a lock-in
amplifier technique has been used.
In our experiments we have observed a decrease of
capacitance when the tunnel current is increasing,
as predicted by theory[2-4]. On an other hand, we
also observe such a decrease in the field emission
regime when increasing the applied bias voltage in
between electrodes (shown at the figure), and
when each field emission resonance state
(Gundlach oscillations) takes place. This effect has
also been independently observed by the
measurement of the forces at the junction by the
Tuning Fork technique.
Figure 1. Au>Au measurements taken at 4.2K and
cryogenic vacuum using STM where distance between
tip and sample is held constant.
References
[1] N. Agraït, A. Levy-Yeyati, J.M. Van Ruitenbeek.
Phys. Rep. 377, 81 (2003).
[2] J. G. Hou et al., Phys. Rev. Lett. 86, 5321
(2001).
[3] M. Büttiker, J.Phys.:Condens. Matter 5, 9361
(1993).
[4] J. Wang et al. , Phys. Rev. Lett. 80, 4277 (1998).
Bernat Olivera1,
Giovanni Sáenz-Arce1,
Martina Corso2,
Carlos Sabater1,
Juan Ignacio Pascual2 and
Carlos Untiedt1
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Protein-polymer nanoreactors and
processors act as artificial organelles
Department of Chemistry,
University of Basel,
Klingelbergstrasse 80, Basel 4056, Switzerland
The combination of biological molecules and
synthetic polymer carriers/templates represents a
very promising approach for development of
efficacious therapies with minimum side effects,
diagnostic methods featuring significantly higher
sensitivity and selectivity, and personalized
diagnostics and therapeutics via theragnostic
approaches. In this respect, suitable amphiphilic
block copolymers self-assemble into in aqueous
media into vesicles with membranes mimicking
biological membranes. The properties of such
vesicles can be extensively controlled via chemical
composition, molecular weight and the hydrophilic-
to-hydrophobic block length ratio of the polymers,
and have the advantage of superior stability and
robustness. The combination with suitable
biological molecules (proteins, enzymes, DNA,
peptides) introduces other well-defined functions,
such as molecular recognition, cooperation, and
catalytic activity.
We exploited the concept of bio-synthetic
combination to develop antioxidant nanoreactors
that encapsulated superoxide dismutase/mimics in
the aqueous cavities of vesicles generated by the
self-assembly of poly(2-methyloxazoline)-b-
poly(dimethylsiloxane)-poly(2-methyloxazoline),
PMOXA-PDMS-PMOXA copolymers [1,2]. By
synthesizing appropriately functionalized polymers
(e.g. biotin, antibody) we successfully immobilized
the nanoreactors on solid support to follow the
folding/unfolding of single proteins, and to monitor
enzymatic reactions down to the scale of a few
molecules [3]. A step further in obtaining
multifunctionaliy, is to co-encapsulate enzymes that
act in tandem inside the polymer cavity: cascade
reactions can therefore take place in situ [4].
Here we present antioxidant processors designed
by simultaneous co-encapsulation of enzymes and
channel proteins (Figure 1) [5]. Cascade reaction of
co-encapsulated superoxide dismutase and
lactoperoxidase allowed for a complete
detoxification of superoxide radicals and related
H2O2. The polymer membrane was selectively
controlled by insertion of channel proteins, which
allowed the exchange of substrates and products
with the environment, supporting the in situ
activity of the enzymes. In addition, the detection
of superoxide radicals and related H2O2 was based
on a fluorescent product of the second enzyme that
strongly favored a dual application of the
processor: in biosensing and detoxification of
reactive oxygen species. By changing the
enzyme/combination of enzymes either to
hemoglobin, or to superoxide dismutase - catalase,
we enlarged the detoxification approach to other
free radicals species, such as nitrogen reactive
species, or combination of oxygen and nitrogen
reactive species.
Figure 1. Schematic representation of an antioxidant
processor based on the co-encapsulation of a
combination of enzymes inside polymer nanovesicles.
Cornelia G. Palivan
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Inside cells nanoreactors and processors preserved their integrity over more than 48hours, and did not
present toxicity in that interval. After cellular uptake, the nanoreactors/processors retained their function
over extended periods of time, thus acting as artificial organelles that continuously exchange molecular
information with the host cell. This opens new avenues in protein therapy as well as intracellular sensing
approaches.
References
[1] F. Axthelm, O. Casse, W. Koppenol, T. Nauser, W. Meier, C. Palivan, J. Phys. Chem. B, 112(28), (2008),
8211.
[2] O. Onaca, D.W. Hughes, V. Balasubramanian, M. Grzelakowski, W. Meier, C. G. Palivan, Macromol.
Biosci, 10(5), (2010), 531.
[3] S. Egli, M. G. Nussbaumer, V. Balasubramanian, M. Chami, N. Bruns, C. G. Palivan, W. Meier,
J.Am.Chem.Soc., 133 (12), (2011), 4476.
[4] a. D. M. Vriezema, J. Hoogboom, K. Velonia, K. Takazawa, P. C. M. Christianen, J. C.Maan, A. E.
Rowan and R. J. M. Nolte, Angewandte Chemie, 115, (2003), 796. b. S. F. M. van Dongen, M. Nallani,
J. L. L. M. Cornelissen, R. J. M. Nolte and J. C. M. van Hest, Chem.Eur. J., 15, (2009), 1107.
[5] P. Tanner, O. Onaca, V. Balasubramanian, W. Meier, C. G. Palivan. Chem. Eur. J, 17, (2011), 4552.
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Plasmonic nanoparticles for the
protection of the final optics in
inertial confinement fusion facilities:
capabilities and limitations
Instituto de Fusión Nuclear, Universidad Politécnica de Madrid,
C/ José Gutiérrez Abascal 2, E-28006 Madrid, Spain
HiPER (High Power Laser Energy Research Facility)
is an ESFRI project of the EU for the production of
energy using laser-driven Inertial Confinement
Fusion (ICF). In this kind of facilities the final optics
assemblies are the last element of the main laser
system and the first one of the target area systems.
The materials of this system are subject to bursts of
direct targets of more than 100 MJ injected at 10-
20 Hz. Currently there are no materials capable of
withstanding these conditions for a reasonable
camera size (R ∼ 5 m). The use of a certain
concentration of gas (typically a few μg/cm3 Xe) or
deflecting incident ions by means of electric fields
are some of the solutions that have been proposed
to mitigate this effect. However, the optimal
solution is the development of new materials able
to protect the lenses and maintain its transparency
in these aggressive conditions. Plasmonic
nanostructures embedded in thin films look like an
ideal candidate for this task because they are able
to stop an important part of the radiation and,
simultaneously, they offer unprecedented abilities
to manipulate electromagnetic waves. For instance,
simple spherical silver nanoparticles present a quite
low optical density at 350 nm (i.e., the wavelength
of HiPER’s lasers). Another possibility worth
exploring is the usage of plasmonic Fano
resonances to produce a high transparency in some
selected spectral regions. Finally, another attractive
feature of plasmonic nanostructures is that they
can potentially behave as self-healing materials
because the mean free path of the vacancies is
greater than the material grains, which leads to
effective annihilation of vacancies at grain
boundaries.
Ovidio Y. Peña Rodríguez
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Functionalizated magnetic
nanoparticles for biodetection,
imaging and separation of Mytilus galloprovincialis larvae using NIT-zipper
® technology.
*University of Vigo, Spain Novel nanomaterials are envisaged to have a major impact on a number of relevant areas. It is anticipated that within the next few years the application of nanomaterials and nanotechnology-based manufacturing will have a crucial role in biomedical, pharmaceutical, cosmetic, veterinary, environmental and agro-food technologies. In this work, several sizes of high-quality monodisperse Fe3O4 Nanoparticles (NPs) were synthesized and functionalizated (or bioconjugated)using NIT-zipper® disruptive technology, following the manufacturer's instructions (Nanoimmunotech), with monoclonal antibodies (mAbs) directed against mussel (Mytilus galloprovincialis) larvae, such as M22.8 and M36.5 (Pérez et al., 2009), and with different labels (fluorescent dyes), that may allow an easier and more specific identification. Functionalizated Nps were incubated with mussel larvae and magnetic separation was perform. The
larvae collected in the magnet were analyzed by fluorescent and optical microscopy (pictures: A; 20X mussel larvae with Texas Red dye, B; magnetic nanoparticles aggregates inside mussel larvae, and C; 20X mussel larvae with FITC dye) and flow citometry. The obtained results clearly indicate that our successful nanosystem recognise the mussel larvae in field plankton samples from different geographical regions, but not the larvae of any other bivalve species. Thus, it could be used for routine monitoring and purification of mussel larvae in plankton samples from different sources, offering an innovative solution to agro-food markets that could give rise to new processes and solve current problems, like the lack of suitable methods for an unequivocal recognition and a rapid sorting of the bivalve larvae species in plankton samples, in these industries.
Daniel Pérez-Estévez*, Christian Sánchez-Espinel, Gonçalo Doria, Sara Puertas, Silvia Lorenzo-Abalde, África González-Fernández, Rubén Santos.
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Urchin-inspired zinc oxide as
building blocks for nanostructured
solar cells 1 Laboratory for Mechanics of Materials and Nanostructures, EMPA Materials Science &
Technology, Feuerwerkstrasse 39, 3602 Thun, Switzerland 2 Institut Européen des Membranes (UMR CNRS 5635), Université Montpellier 2, Place
Eugène Bataillon, 34095 Montpellier, France. 3 Electron Microscopy Center, EMPA Materials Science & Technology, Ueberlandstrasse
129, 8600 Duebendorf, Switzerland 4 Laboratory for Thin Films and Photovoltaics, EMPA, Materials Science & Technology,
Ueberlandstr. 129, CHD-8600 Dübendorf, Switzerland
According to recent studies on the global power plant
market, the installed capacity of solar power grew
faster than that of any other power technology. Last
generation nanostructured photovoltaic devices
include dye sensitized (photoelectrochemical, quasi-
solid, and solidstate) solar-cells and their hybrid and
fully inorganic variants as extremely thin absorber
(ETA) solar-cells. They appear to have a big light
harvesting potential compared to planar thin film
photovoltaic devices due to their “built-in” large
surface area architecture involving an n-type
semiconductor material covered by a light absorber
(dye, organic or inorganic films) for collecting
photons. After charge separation, electrons are
collected by a photoanode for electricity generation.
TiO2 and ZnO were agreed to be the most promising
materials as wide band gap n-type semiconductors
with a preference for ZnO due to its better electronic
transport properties and its comparatively easy
controllable growth as single-crystal nanowire arrays
Better control of light-scattering and electronic
transport through this n-type semiconductor is
essential for improving the solar efficiency.Among
numerous studied architectures, nanoparticles and
nanowires are the most employed building-blocks
because they either provide high surface areas
(nanoparticles) or direct electron transport
(nanowires). In direct comparison, single-crystal
nanowire arrays offer shorter electron collection
paths, thus avoiding charge recombination; but solar
cells based on nanoparticles still have a higher solar
efficiency due to their larger surface area. Hence,
increasing the surface area of planar nanowire
carpets by increasing the diameter and length of the
individual nanowire has been proposed in many
research reports to enhance the solar light harvesting.
As a commonly acquired result, such an increase of
the surface area in nanowire carpets leads to an
augmentation of charge recombination being
detrimental for solar cell efficiency. Therefore, future
nanostructured solar-cell architectures need to
improve multiple light-scattering while keeping
reasonable surface areas with a short electron
collection path; in other words, improving the solar
light absorption and reducing the electron-hole
recombination. To tackle this challenge we have
recently developed urchin-like nanostructures by
electrodeposition of ZnO nanowires onto surface
activated polymer spheres. This structure showed a
twofold improvement of light scattering compared to
nanowire arrays. However, these nanostructures had
a limited mechanical stability and their interspacing
could not be varied which prohibited further
optimized use in applications. In the present paper,
we report on a novel architecture – based on a self-
stabilized hollow urchin-like ZnO nanowire building-
blocks using a novel low-costand scalable synthesis
route which allows for controlled building-block
interspace and tunable nanowire dimensions. We
show that the light diffusion and absorption as well as
solar cell efficiency can be elegantly controlled and
enhanced by engineering the dimensions of such
building-blocks.
References
[1] J. Elias, C. Levy-Clement, M. Bechelany, J.
Michler, G. Y. Wang, Z. Wang, L. Philippe Adv.
Mater. 2010, 22, 1607.
Laetitia Philippe1,
Jamil Elias1, Mikhael
Bechelany2, Ivo Utke
1,
Rolf Erni3, Davood Hosseini
4
and Johann Michler1
laetitia [email protected]
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Figure 1. Schematic view of synthesis route for (I) self-stabilized hollow urchin-like ZnO nanowire building blocks and (II)
successive fabrication steps for the ETA solar-cell: a) Dip coating for the deposition of an ordered monolayer of
polystyrene microspheres onto an FTO covered glass substrate; b) Size reduction of spheres using plasma etching with
oxygen plasma; c) Deposition of a uniform conformal thin layer of about 20 nm of ZnO by ALD; d) Electrodeposition of
n-type ZnO NWs with controlled length and diameter; e) Formation of hollow u-ZnO by dissolving the polystyrene
spheres in toluene; f) Coating of NWs with an absorber film of CdSe by electrodeposition; g) Covering with p-type
CuSCN by chemical impregnation, and h) Deposition of a gold thin film electrode by physical vapor deposition.
Figure 2. SEM images of ZnO urchin-like structures after dissolution of the polystyrene sphere monolayers a) without PE
and b) with 20 min PE treatment. The insets of a) and b) are the SEM images of the ordered PS before electrodepostion
coated with 20 nm of ZnO by ALD. c) Side view of individual u-ZnO structures. Note: the planar NW-carpet between the
u-ZnO. d) and e) are views of individual hollow u-ZnO structures from a scratched part of the sample where the
structures were reversed upside down. All the scale bars in the figure (except (e)) are 2 μm.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 145
Improving the Direct Electron
Transfer Efficiency in Laccase
Electrodes for Biofuel Cell Cathodic
Reactions 1 Instituto de Catalisis y Petroleoquimica, Consejo Superior de Investigaciones Cientificas.
C/Marie Curie 2 L10, 28049 Madrid, Spain 2 Biomedical Laboratory Science and Technology, Faculty of Health and Society,
Malmö University SE-205 06 Malmö, Sweden
Fungal laccases are one of the best candidates for
enzymatic biofuel cell cathodes due to its ability to
reduce O2 directly to H2O at high potentials;
laccases are also suitable for direct electron
transfer when appropriately wired toward different
electroactive surfaces such as gold or graphite.
However, laccase faces several hindering conditions
when taking to many in vivo-like environments,
being the most relevant chloride inhibition and the
functional pH. Chloride anions are a reversible
inhibitor of laccase and are present in most
biological fluids. Additionally, the typically acidic
pH-optima for laccase performance take any
laccase-modified electrode out of range for many
natural fluids.
This presentation will show strategies to improve
laccase performance under these nonfavoured
environments. It has been shown that specific
orientation of laccase for DET can reduce this
inhibition source when immobilized on a low-
density graphite (LDG) electrode [1] and how to
extend this immobilization method to gold planar
electrodes [2]. We will show the improvement
brought to current density and chloride resistance
by combining a LDG electrode with gold
nanoparticles. The limitations brought by the use of
neutral pH can be addressed by generation of a
local acidic pH environment. This has been
achieved by inserting the laccase electrode in a
magnetic ring that allows the deposition of
magnetic nanoparticles carrying another enzyme
able to acidify the environment [3]. For conceptual
purposes we have used glucose oxidase (GOx) to
produce a gluconic-acid environment, managing to
lower pH 2 units while keeping the bulk pH neutral
and therefore allowing laccase to work. Catalase
was present for oxygen-regeneration purposes.
References
[1] Cristina Vaz-Dominguez, Susana Campuzano,
Olaf Rüdiger, Marcos Pita, Marina Gorbacheva,
Sergey Shleev, Victor M. Fernandez, Antonio L.
De Lacey. Biosensors and Bioelectronics, 24,
(2008), 531–537.
[2] Marcos Pita, Cristina Gutierrez-Sanchez, David
Olea, Marisela Velez, Cristina Garcia-Diego,
Sergey Shleev, Victor M. Fernandez, Antonio L.
De Lacey. Journal of Physical Chemistry C, 27,
(2011), 13420-13428.
[3] Sylvain Clot, Cristina Gutierrez-Sanchez, Sergey
Shleev, Antonio L. De Lacey, Marcos Pita.
Electrochemistry Communications, 18, (2012),
37-40.
Marcos Pita1,
Cristina Gutierrez-Sanchez1,
Sergey Shleev2 and
Antonio L. De Lacey1
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Strategies and activities in nano Photonics Unit - Instituto Tecnológico la Marañosa, Ctra M301 Km 10.500, 28330 San Martín de la Vega, Spain In recent years, emerging technologies are becoming of great interest due to the possibility of developing applications which can improve the features of the existing ones, and even, there is the possibility of developing novel applications that cannot be achieved without these. Usually, there are two different ways of developing applications: a bottom-up approach, starting from the development of science and technology to assess its properties and create an application from them. A top-down approach, on the other hands, starts with a real problem that needs a specific application, and then seeks for the most optimal technology that can create an application to solve that problem. With this end-user point of view, Ministry of Defense has defined several sectors of interest [1], in which different kind of technologies can provide the means to develop the required applications, and among them, nanotechnology, and more specifically photonics and new emerging fields like metamaterials and plasmonics are expected to play an important role. Applications related to light guiding, multispectral sensing, lensing, and reduction of scattered light can be achieved using metamaterials. These are artificial materials [2] whose optical properties are solely determined by the fabricated microstructure, making it possible to the control the dielectric permittivity (ε) and magnetic permeability (μ) to achieve unsual properties such as negative refraction at certain wavelengths. Combined with Transformation Optics [3], these new materials allow an accurate control of the flow of light. This
unique properties of metamaterials make them also attractive to be used in security features like of bank notes, passports or ID cards. Fast and accurate detection of biological or chemical agents is a topic of great interest in the field of security. IR spectroscopy is one of the most promising technologies for this application, since it allows the detection of IR signatures to be compared with databases to identify the threat. Also, the interaction of agents with sensing surfaces can change the optical properties, making it suitable for the use of plasmons in this kind of detection.
References
[1] Ministerio de Defensa. Estrategia de Tecnología e Innovación para la Defensa – ETID (2010)
[2] V.G. Veselago, The electrodynamics of substances with simultaneously negative values of ε and μ. Soviet Physics Uspekhi (1968) Vol 10 N4, 509
[3] D. Schurig, J.J. Mock, B.J. Justice, S.A. Cummer, J.B. Pendry, A.F. Starr, D.R. Smith, Metamaterial Electromagnetic Cloak at Microwave Frequencies. Science(2006) 977
J. Plaza, R. Almazán, L. Gómez, D. Fernández, M.T. Rodrigo, M.C. Torquemada, V. Villamayor, I. Catalán, C. Sierra, I Génova, F. Rangel, A. Vicioso, C. Gutiérrez, M. Álvarez and M. Magaz
148 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
High Precision local electrical
Probing: A New Low Temperature
4-Tip STM with Gemini UHV-SEM
Navigation
Instituto Omicron NanoTechnology GmbH,
Limburger Str. 75, 65232 Taunusstein, Germany
Developments in commercial surface science
instrumentation regularly follow the major trends
in science. The variety of instrumental approaches
is as wide-ranged as science itself. Therefore, the
identification of relevant analysis techniques and
their advancement towards ease-of-use and a
routinely accessible performance level represent a
major challenge for enterprises. Beside OMICRON´s
major activities in conventional SPM, electron
spectroscopy and thin film techniques, the class of
“multitechnique” instruments represents another
important R&D line that is in the focus of this
presentation.
One prominent example in nanotechnology is the
development of individual nano-scale devices. A
tremendous variety of approaches exist and
fundamental questions arise. Comprehensive
concepts towards electrically integrated and
therefore functional devices are however rare.
Individual (metallic) nano-scale contacts represent
one of the main challenges. High precision local
electrical probing has the potential to increase
efficiency in evaluating different approaches.
The OMICRON UHV NANOPROBE already meets the
involved requirements: (1) Rapid and simultaneous
SEM navigation of four local STM probes; (2)
Localization of nanostructures by sub-4nm UHV
Gemini SEM resolution; (3) Individual probe fine
positioning by atomic scale STM imaging; (4) STM
based probe approach for “soft-landing” of sharp
and fragile probes and controlled electrical contact;
(5) suitable low noise signal re-routing for transport
measurements; (6) chemical/magnetic analysis by
complementary analysis techniques such as SAM,
SEMPA, CL and others.
And although the UHV NANOPROBE represents a
flexible solution, especially in combination with
complementary techniques, it´s concept is
fundamentally limited in terms of lowest
temperature and SPM resolution. Together with
the Forschungszentrum Jülich, we thus have been
developing a completely new design, the Low
Temperature UHV NANOPROBE. It represents the
evolution from a high performance probing system
towards 4 simultaneously operating and high
performing low temperature SPMs, navigated by
SEM. The major R&D targets have been (1)
equilibrium temperature of sample and probes at
temperatures T<5K; (2) simultaneous SEM for
probe navigation close to base temperatures; and
(3) high STM performance of all four probes, truly
suitable for manipulation and spectroscopy. First
evaluation measurements will be presented: STM
on Au(111) with pm stability, STS revealing the
supeconducting gab of a Nb tip with approx. 3meV
gap size, and first transport measurement at T<5K.
Figure 1. Left: Image of the LT NANOPROBE stage. Right:
STM on Au(111) at a temperature of below 5 K. The
atomic structure and the herringbone reconstruction are
clearly visible.
A. Bettac, B. Guenther,
J. Koeble, M. Maier and
A. Feltz
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S-layer proteins as patterning
elements in the life and
non-life sciences
Department of Nanobiotechnology,
University of Natural Resources and Life Sciences,
Vienna, Austria
Crystalline S(urface)-layers are the most commonly
observed cell surface structures in prokaryotic
organisms (bacteria and archaea) [1]. S-layers are
highly porous protein meshworks with unit cell
sizes in the range of 3 to 30 nm, and thicknesses of
∼10 nm. S-layers exhibit either oblique (p1, p2),
square (p4) or hexagonal (p3, p6) lattice symmetry.
One of the key features of S-layer proteins is their
intrinsic capability to form self-assembled
monolayers in solution, at solid supports such as
silicon or gold, at the air-water interface, at planar
lipid films and at liposomes and nanocapsules.
Basic research on S layer proteins enabled us to
make use of the unique self-assembly properties of
native and, in particular, genetically functionalized
S-layer fusion protein lattices as matrices for the
binding of molecules and the templated synthesis
of nanomaterials [2]. S-layer proteins were already
used as scaffolds for making hybrid organic-
inorganic nanostructures such as highly ordered
nanoparticle arrays or silicified nanoporous
biomembranes. In another approach the genetic
engineering of fluorescent S-layer proteins allowed
to develop novel pH indicators as used in drug-
targeting and delivery systems. Further on,
advances in elucidating the atomistic structure of S-
layer proteins and simulating the self-assembly
process opened the door to the design of new bio-
functional materials for a diverse range of
applications.
The overall goal of our research is dedicated
towards the development of an S-layer-based
biomolecular construction kit. This presentation
summarizes the key properties of S-layer proteins,
with a focus on the self-assembly process, and
describes different applications in the life and non-
life sciences.
Figure 1. Confocal micrographs showing the pH
dependence of four different fluorescent S-layer fusion
proteins.
Acknowledgements: Part of this work was funded
by the Air Force Office of Scientific Research
(AFOSR) Agreement Awards FA9550-09-0342 and
FA9550-10-0223, the Austrian Nano-Initiative
(Project Slaysens), and the Erwin Schödinger Society
for Nanobiosciences, Vienna, Austria.
References
[1] Sleytr, U.B., Schuster, B., Egelseer, E.M., Pum,
D., Horejs, C.M., Tscheliessnig, R., Ilk, N., In
Progress in Molecular Biology and
Translational Science, Horworka, S. (Ed.),
Academic Press, Burlington, MA (USA), Vol.
103 (2011) 277.
[2] Pum, D., Sleytr, U.B., In Nanobioelectronics –
for electronics, biology, and medicine,
Offenhäuser, A., Rinaldi, R. (Eds.), Springer,
New York, NY (USA), (2009) 167.
Dietmar Pum and
Uwe B. Sleytr
150 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Near field X-ray
spectromicroscopies:
new tools for nanoscience
Institute of Solid State Physics,
8 Kengaraga Riga, Latvia
In the last years, the X-ray absorption (XAS)
techniques have undergo remarkable development:
(i) experiments with unprecedented femtometer
accuracy, under extreme conditions of high
pressure and temperature [1], (ii) experiments with
nanoscale lateral resolution [2]. Nevertheless,
investigations of complex nanostructured materials
used in modern technologies require special X-ray
experimental techniques able to imaging
simultaneously topography and chemical mapping
(X-ray analysis of matter) on the nanometer scale.
Near Field (NF) X-ray Spectromicroscopy (FF
illumination and NF detection) is a fully new
approach for the detailed investigation of
nanostructures down to the nanometer level. The
extremely high lateral resolution of Local Probe
Microscopies (LPM, AFM,STM) makes them among
the most largely used in nanoscience. However,
these tools suffer of a lack in chemical sensitivity.
On the other hand, far field X-ray spectroscopy
probes the chemical and structural properties of
materials. A combination of X-ray spectroscopies
and LPM is the ideal answer to many problems in
nanosciences. This report highlights the most
important contributions which were held in the
combination of X-ray spectroscopies and LPM
techniques.
The basics of such approach are circulating since
years. The first observations of core-level
photoelectrons generated by X-ray irradiation of the
tip-surface region of STM have been published by
Tsuji [4]. Ishii [5] has measured the capacitance XAS
signal with a metal tiny electrode. The combination
of XAS and scanning near-field optical microscopy
(SNOM) as a local detector was proposed by Purans
[6], while a combination of XRF technique and LPM
with a cantilever, having a hole of 100 nm, as a
collimator of X-ray beam was proposed by Nagamura
[7]. First STM and SNOM experiments under focused
synchrotron-radiation (SR) were performed at ESRF
on the microbeam line ID-3 [8]. Detailed STM study
using soft SR X-rays was performed by Matsushima et
al. [9]. A STM dedicated to in situ experiments under
the irradiation of highly brilliant hard-X-rays of
synchrotron radiation has been developed by Saito et
al. [10] and a current modification was detected at
the absorption edge with a spatial resolution of the
order of 10 nm. Finally, Ishii and Hamilton et al. [11]
has combined electrostatic force microscopy (EFM)
with tunable synchrotron x-ray source excitation.
Further progress we have achieved in the framework
of the European X-TIP project by the focusing SR
beam to increase the density of the incident
photons. X-ray optics at third generation
Synchrotron Radiation facilities have lead to the
stable production of X-ray microbeams with
extremely high photon densities making this
approach feasible. We have started with three types
of experiments: (i) XAS-AFM: X-ray excited
secondary electrons detection by conductive tip in
AFM mode; (ii) XAS-SNOM: X-ray excited optical
luminescence (XEOL) detection by SNOM in AFM
mode; (iii) XAS-SCM/AFM: X-ray excited capacitance
or/and photoconductivity of sample detection by
conductive tip in SCM, KFM or AFM mode.
The new instrumentation developed within this
project offers the possibility to carry out a selective
structural analysis of the sample surface with the
subwavelength spatial resolution determined by
the SNOM probe aperture. In addition, the apex of
the optical fibre plays the role of a topographic
probe, and chemical and topographic mappings can
be simultaneously recorded.
Juris Purans
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References
[1] J. Purans et al., Phys. Rev. Lett. 100 (2008) 055901 ; R.F. Pettifer et al., Nature 435 (2005) 78.
[2] W. Chao et al., Nature 435 (2005) 1210; DT. Attwood, Nature 442 (2006) 642.
[3] S. Larcheri and J. Purans, Rev. Sci. Instrum. 79 (2008) 013702.
[4] K.Tsuji et al., Surf. and Interface Anal. 27 (1999) 132.
[5] M.Ishii, Physica B. 308-310 (2001) 1153 ; M. Ishii et al., Appl. Phys. Lett. 90 (2007) 063101.
[6] J.Purans, Proc. TXRF2003 Sat. meeting on micro X-ray beam analysis, 13.09.2003, Osaka, Japan.
[7] T. Nagamura, Proceedings TXRF2003 Sat. meeting on micro X-ray beam analysis, 13.09.2003, Osaka,
Japan.
[8] F.Comin, D. Pailharey, R. Felici, J. Chevrier, J.Purans, ESRF user report on the project SI-956, 2004,
Grenoble.
[9] T.Matsushima et al., , Rev. Sci. Instr. 75 (2004) 2149.
[10] A. Saito et al., J. Synchrotron Rad. 13 (2006) 216.
[11] M. Ishii et al., Appl. Phys. Lett. 90 (2007) 063101.
152 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Unveiling the Landau levels structure
of graphene nanoribbons 1 Laboratoire National des Champs Magnétiques Intenses, INSA UPS CNRS,
UPR 3228, Université de Toulouse, 143 av. de Rangueil, 31400 Toulouse, France 2 IMEP-LAHC, Grenoble-INP, Minatec 3 Parvis Louis Néel, BP 257 38016 Grenoble, France
3 CIN2 (ICN-CSIC) and Universitat Autonoma de Barcelona, Catalan Institute of
Nanotechnology, Campus de la UAB, 08193 Bellaterra (Barcelona), Spain 4 ICREA, Institucio Catalana de Recerca i Estudis Avançats, 08010 Barcelona, Spain
In the present work we show the first experimental
evidence of Hall quantization in graphene
nanoribbons along with the impact of the 1-D
confinement of Dirac fermions.
Carbon-based nanoelectronics is, in the actuality,
one of the most promising subjects of
nanotechnology. The challenging task for
technologists is the achievement of clean devices
with an engineered energy gap. The lateral
confinement in graphene nanoribbons leads to a
series of 1-D electronic sub-bands with a
confinement gap. In presence of a large enough
magnetic field, the band structure evolves to
magneto-electric sub-bands and graphene-like
Landau levels are expected to develop. The
presence of these Landau levels makes itself
evident with the appearance of ShubnikovdeHaas
(SdH) oscillations and conductance quantization
plateaus.
Up to now, Hall quantization in graphene
nanoribbons (GNRs) remains puzzling since no
experimental evidence has been found for widths
smaller than 200 nm [1-4]. The absence of Hall
quantization in GNRs has been attributed to
disorder, which is suspected to crosslink the chiral
edge currents and impede the conductance
quantization.
Lithographically patterned GNRs of 100 and 70 nm
widths are made using oxygen plasma etching and
a PMMA etching mask. These GNR present a high
conductance, a high field effect mobility and a
weakly diffusive transport regime with presence of
Fabry-Perot oscillations at low temperature.
Magneto-resistance (MR) measurements show the
first experimental evidence of Hall quantization in
GNRs (Fig. 1) for filling factors ʋ= 2 and 6. On the
other hand, anomalies in the magneto-transport
measurements are evidenced:
(i) At high electrostatic doping level SdH
oscillations show a clear departure from the
regular linear behaviour of the Landau index as
a function of 1/B (Fig. 1(a) inset). This is a
direct signature of the electronic confinement
that starts to overcome the magnetic
confinement.
(ii) The maxima of MR for all the ribbons,
fingerprint of the Landau levels depopulation
[5], present an up-shift of several Tesla
compared to the theoretical value [6].
(iii) The narrower ribbons exhibit the expected 6G0
conductance maxima for a two-terminal
measurement [5] but the 2G0 plateau is absent
and the depopulation of the N=2 Landau level
goes along with an unusual double peak of the
resistance (Fig. 1(b)).
To unveil the origin of the singular Landau
spectrum we performed numerical simulations of
the GNR band structure as a function of the
perpendicular magnetic field and self-consistent
calculations of the carrier distribution under
magnetic field. We directly compared the
oscillatory behaviour of the magnetoresistance and
the onset of the magneto-electric sub-bands (Fig.
2). The simulations give evidence of magneto-
oscillations of the Fermi energy (blue line in Fig. 2)
which consistently explains the broadening of the
magneto-resistance peaks and their up-shift lo
larger magnetic field. The presence of a second
peak in the MR spectrum (Fig. 2 (b)) also finds a
natural explanation: this is the clear signature of
the orbital degeneracy lifting enhanced by the
magnetic field and the pinning of the Fermi energy.
R.L. Ribeiro1,
J.M. Poumirol1, A. Cresti
2,
W. Escoffier1, J.M. Broto
1,
S. Roche3,4
and B. Raquet1
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Figure 1. Two terminal magneto-resistance measurements in a) GNR of 100nm width exhibiting the h/2e2 and h/6e
2
quantization Hall resistance. Inset: Landau level index as a function of 1/B from: experimental magneto-resistance
(circles) at high electrostatic doping, band structure calculations (crosses) and calculations of occupied sub-bands in a
hard-wall confinement. b) Magneto-resistance of a GNR of 70nm width with the presence of a double resistance peak
in the crossing of N=2 Landau level.
Figure 2. Numerical simulation of the band structure (black lines) in 814-aGNR (100 nm, Sample A) and 571-aGNR (70
nm, Sample B), self-consistent calculations of the Fermi energy under magnetic field (blue curve) and direct comparison
with magneto-resistance measurements (red curve).
References
[1] C. Berger et al. Science, 312 (2006) 1191.
[2] F. Molitor et al. PRB 79 (2009) 075426.
[3] J. B. Oostinga et al. PRB, 81 (2010) 193408.
[4] J. M. Poumirol, et al. PRB, 82 (2010) 041413.
[5] J. R. Williams et al. PRB, 80 (2009) 045408.
[6] N. M. R. Peres et al. PRB, 73 (2006) 241403
[7] R. L. Ribeiro et al. PRL 107 086601 (2011).
154 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Graphene potentialities for space and
defense applications: focus on
mechanical properties 1 Ingeniería y Servicios Aeroespaciales, S.A., Paseo del Pintor Rosales 34, 28008, Madrid,
Spain 2 Unidad de Fotónica, Instituto Tecnológico “La Marañosa”, Crta. San Martín de la Vega,
km. 10.5, 28330, Madrid, Spain
The promising properties of graphene have
motivated considerable research effort in recent
years [1]. Surprisingly, the potential advantages
offered by the technology based on graphene
structures extend to a great variety of physical
phenomena, including those affecting to electrical,
optical, magnetic, thermal, chemical and
mechanical properties. In some cases, the
parameters predicted and measured have reached
even the highest values reported for any known
material (e.g., the highest carrier mobility at room
temperature or the greater strength). However,
much work must still be carried out to bring the
inherent advantages of graphene to practical
applications. Such work comprises the
development of an efficient method to synthesize
graphene in the proper form for each desired
application without degrading its intrinsic
properties. Further steps should also ensure the
suitability of other technological aspects such as
the compatibility with device-oriented fabrication
processes, the scalability or the affordability.
Here we provide a comprehensive overview of the
potential uses of graphene-based devices and
components for space and defense sectors.
Basically, funded programmes have promoted next
generation electronics and fundamental research
topics. The development of future radio-frequency
(RF) electronics is of paramount importance to
improve the ever more demanding systems,
especially taking into account the difficulty to
maintain the historical trend predicted by Moore's
law with traditional Si-based electronics. In addition
to the more conventional approach of improving
performance parameters of active devices, new
functionalities or uses, such as those derived from
the ambipolar nature of graphene or the possibility
to achieve low-resistivity interconnects,
respectively, have also been proposed [2].
Nevertheless, the benefits explored have not only
been restricted to the utilization of graphene's
superb electrical properties. Graphene has also
been studied as building block of metamaterials
and plasmonic components, as well as for
transparent conductors, and high-speed electro-
optical modulators and photodetectors [3].
Another remarkable areas which deserve attention
in the present work are sensors and coatings (e.g.,
for inflatable structures or impermeable
membranes) [4],[5]. In all cases, the success of
graphene-based devices will depend on whether
this material can lead to substantial improvement
over competing technologies.
The case of mechanical properties and the
corresponding applications will be discussed in
further detail. Three topics, namely, piezoelectricity
(both engineered by chemical modification of the
surface or introducing stressor structures),
graphene papers and graphene composite
materials, will be addressed [6],[7]. The analysis
performed for the later structures will be focused
on determining their effective Young's modulus,
intrinsic strains and failure strains, as well as the
proper parameters to account for the interlayer
and intralayer bond strengths. It is worth noting
that graphene composites could be exploited to
enhance the macroscopic properties of the matrix
material. Therefore, other macroscopic behaviours
such as those due to the impact resistance will be
assessed for suitable structures. The applications
considered regarding mechanical properties will
include the use of graphene as filler material, the
control of mechanical motion, energy harvesting
and sensors (e.g., resonator-based mass sensors).
Carlos Rivera1,2
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References
[1] A. K. Geim and K. S. Novoselov, Nature Materials, 6 (2007) 183–191.
[2] J.-S. Moon and D. K. Gaskill, IEEE Trans. Microw. Theory Tech., 59 (2011) 2702–2708.
[3] T. Mueller, F. Xia, and P. Avouris, Nature Photonics, 4 (2010) 297–301.
[4] J. S. Bunch, S. S. Verbridge, J. S. Alden, A. M. van der Zande, J. M. Parpia, H. G. Craighead, and P. L.
McEuen, Nano Lett., 8 (2008) 2458–2462.
[5] E. W. Hill, A. Vijayaragahvan, and K. Novoselov, IEEE Sensors J., 11 (2011) 3161–3170.
[6] S. Stankovich, D. A. Dikin, G. H. B. Dommett, K. M. Kohlhaas, E. J. Zimney, E. A. Stach, R. D. Piner, S. T.
Nguyen, and R. S. Ruoff, Nature, 442 (2006) 282–286.
[7] M. T. Ong and E. J. Reed, ACS Nano, 6 (2012) 1387–1394.
156 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Supported nanomaterials for
photocatalytic water disinfection at
rural areas: from lab. scale to on-site
experiments
Facultad de Ciencias, Universidad Nacional de Ingeniería,
P.O. Box 31-139, Av. Túpac Amaru 210, Lima, Perú
In this work, It will be reviewed our experience in the fabrication and characterization of photocatalytic
nanomaterials for water purification. The growth of TiO2 nanoparticles fixed onto rigid and flexible
substrates will be shown as well as ZnO nanorods supported onto a flat substrate. All of these materials will
be discussed as a function of the main parameters used in their preparation and their ability to
photocatalytically eliminate bacteria in water. Studies were performed in the laboratory as well as at a
greenfield site. For long term on-site experiments, for example, bacteria decontamination under real
conditions has been successfully tested at rural places using solar irradiated photocatalytic prototypes of up
to 120 L. With these studies, it was demonstrated the feasibility to obtain water disinfection by using
supported photocatalytic nanomaterials illuminating it with solar radiation and makes us optimistic for the
development of robust technologies for water treatment at rural areas.
Juan Rodríguez
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Substantial increase of the critical
current on a Spin Transfer Nanopillar
by adding an Fe/Gd/Fe trilayer 1 Instituto de Sistemas Optoelectrónicos y Microtecnología, Universidad Politénica de
Madrid. Avenida Complutense 30, Madrid, Madrid, Spain. 2 Unité Mixte de Physique CNRS/Thales and Université Paris Sud 11, 1 ave. A. Fresnel,
91767 Palaiseau, France. 3 Intitut d’Électronique Fondamentale, Université Paris Sud 11-CNRS, rue André Ampère -
F 91405 Orsay, France. 4 Instituto de Microelectrónica de Madrid (CNM, CSIC), Isaac Newton 8, Tres Cantos,
Madrid 28760, Spain. Spin Transfer Torque (STT) excitations have created an increasing interest on the last few years due to the technological possibilities of current induced domain wall movement [1], switching nanomagnets [2] or generating radiofrequency signals [3]. However, they can also be detrimental in other applications like magnetic read heads, where stability and signal-to-noise ratio are very important issues in which STT has a negative effect [4]. In consequence, while for many applications the goal is to reduce the critical current density (jC) at which STT is induced, others require just the opposite.
The inclusion of Rare Earths (RE) contaminants on a magnetic layer has been one of the main approaches used to affect important magnetic properties like polarization, precessional frequency or damping [5,6,7]. Within RE, Gadolinium (Gd) is of special interest because it is ferromagnetic up to Room Temperature (TC(Gd)=293 K) and it has a very large magnetic moment at low temperatures. As a dopant it has already shown great potential for tuning the resonance frequency of a magnetic domain wall [8] or its velocity in magnetic nanostripes [9], or even controlling the spin polarization of the material [5,9].
In this work we have studied the influence of Gadolinium on the STT in Permalloy based nanopillars. We report a remarkable increase of the jC required to destabilize the Permalloy layer when a Fe/Gd/Fe ferrimagnetic trilayer is added onto the structure. Indeed, other ferrimagnetic structures have been already successfully applied in spin valves in order to increase the critical current for STT [10]. The use of a thin layer of Gd could potentially add
stability to this kind of structures without detriment of performance.
Figure 1. Stability phase diagram at 10 K corresponding to a reference Py device (a) and to a device with Fe/Gd/Fe (c). Color diagrams have been obtained from the positive branch (i.e. from –Imax to +Imax) of the R-I loops for different fields, and normalized so ΔR=0 corresponds to P state (dark blue in the diagrams). The colored lines on top of the contour plots highlight hysteretic transitions. Brown lines indicate a transition from high to low resistance in the positive branch (–Imax to +Imax), either from AP-state to lower resistance (solid brown line) or from some other intermediate resistance value (I-state) to a lower resistance (dashed brown line). Black lines represent transitions from the P state to a higher resistance state on the negative branch of the R-I loops, either from P to AP state (solid black line) or from P to a I-state (dashed black line). Selected R-I loops at 10 K and different fields for the reference device are represented in (b) and for the device with Fe/Gd/Fe in (d). The current sequence was I=0→ -Imax → +Imax → 0. Arrows in (c) and (d) emphasize minor transitions or instabilities.
M. Romera1, J. Grollier2,
V. Cros2, S. Collin2, T. Devolver3, M. Muñoz4 and J. L. Prieto1
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The basic structure used in this study is SiO2// Cu(60)/ CoFe(12)/ Cu(10)/ Py(4)/ AFL/ Cu(8) where Py stands for Permalloy (Ni80Fe20) and AFL is an Artificial Ferrimagnetic Layer of Fe(1)/ Gd(1)/ Fe(1). Numbers between brackets represent thickness in nanometers. In order to understand the effect of the AFL, we have measured also a reference sample with only Py in the free layer (i.e. SiO2// Cu(60)/ CoFe(12)/ Cu(10)/ Py(4)/ Cu(8)). Figure 1 shows the phase diagram and some selected R-I loops measured at 10 K on elliptical pillars (with axis of 50 and 150 nm) patterned on the reference sample (Fig. 1a and 1b) and on the sample with AFL (Fig. 1c and 1d) respectively.
In the hysteretic region of the diagrams (at low fields) the jC is observed to increase almost an order of magnitude with the insertion of the AFL (from 2.3·107 A/cm2 to 1.6·108 A/cm2). In the reference device, reversible transitions (usually associated to unstable precession-like motion of the free layer) are predominant out of the hysteretic region and can be observed even for very high fields (~500 Oe). On the other hand, in the device with AFL these reversible transitions are almost no existent in all the range of field applied. In fact, in this device there are not transitions at all for applied fields higher than ~200 Oe.
The effect of the Fe/Gd/Fe trilayer on the magnetic properties of the Py layer has been studied through Ferromagnetic Resonance, SQUID and P-Moke measurements (Fig. 2). We observed that the AFL modify the damping, saturation magnetization and thickness on the free layer, but these variations only explain an increase of the critical current by a factor 1.6. On the other hand, Gd has small polarization (~13% [5]), and most of the magnetic moment in the Gd layer comes from strongly localized 4f electrons. Therefore, all the angular momentum carried by the spin polarized current in the Py/Fe free layer must be transferred to the antiparallel Gd layer at the interface between the 3d Py/Fe and the 4f Gd. The effect of this sudden transfer of angular momentum can be observed experimentally in any standard Spin Valve just by inserting a very thin Gd layer between the non-magnetic layer and the free layer. By doing this the magnetoresistance value drops to zero [11]. The large jC enhancement observed in our nanopillars seems to be caused by a reduction of the effective torque on the free layer associated to the sudden transfer of angular momentum at the interface of the antiparallel Gd layer.
Figure 2. Measurements at RT in a Py(4nm)-film (black symbols) and a Py(4nm)/Fe(1nm)/Gd(1nm)/Fe(1nm)-film (red symbols). (a) Imaginary part of the permeability measured at high fields. (b) FMR data (symbols) adjusted to the Kittel equation (line). (c) P-Moke hysteresis loops with the field applied perpendicular to the sample plane. It is also important to highlight the fact that the total ΔR of the device does not change much by adding Fe/Gd/Fe, as the thickness of the Py layer underneath is of the order of its spin diffusion length. Therefore our results with this type of trilayers might constitute a potential solution to the problems of STT instability in some nanometer-size devices.
References [1] S. S. P. Parkin, M. Hayashi, L. Thomas, Science,
320 (2008) 190. [2] B. O¨ zyilmaz, A. D. Kent, D. Monsma, J. Z. Sun,
M. J. Rooks, and R. H. Koch, Phys. Rev. Lett., 91 (2003) 067203.
[3] D. Houssameddine, U. Ebels, B. Delaët, B. Rodmacq, I. Firastrau, F. Ponthenier, M. Brunet, C. Thirion, J.P. Michel, L. Prejbeanu-Buda, M.C. Cyrille, O. Redon and B. Dieny, Nat. Mat., 6 (2007) 447.
[4] J.G. Zhu and X. Zhu, IEEE Trans. Magn., 40 (2004) 182.
[5] C. Kaiser, A.F. Panchula and S.S.P. Parkin, Phys. Rev. Lett., 95 (2005) 047202.
[6] S.G. Reidy, L. Cheng and W.E. Bailey, Appl. Phys. Lett., 82 (2003) 1254.
[7] G. Woltersdorf, M. Kiessling, G. Meyer, J.U. Thiele, and C. H. Back, Phys. Rev. Lett., 102 (2009) 257602.
[8] S. Lepadatu, J.S. Claydon, D. Ciudad, C.J. Kinane, S. Langridge, S.S. Dhesi and C.H. Marrows, Appl. Phys. Lett., 97 (2010) 072507.
[9] R. L. Thomas, M. Zhu, C. L. Dennis, V. Misra and R. D. McMichael, J. Appl. Phys., 110 (2011) 033902.
[10] N. Smith, S. Maat, M. J. Carey and J. R. Childress, Phys. Rev. Lett., 101 (2008) 247205.
[11] M. Romera, M. Muñoz, P. Sánchez, C. Aroca and J. L. Prieto, J. Appl. Phys., 106, 0239922 (2009).
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New capabilities at the interface of
X-rays and scanning tunneling
microscopy
Advanced Photon Source and Center for Nanoscale Materials
Argonne National Laboratory, USA
In this talk we will discuss the development of a
novel high-resolution microscopy technique for
imaging of nanoscale materials with chemical,
electronic, and magnetic contrast. It will combine
the sub-nanometer spatial resolution of scanning
tunneling microscopy (STM) with the chemical,
electronic, and magnetic sensitivity of synchrotron
radiation. [1,2] Drawing upon experience from a
prototype that has been developed to demonstrate
general feasibility, current work has the goal to
drastically increase the spatial resolution of existing
state-of-the-art x-ray microscopy from only tens of
nanometers down to atomic resolution. Key
enablers for high resolution are insulator-coated
“smart tips” with small conducting apex (cf. Fig. 1).
[3] The technique will enable fundamentally new
methods of characterization, which will be applied
to the study of energy materials and nanoscale
magnetic systems. A better understanding of these
phenomena at the nanoscale has great potential to
improve the conversion efficiency of quantum
energy devices and lead to advances in future data
storage applications. The combination of the high
spatial resolution of STM with the energy selectivity
afforded by x-ray absorption spectroscopy provides
a powerful analytical tool.
Scan me
Figure 1. X-ray nanotomography surface rendering of a
smart scanning tunneling microscope tip. The platinum-
iridium tip (red) has been coated with a SiO2 insulating
layer (green).
References
[1] V. Rose, J.W. Freeland, S.K. Streiffer, “New
Capabilities at the Interface of X-rays and
Scanning Tunneling Microscopy”, in Scanning
Probe Microscopy of Functional Materials:
Nanoscale Imaging and Spectroscopy, S.V.
Kalinin, A. Gruverman, (Eds.), Springer, New
York (2011), pg 405-432.
[2] M.L. Cummings, T.Y. Chien, C. Preissner, V.
Madhavan, D. Diesing, M. Bode, J.W. Freeland,
V. Rose, Ultramicroscopy 112, 22 (2012).
[3] V. Rose, T.Y. Chien, J. Hiller, D. Rosenmann,
R.P. Winarski, Appl. Phys. Lett. 99, 173102
(2011).
Volker Rose
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Mechanical properties of freely
suspended atomically thin
dielectric layers of mica 1 Dpto de Física de la Materia Condensada. Universidad Autónoma de Madrid,
Campus de Cantoblanco. E-28049 Madrid, Spain. 2 Kavli Institute of Nanoscience, Delft University of Technology, Lorentzweg 1,
2628 CJ Delft, The Netherlands. 3 Yale University. Department of Engineering Science. Becton 215, 15 Prospect St. New
Haven, CT 06520, USA. 4 Instituto Madrileño de Estudios Avanzados en Nanociencia IMDEA-Nanociencia,
E-28049 Madrid , Spain.
We study the elastic deformation of freely
suspended atomically thin sheets of muscovite
mica [1][3] (see Figure 1), a widely used electrical
insulator in its bulk form. Using an atomic force
microscope, we carried out bending test
experiments [1,2] (see Figure 2) to determine the
Young’s modulus and the initial pre-tension of mica
nanosheets with thicknesses ranging from 14 layers
down to just one bilayer. We find that their Young’s
modulus is high (190 GPa), in agreement with the
bulk value which indicates that the exfoliation
procedure employed to fabricate these nanolayers
does not introduce a noticeable amount of defects.
Additionally, ultrathin mica presents low pre-strain
and it can stand reversible deformations up to tens
of nanometers without breaking. The low pre-
tension and high Young's modulus and breaking
force found in these ultrathin mica layers
demonstrates their prospective use as complement
for graphene in applications requiring flexible
insulating materials or as reinforcement in
nanocomposites.
References
[1] A. Castellanos-Gomez et al., Nano Research
(accepted) 2012.
[2] A. Castellanos-Gomez et al., Advanced
Materials, 24 (2012) 772-775.
[3] A. Castellanos-Gomez et al., Small, 7 (2011)
2491-2497.
Figure 1. Optical micrograph of ultrathin two
dimensional mica layers deposited on a silicon subtrate
patterned with holes, where the mica sheet is
suspended. Different colors correspond to different mica
sheet thicknesses. The graph shows the optical contrast
dependence on the mica sheet thickness.
Figure 2. Force vs. deformation traces measured at the
center of the suspended part of mica nanosheets with 2,
6 and 12 layers in thickness. The slope of the traces
around zero deflection is marked by a dotted line. (Inset)
schematic diagram of the bending test experiment
carried out on a freely suspended mica nanosheet.
G. Rubio-Bollinger1,
A. Castellanos-Gomez1,2
,
M. Poot3,2
, G. A. Steele2,
H.S.J. van der Zant2 and
N. Agraït1,4
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An efficient MRI contrast agent
based on PEGylated iron oxide
nanoparticles
Instituto de Ciencia de Materiales de Madrid/CSIC, Cantoblanco, 28049 Madrid, Spain
Estudios Avanzados de Cuba, San Antonio de Los Baños km 3½, La Habana, Cuba
Superparamagnetic nanoparticles are of special
interest for various applications in nanomedicine.
Nowadays, one of the most important and rapidly
growing fields is the use of iron oxide particles as
contrast agents for magnetic resonance imaging
(MRI). Also, the immobilization of poly(ethylene
glycol) (PEG) onto the nanoparticles's surface is the
most used strategy to avoid opsonisation and
cellular recognition, improving biocompatibility and
pharmacokinetic. In this study, we developed a MRI
contrast agent based on PEGylated iron oxide
nanoparticles. Magnetite nanoparticles (12 nm in
diameter) were obtained via thermal
decomposition of a iron coordination complex to
assure nanoparticle homogeneity in size and shape
(Fig. 1). Particles were coated with DMSA by a
ligand exchange process to remove oleic acid, after
which three distinct short-chain PEG polymers were
covalently bound to the nanoparticle surface via
EDC activation of the carboxylic groups. In all cases,
colloidal suspensions had hydrodynamic sizes
below 100 nm and low surface charge,
demonstrating the effect of PEG coating on the
colloidal properties and stability of the magnetic
nanoparticles. We tested in vitro the internalization
and biocompatibility of these materials in the HeLa
human cervical carcinoma cell line. Cells
preincubated with PEG-coated iron nanoparticles
were visualized outside the cells and their
biocompatibility at high Fe concentrations was
demonstrated using a standard MTT assay. Finally,
we used relaxivity parameters (r1 and r2) to
evaluate the efficiency of suspensions as MRI
contrast agents; r2 values were four times higher
than that for commercial products, probably due to
the larger nanoparticle size. The time of residence
in blood after coating increased up to hours in New
Zealand rabbits and Wistar rats (Fig. 2). Our results
suggest that this PEGylation strategy for large
magnetic nanoparticles (>10 nm) holds promise for
biomedical applications. T2 MRI images of rat liver
before and after injecting the synthesized contrast
agent showed a significant increase in the contrast
with time from 10 min up to 50 minutes (Fig. 3).
References
[1] D. Peer, J.M. Karp, S. Hong, O.C. Farokhzad, R.
Margalit, R. Langer, Nat. Nanotechnol. 2007, 2,
751
[2] M. Colombo, S. Carregal-Romero, M. F. Casula,
L. Gutiérrez, M.P. Morales, I.B. Böhm, J.T.
Heverhagen, D. Prosperi, W. J. Parak, Chem.
Soc Rev. 2012, DOI:10.1039/c2cs15337h.
[3] J. Gao in Biofunctionalization of Nanomaterials
(Eds: Ch. Kumar), Wiley-VCH Verlag GmbH &
Co. KGaA, Weinheim, Germany 2005, Ch. 3.
[4] S. Perrault, C. Walkey, T. Jennings, H. Fischer,
W. Chan, Nano Lett. 2009, 9, 1909.
[5] C. Fang, N. Bhattarai, C. Sun, M. Zhang, Small
2009, 5, (14) 1637.
[6] A. G. Roca, S. Veintemillas-Verdaguer, M. Port,
C. Robic, C. J. Serna, M. P. Morales, J. Phys.
Chem. B 2009, 113, 7033.
Amalia Ruiz, Gorka Salas,
Macarena Calero, Yenisel
Hernández, Angeles
Villanueva, Fernando
Herranz, Sabino
Veintemillas-Verdaguer,
Eduardo Martínez,
Domingo F. Barber and
María del Puerto Morales
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Figure 1. (a) TEM images of magnetite nanoparticles (b) Size-distribution graph. The red line is the log-normal fitting
function of the particle size data.
Figure 2. (e, f) ICP quantification of iron concentration in
blood after injection into e) rabbits and f) rats. NP-
DMSA-PEG-NH2 [○], NP-DMSA-PEG-(NH2)2 [■] and NP-
DMSA-PEG-Prop-(NH2)2) [∆].
Figure 3. T2 MR images of rat liver before and after
injecting the synthesized contrast agent. In the left
animal injected with NP-DMSA-PEG-(NH2)2 and in the
right control animal (a)T2 image after 10 minutes of
injection.(b)T2 image after 50 minutes of injection.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 163
Creating nanowires with
atomic precision
University of Alicante, Departamento Física Aplicada, Carretera San Vicente del Raspeig
s/n, San Vicente del Raspeig, Spain
Measuring the conductance between gold
electrodes and limiting the indentation depth
between the two electrodes up to a conductance
value of approximately 5G0 in the case of gold we
can obtain the same conductance behavior for
hundreds of cycles of formation and rupture of the
nanocontact. Furthermore, when two metals
approach, the first contact between them occurs
abruptly in most cases. This phenomenon is called
“jump-to-contact”. It is well known that the
conductance in a nanocontact is related to the
smallest area of the contact between the two
electrodes. Therefore, variations of the
conductance should be related to changes in the
atomic structure at the contact. Similarly, a jump in
the conductance is observed when the two
electrodes are pulled apart and the contact is
broken, in what is called "jump-out-of-contact".
Both experiments are rationalized using molecular
dynamics simulations together with density
functional theory transport calculations which show
how:
a) after repeated indentations (mechanical
annealing), the two metallic electrodes are
shaped into tips of reproducible structure.
b) certain atomic contact structures are most
likely to occur.
These results provide a crucial insight into
fundamental aspects relevant to nano-tribology or
scanning probe microscopies.
References
[1] C.Sabater, C. Untiedt, J.J.P, Phys. Rev. Lett.
108, 205502 (2012).
[2] C. Untiedt, M. J. Caturla, M. R. Calvo, J. J.
Palacios, R. C. Segers, and J. M. van
Ruitenbeek, Phys. Rev. Lett. 98, 206801 (2007)
Figure 1. Experimental traces obtained for Au
nanocontacts during formation and rupture when
limiting the conductance to (a) 5G0 and (b) 8G0. The inset
shows a 3D figure of the rupture where the third axis is
each individual trace.
Figure 2. Snapshots of the MD simulations of rupture
and formation of a nanocontact in gold for the initial
configuration and before cycles 2, 5, 10, 15 and 20 (top).
Number of atoms in the top nanoelectrode (in %) that
were initially on the second one, and viceversa, as a
function of the number of cycles(bottom). Temperature
was not fixed in this calculation.
C. Sabater, J.J. Palacios,
M.J. Caturla, C. Untiedt
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Figure 3. Traces of conductance from DFT (open circles
are calculations with 1 electron and diamonds are
calculations with 11 electrons) and estimates from MD
minimum cross section (lines) for calculations with 525
atoms. (a) Rupture trace during first cycle and (b)
rupture trace for cycle number 10 for a maximum
indentation of 5 atoms in cross section.
Figure 4. (color online) Analysis of the steepest jump of
conductance before the formation of a metallic contact
for the case of gold, made from more than 300 000
conductance traces. The left panel shows a density plot,
where the horizontal axes represents the conductance at
which the jump takes place and the vertical axes shows
the conductance of the contact formed. We have
artificially changed the colors of the peak above (gray
scale) to make it visible. The right panel shows the
corresponding histogram of the conductance of the
contact formed after the jump.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 165
Nanoscale elemental analysis and
applications using STM combined
with brilliant hard X-rays 1 Department of Precision Science & Technology, Osaka University, 2-1 Yamada-oka,
Suita, Osaka 565-0871, Japan 2 RIKEN SPring-8 Center, 1-1-1 Kouto, Sayo-cho, Hyogo 679-5148, Japan
3 Institute for Molecular Science, Myodaiji-cho, Okazaki 444-8585, Japan
4 WPI center, National Institute for Materials Science,Tsukuba 305-0003, Japan
Analyses by scanning tunneling microscopy (STM)
combined with brilliant X-rays from synchrotron
radiation (SR) can provide various possibilities of original
and important applications. The STM observation under
inner-shell excitation at a specific core-level enables us
to analyze the elements or control the local reaction
with the high spatial resolution of STM [1].
We have recently demonstrated the elemental analyses
with a spatial resolution lower than 2 nm on
semiconductor surfaces [2]. The principle of our
analyses is not to collect the secondary electrons by
STM tip (that may damage the spatial resolution), but to
extract the element-specific modulation of the
”tunneling current” succeeding the core-excitation
process, which contains truly local information. A key to
accomplish successful results is to effectively increase
the signal to noise (S/N) ratio. On this purpose, we
developed a special SR-STM system.
The experimental setup is shown in Fig.1. To surmount
a tiny core-excitation efficiency by hard X-rays, we
focused two-dimensionally an incident beam having the
highest photon density at the SPring-8. Many problems
derived from the high brilliance (thermal and electrical
noise, damage of STM scanner, instability such as
thermal drift, etc.) were solved by the special apparatus
and system [1]. Furthermore, we developed a special tip
[3] (that can eliminate the noisy electrons coming from
a wide area) and signal acquisition system that realizes a
high signal to noise ratio to obtain a small modification
of the tunneling current originating from the core
excitation.
After first results on a semiconductor hetero-interface
(Si(111)7x7-Ge) [1], second results on the nanoscale
elemental analysis were acquired for metal-
semiconductor interface (Ge(111)-Cu nano-domains)
[2]. For both cases, the spatial resolution of the analysis
was estimated to be 1~4 nm, and it is worth noting that
the measured domains had a thickness of less than one
atomic layer (Fig.2).
Figure 1. Schematic view of experimental setup.
Figure 2. (a) Line profile of beam-induced tip current
image along the line shown in the bottom image. (b)
Topographic image and (c) beam-induced tip current
image of Ge (111)-Cu (-2V, 0.2 nA).
After progresses of the measurement system and
techniques, we succeeded in obtaining a series of
successive STM images at an atomically same area
Akira Saito1,2
, T. Tanaka1, H.
Matsuno1, H. Miki
1, Y.
Furudate1, Y. Takagi
3, M.
Akai-Kasaya1, Y. Tanaka
2, Y.
Kohmura2, T. Ishikawa
2, Y.
Kuwahara1,2
and M. Aono4
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without serious drift or sample damages. Accordingly,
we could acquire a linear dependence of the element
contrast on the incident photon density. The photon
density dependence of the elemental contrast will give
an important clue to know the origin of the element
contrast. Actually, our result on the linear dependence
of the element contrast on the photon density suggests
that we can deny a possibility of the local potential
change derived from the core excitation, because the
potential should give an exponential dependence of the
contrast on the incident photon density.
Also we could recently measured scanning tunneling
spectroscopy (STS), which have long been impossible
because of instability due to brilliant X-ray irradiation.
STS information gives us more direct hint to approach
the mechanism of contrast to obtain a higher
resolution. It is notable that the image in Fig. 2(c) shows
the contrast originating from the chemical difference
(that is not based on the surface step height),
presenting the structures different from the
conventional topographic (Fig. 2(b)) image.
Next, we have recently achieved a direct observation of
the “X-ray induced atomic motion” with the track of the
atomic motion at an atomic scale using the SR-STM
system under the incident photon density of ~2x1015
photon/sec/mm2 [4]. This observation was enabled only
by use of the in situ SR-STM system, because the STM
images in the atomically same area should be compared
before and after X-ray irradiation. In our STM images,
the low-magnification images showed that the X-ray
induced atomic motion rate is so low that structural
changes are hardly detectable by other surface analysis
techniques such as diffraction analysis. However, the
magnified STM images revealed a clear change in the
atomic structures after X-ray irradiation. Then, we
developed a technique to recognize atomic motions
directly to comprehend their behavior. By merging the
STM images obtained before and after X-ray irradiation,
the atomic motion track could be newly presented as
several continuous lines (Fig. 3), whereas other stable
atoms are shown as spheres. The appeared atomic track
is the direct evidence and visualized information of the
atomic diffusion at an atomic scale. It is worth
comparing our results with past conventional thermal
STM observations on the same surface [5], where the
atomic motion was found to occur in the form of 2-
dimensional domain and begin at ~220°C. However, our
results show the atomic track having a local chain
distribution. This locality in diffusion can be attributed
to the anisotropy of the surface structure, and probably
the origin of atomic motion, to core excitation. In fact,
considering the temperature increase of 92 K from the
room temperature estimated from the X-rays
irradiation, our atomic motion occurs at very low
temperature in comparison with the past report.
Apart from the result on the elemental analysis, this
finding on the atomic motion will serve to study the
initial radiation effect on the optical devices such as
mirror or grating at the X-ray sources of new generation
such as X-ray free electron laser (XFEL). Also our
observation of the damage barrier has potential
importance as an indicator for a damage threshold in
the near future for analyzing tiny materials using strong
X-rays.
On the other hand, the above mentioned results will
allow us to study the element-specific atomic control of
local reaction with the spatial resolution of STM, giving
hope of wide application. For example, the dense X-rays
are suggested to have new applications, such as direct
X-ray lithography. In other viewpoint, our results show a
new application of the in situ SR-STM system. Our
method for observing the atomic track will serve to
provide new information not only for the radiation
effects on various optical devices in new X-ray
generators, but also for basic science by observing
photon-matter interactions.
Figure 3. Atomic motion tracks newly presented by
merging the STM images before and after X-ray
irradiation.
References
[1] A.Saito, et al.: J.Synchrotron Rad.13 (2006)
216. ;Jpn.J.Appl.Phys.45 (2006) 1913.; Curr.
Appl.Phys. (2012) in press.
[2] A.Saito et al.: Surf. Interface Anal. 40 (2008)
1033.; "Nano-imaging" (NTS publisher, 2008)
p.278.
[3] A.Saito et al.: Surf. Sci. 601 (2007) 5294.
[4] A.Saito et al.: J. Nanosci. Nanotechnol. 11
(2011) 1873.
[5] R.M. Feenstra et al.: Phys. Rev. Lett. 66 (1991)
3257.
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Biorthogonal chemistry for the
functionalization of
superparamagnetic nanoparticles:
cross olefin metathesis 1 Unidad de Imagen Avanzada. Centro Nacional de Investigaciones Cardiovasculares
(CNIC).Madrid, Spain 2 Dpto.Química-Física II, Facultad de Farmacia Universidad Complutense, CIBERES,
Madrid, Spain 3 Biomaterials and Bioinspired Materials Instituto de Ciencia de Materiales de
Madrid,Madrid, Spain
The use of magnetic nanoparticles in biomedical
applications has witnessed an exponential growth
last years. Iron oxide nanoparticles (NP),
particularly, have gained a dominant role because
of their physicochemical properties and low
toxicity. Due to their superparamagnetic behavior
these particles are of paramount importance in
imaging techniques like Magnetic Resonance
Imaging (MRI) and Magnetic Particle Imaging (MPI).
In order to provide stability and targeting these NPs
require specific coating. The association of one or
more biologically relevant molecules at the
interface of a NP defines a NP-bioconjugate, which
combines the unique physicochemical properties of
NP materials with biological activity such as
selective binding. To date, researchers have largely
relied upon the traditional chemistries associated
with protein labeling for the preparation of NP-
bioconjugates. However, the range of
bioconjugation techniques used with NPs has
lagged behind the multitude of biological
applications proposed. Although traditional
bioconjugate chemistries have been adequate for
proof-of-concept studies, the optimization of NP-
bioconjugates for real applications (e.g., clinical)
will require much greater control than these
chemistries can offer. Rather, clean, efficient, and
bioorthogonal conjugation reactions are required
to eliminate undesirable side reactions, minimize
nonspecific NP-bioconjugate activity, improve
reproducibility in production, and maximize efficacy
[1-3]. Within this group of bioorthogonal chemistry,
olefin metathesis offers many of these features
thanks to the new family of catalysts, especially
Hoveyda-Grubbs 2nd generation. The metathesis
mechanism reorganizes the carbon atoms of two
C=C bonds, generating two new ones in the
presence of a catalyst. This kind of reaction allows
access from the easily prepared olefins to those
that are cumbersome to obtain, being an efficient
and stereoselective synthesis of the more
substitute olefins in mild conditions. All of these
advantages make the metathesis of alkenes one of
the most powerful tools in synthetic chemistry, but
as far as we know, it has not been applied for the
functionalization of iron oxide superparamagnetic.
Here we present our results in the functionalization
of superparamagnetic iron oxide nanoparticles with
four different terminal olefins through metathesis
reaction [4]. First, we synthesized iron oxide
nanoparticles by the decomposition of organic
precursor obtaining hydrophobic Fe3O4 NPs, with
oleic acid as surfactant. The olefin metathesis was
made between the double bond in oleic acid
structure and four different molecules with a
terminal double bond; methyl acrylate, 6-
hexenetirile, allyltrifluoroacetate and 3-allyloxi-1,2-
propandiol, in presence of catalytic amounts
(4%mol) of Hoveyda-Grubbs second generation
catalyst. These new NPs were fully characterized by
TEM, VSM, MS and FTIR, showing the success of the
reaction and quite good values for the
hydrodynamic size and PDI as can be seen in
figure 1.
B. Salinas1,2
,
J. Ruiz-Cabello1,2
,
M.P. Morales3 and
F. Herranz2
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Figure 1. General metathesis synthesis and summary of
the averaged sizes.
Figure 2. Hydrolysis of NPs (2) with methyl acrylate,
generating hydrophilic NPs.
After the metathesis the ester bond in 2 was
hydrolyzed rendering water stable sample 6 due to
the presence of the terminal carboxylic acid, with a
Z average of 28 ± 10 nm (PDI 0.30 ± 0.07, N=3).
These NPs were fully characterized. The
physicochemical properties of the inorganic core
were studied by TEM and VSM, which
demonstrated the superparamagnetic behavior of
the sample [4].
The presence of the acid was probed through the
FTIR spectrum and the ζ potential profile, which
exhibit their stability in physiological conditions,
with a value of -37 ± 5 mV at pH 7, and the typical
profile for NPs stabilized by a carboxylic acid.
For biomedical applications the nanoparticles must
show high stability in solutions with high ionic
strength. To this end metathesis is especially well
suited as it allows such modifications in one single
step from the hydrophobic particles if the right
olefins are used. For this reason once
demonstrated the possibility of using the
metathesis in USPIO the second stage was the
direct bioconjugation with hydrophilic polymers
bearing a terminal olefin. On this regard we will
focus in the results obtained with Polyethylene
glycol (PEG) and different proteins from the
extracellular matrix. First, the biopolymers were
modified to show a terminal olefin through a
substitution reaction. The metathesis was applied
as shown before over the sample 1, rendering
hydrophilic NPs. These NPs were fully characterized
by FTIR, MS, VSM and TEM, showing the success of
the reaction keeping the superparamagnetic
behavior of the NPs, which allow their possible use
as MRI contrast agent.
In this work we demonstrate, for the first time, the
use of the cross olefin metathesis reaction for
bioorthogonal functionalization of iron oxide
nanoparticles with different ligands, allowing the
incorporation of different functional groups and
biomolecules. Using appropriate catalyst and
reaction conditions it is possible to modify the
structure of the surfactant without self-metathesis,
as demonstrated with the hydrodynamic size, TEM
images and FT-IR spectra reported here. This
simplifies the synthesis of hydrophobic and
hydrophilic nanoparticles with applications in
different fields.
References
[1] Russ Algar W., Prasuhn D. E., Stewart M. H.,
Jennings T. L., Blanco-Canosa J. B., Dawson P.
E., Medintz I. L. 2011 Bioconjugate Chem., 22,
825–858.
[2] Herranz F., Morales M.P., Roca A.G., Desco M.,
Ruiz-Cabello J. 2008 Chemistry- A European
Journal, 14(30), 9126-9130.
[3] Herranz F., Almarza E., Rodríguez I., Salinas B.,
Rosell Y., Desco M., Bulte J.W.M., Ruiz-Cabello
J. 2011 Microsp. Res. Tech. 74 (4), 577-591.
[4] B. Salinas, J. Ruiz-Cabello, M.P. Morales, F.
Herranz. 2012 Bioinspired, Biomimetic and
Nanomaterials. 1, 166-172.
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AC Josephson effect in finite-length
nanowire junctions with Majorana
modes
Instituto de Estructura de la Materia (CSIC)
Serrano 123, 28006 Madrid (SPAIN)
It has been predicted that superconducting junctions made with topological nanowires hosting Majorana
bound states (MBS) exhibit an anomalous 4π-periodic Josephson effect. Finding an experimental setup with
these unconventional properties poses, however, a serious challenge: for finite-length wires, the equilibrium
supercurrents are always 2π periodic as anticrossings of states with the same fermionic parity are possible.
We show, however, that the anomaly survives in the transient regime of the ac Josephson effect. Transients
are, moreover, protected against decay by quasiparticle poisoning as a consequence of the quantum Zeno
effect, which fixes the parity of Majorana qubits. The resulting long-lived ac Josephson transients may be
effectively used to detect MBS.
References
[1] Phys. Rev. Lett. 108, 257001 (2012)
Pablo San Jose
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Thermal and mechanical effects of
different excitation modes based on
low frequency laser modulation in
optical hyperthermia
Centre for Biomedical Technology (CTB), Technical University of Madrid (UPM),
Campus Montegancedo, Pozuelo de Alarcón (Madrid), Spain
Recently, gold nanoparticles, in combination with
laser light, have been used successfully to achieve
controlled thermal damage in tumor tissue [1] [2].
Gold nanostructures show a unique optical
property, ie, they efficiently absorb light due to the
surface plasmon resonance phenomenon and then
convert the absorbed light into localized heat [3].
Our first work was aimed at obtaining a proof of
concept of an optical hyperthermia system [4]. The
instrument was similar to others currently being
used [5] [6], but with the possibility of using
different excitation methods by changing the light
exposure pattern from continuous wave light to
pulsed light. The system was developed to evaluate
the effectiveness of gold nanorods designed to
work in the optimal tissue window for light
absorbance (808 nm) used to produce cellular
death in glioblastoma cell lines (1321N1). The
obtained results showed that the use of gold
nanorods in hyperthermia therapy is very effective
(Figure 1) but in order to develop an optimal
treatment, many parameters still need to be
optimized, concerning both laser irradiation and
gold nanorods characteristics.
After these first results, our work is focused on the
development of new excitation methods with the
aim of increasing the effectiveness of the
hyperthermic treatment thanks to the well known
thermal effects and to other mechanical effects
that are being studied and could influence the cell
death process.
The low frequency modulation of the laser source
(<30KHz) allows the generation of a pulsed signal
that intermittently excites the gold nanorods. The
temperature curves obtained for different
frequencies and duty cycles of modulation but with
equal average power and identical laser
parameters, show that the thermal behavior in
continuous wave and modulation modes are the
same (Figure 2). However, the cell death
experiments suggest that the percentage of death
is higher in the cases of modulation (Figure 3). This
observation allows us to conclude that there are
other effects in addition to temperature that
contribute to the cellular death.
Figure 1. Photothermal treatment of 1321N1. The cells
were stained with propidium iodide and then fixed and
analyzed on a flow cytometer. The graph shows the
percentages of dead cells (IP+-cells) over total cells,
calculated for each condition. Control: 1321N1 basal cell
death rate. AuNRs: 1321N1 cells incubated with gold
nanorods. Laser: 1321N1 cells subjected to laser
irradiation. Laser + AuNRs: 1321N1 cells subjected to
laser irradiation in the presence of gold nanorods.
The mechanical effects like sound or pressure
waves are expected to be generated from thermal
expansion of gold nanorods. In order to study the
behavior and magnitude of these processes we
have developed a measure device based on
ultrasound piezoelectric receivers (25KHz) and a
lock-in amplifier that is able to detect the sound
Cristina Sánchez,
Julio Alberto Ramos,
Tamara Fernández,
Milagros Ramos,
Alberto Martínez,
Francisco del Pozo,
José Javier Serrano
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waves generated in samples of gold nanorods
during laser irradiation providing us a voltage level
proportional to the pressure signal.
The first results (Figure 4) show that the pressure
measurements are directly proportional to the
concentration of gold nanorods and the laser
power, therefore, our present work is focused on
determine the real influence of these effects in the
cell death process.
References
[1] Huff TB, Tong L, Zhao Y, Hansen MN, Cheng JX,
Wei A. Hyperthermic, Nanomedicine (Lond), 2
(2007) 125-132.
[2] Kuo WS, Chang CN, Chang YT, et al., Angew
Chem Int Ed Engl., 49 (2010) 2711-2715.
[3] Jain PK, El-Sayed IH, El-Sayed MA, Nano Today,
2 (2007) 16-27.
[4] Fernández T, Sánchez C, Martínez A, del Pozo
F, Serrano JJ, Rarmos M, Int. J. Nanomed, 7
(2012) 1511-1523.
[5] Fourkal E, Vlechev I, Taffo A, Ma C, Khazak V,
Skobeleva N., IFMBE Proc., 25 (2009) 761-763.
[6] Rozanova N, Zhang JZ, Science in China Series
B: Chemistry, 52 (2009) 1559–1575.
Figure 2. Temperature curves of gold
nanorods suspension for different duty
cycles of modulation in comparison to the
continuous wave mode (CW). The
parameters of the laser are fixed in an
average power of 381 mW and a frequency
of modulation of 5KHz.
Figure 3. IP/calcein essay 24h after irradiation: Comparison between different times and excitation modes (modulation
and CW).
Figure 4. Voltage levels for different laser
intensitiy values (linearly proportional to
the power source) in a duty cycle sweep.
172 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Maximal entanglement out of
transport through double
quantum dots
Instituto de Ciencia de Materiales de Madrid (ICMM-CSIC),
Sor Juana Inés de la Cruz 3, Madrid, Spain
Double quantum dots connected in series to source and drain electronic reservoirs can be tuned to contain
up to two electrons. In such configuration, current suppression due to Pauli exclusion principle has been
detected [1]. This effect is known as spin blockade. Driving the system with time dependent magnetic fields
allows the coherent manipulation of the two electron states. Single spin rotations remove Pauli correlations
and restore the flow of current [2,3]. Analyzing the current spectrum as a function of the driving frequency,
we find dark resonances where spin blockade is restored due to collective rotations of the two spins. Then,
the two electrons are spatially separated, each one kept in a different quantum dot. Furthermore, for such
frequencies the system evolves towards a maximally entangled stationary state [4]. We find robust Rabi
oscillations of two positive parity Bell states for weak coupling to the reservoirs. We investigate the influence
of the magnetic field polarization.
References
[1] K. Ono, D.G. Austing, Y. Tokura, S. Tarucha, Science 297 (2002) 1313.
[2] F.H.L. Koppens, C. Buizert, K. J. Tielrooij, I. T. Vink, K. C. Nowack, T. Meunier, L. P. Kouwenhoven, L. M. K.
Vandersypen, Nature 442 (2006) 766.
[3] R. Sánchez, C. López-Monís, G. Platero, Phys. Rev. B 77 (2008) 165312.
[4] R. Sánchez, G. Platero, in preparation.
Rafael Sánchez and
Gloria Platero
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 173
TDDFT simulations of the energy
loss of moving projectiles in solids
and nanostructures
Centro de Física de Materiales UPV/EHU-CSIC,
Paseo Manuel de Lardizabal 5, 2018 San Sebastián, Spain
We have recently developed a code to perform real
time time-dependent density-functional theory
simulations [1,2,3]. Our method is based on the
SIESTA code [4] and uses a linear combination of
atomic orbitals as a basis set. Previous versions of
our code had been used to study the optical
response of finite systems [1], i.e., electron
dynamics was followed after the system was
initially perturbed while nuclei were kept fixed in
their initial positions. Our most recent version,
however, allows performing coupled electron-
nuclear dynamics within the Ehrenfest
approximation and has been applied to study the
problem of radiation damage in solids and
nanostructures.
Figure 1. Electronic stopping power of H and He
projectiles in gold as a function of projectile velocity.
Results of our simulations are compared with the
experimental data from on single and polycrystalline thin
gold films.
Although radiation damage processes are of
extraordinary fundamental and technological
importance, ab initio simulations of these effects in
solids are still very scarce to date. Most simulations
for solids and condensed systems are based on
semi-empirical approaches, like SRIM [5]. The
energy transferred to the solid goes both onto
displacements of the target ions (nuclear stopping)
and electronic excitations (electronic stopping).
While at very low velocities nuclear stopping can
we dominant, at moderate, intermediate and high
energies the most efficient energy loss mechanism
is the electronic stopping. The effect of electronic
stopping is frequently incorporated in simulations
through an ion and target dependent friction
coefficient. Thus, the electronic stopping is
assumed to depend linearly on velocity. This is
generally true for simple metals, for which the
friction coefficient can be estimated very efficiently
using a jellium model plus scattering theory [6].
However, it has been recently observed that there
are significant deviations from linearity at low
velocities in insulators and noble metals, both
showing different kinds of threshold effects.
Understanding of such effects demands an explicit
treatment of the electronic stopping in the
presence of the actual atoms and actual electronic
structure of the host system. Our simulations using
time-evolving TD-DFT could reproduces the
anomalies in the stopping power observed
experimentally for projectile velocities below 0.3
a.u., for insulators and noble metals [2,3]. In
addition, we could analyze the Barkas effect
(difference in stopping between protons and
antiprotons) in LiF [2], and the He/H anomaly in Au
[3] (the stopping is larger for He at all velocities,
contrary to expectations based on free electron
models). Our approach has quite general
applicability and we plan to apply it to other
radiation damage problems. As an example, we
have recently studied the influence of the electrons
being excited on the effective internuclear forces
when an Al target is bombarded with protons [7].
Daniel Sánchez-Portal
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Figure 2. Screening of a localized hole during
photoemission from a metal (jellium) clusters. The
induced electronic density is shown close to the
symmetry z-axis (r = 0.02 a.u., the electron is emitted
along the z-axis and r is the perpendicular coordinate).
The time evolves along the vertical axis. The color map
shows the change in density in units of the background
density. The color scale is limited to a maximum value of
in order to reveal the effects in the regions where the
induced density is small. The induced density above this
value is shown in green. The actual maximum value of
the induced density is about 50 in units of background
density. It corresponds to the small region around the
position of the hole. (a) Shows the results of the TDDFT
calculation of the complete system. In (b) the induced
density is calculated as a sum of two separate
contributions, screening of the hole and screening of the
moving electron. The cluster contains 106 electrons and
has radius of 18.93 a.u., with density corresponding to
rs = 4.The velocity of the electron is constant and is
equal to 1 a.u. Insets: profile of the plot along the time
axis at (r= 0.02 a.u., z= 0.2 a.u.)
Finally, the dependence of the electron dynamics
on the size and dimensionality is an important issue
in many fields. For example, it determines the
efficiency and time scale of the screening of
interactions, the rate of many chemical reactions at
surfaces and the optical response of nanoobjects.
We plan to use our methods to investigation some
of these issues. In particular, I will present some of
our recent semi-classical results on the influence of
the localized-hole screening on the energy losses
during photoemission from metal clusters [10].
References
[1] A. Tsolakidis, D. Sánchez-Portal, and R. M.
Martin Phys. Rev. B 66 (2002) 235416.
[2] J. M. Pruneda, D. Sánchez-Portal, A. Arnau, J.
I. Juaristi, and Emilio Artacho Phys. Rev. Lett.
99 (2007) 235501.
[3] M. A. Zeb, J. Kohanoff, D. Sánchez-Portal, A.
Arnau, I. Juaristi and E. Artacho, Phys. Rev.
Lett. 108 (2012) 225504.
[4] J. M Soler, E. Artacho, J. D. Gale, A. García, J.
Junquera, P. Ordejón and D. Sánchez-Portal,
J. Phys.: Condens. Matter 14 (2002) 2745.
[5] J. F. Ziegler, J. P. Biersack, and U. Littmark,
“The Stopping and Range of Ions in Matter”,
New York, 1985. Pergamon. ISBN 0-08-
022053-3.
[6] P. M. Echenique, R. M. Nieminen, J. C. Ashley
and R. H. Ritchie, Phys. Rev. A 33 (1986) 897.
[7] A. A. Correa, J. Kohanoff, E. Artacho, D.
Sánchez-Portal and A. Caro, Phys. Rev. Lett.
108 (2012) 213201.
[8] E. V. Chulkov, A. G. Borisov, J. P. Gauyacq, D.
Sánchez-Portal, V. M. Silkin, V. P. Zhukov and
P. M. Echenique Chemical Reviews 106
(2006) 4160.
[9] R. D. Muiño, D. Sanchez-Portal, V. M. Silkin,
E. V. Chulkov and P. M. Echenique, PNAS 108
(2011) 971.
[10] N. Koval, D. Sánchez-Portal, A. G. Borisov, R.
D. Muiño, to appear on Nanoscale Research
Letters.
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WaveGuide's u-NMR and magnetic
nanoswitches for security and
defense applications
WaveGuide Corporation
One Broadway, 14th floor
Cambridge, MA 02142, USA
The uNMR, innovative technology combined with proprietary Magnetic Nanoswitches enables low cost
rapid, on-site screening for Security and Defense Applications.
Product applications include point of testing of suspicious samples to determine if a biothreat agent is
present, anti-counterfeiting, adulteration and product diversion in industries as diverse as petroleum,
pharmaceuticals and beverages.
WaveGuide Corporation is a Harvard University spin out that is commercializing a handheld nuclear
magnetic resonance spectrometer (uNMR) and proprietary Magnetic Nanoswitches.
Marcus Semones
176 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Fluorescence and Raman
characterization of a transport
system formed by the anti tumoral
drug emodin, silver nanoparticles
and porous silicon 1 Dep. Química Física II, Facultad de Farmacia, UCM, 28040 Madrid, Spain
2 Instituto de Estructura de la Materia, CSIC, Serrano 121, 28006 Madrid, Spain
3 Departamento de Física Aplicada, Facultad de Ciencias, UAM, 28049 Madrid, Spain
Emodin is an orange crystalline solid that belongs
to the anthraquinone family (fig. 1). It has shown
anticancer effect in breast and prostate tumors. It
presents high solubility in organic solvents but it is
insoluble in water. To overcome this limitation
design of advanced drug delivery systems are
necessary in order to deliver the drug at the target
site with the adequate rate and concentration.
Between the new materials that have recently
revealed a lot of promise in drug delivery, porous
silicon (PSi) is an interesting one (fig. 2). It is
biocompatible and biodegradable and is able to
form micro devices to carry the drugs until the site
of interaction [1-3]. If the molecules do not remain
inside the pores it is necessary to functionalize the
silicon surface. As this is the case of emodin, we
have solved the problem by using silver
nanoparticles. These metal nanostructures present
additional advantages derived from the Localized
Surface Plasmon Resonances (LSPR) they support.
The principal benefit is related with the obtaining
of surface enhanced spectroscopy such as SERS
(surface enhanced Raman scattering) and SEF
(surface enhanced fluorescence) that can be used
as potent and high sensitive techniques for
molecular detection.
Figure 1. Structure and acid-base equilibrium of emodin.
Figure 2. Cross section of a porous silicon layer.
Understanding and knowledge of the
physicochemical properties of the systems used to
transport and release the drugs constitute a
prerequisite in designing advanced drug delivery
systems. Interaction of emodin with silver
nanoparticles has been previously studied in our
group [4-5]. In the present work we have used
Raman and SEF spectroscopy to perform a
characterization of emodin adsorbed on silver
nanoparticles and loaded on PSi.
Besides optimization of pore size and impregnation
conditions of PSi, enhancement factor of
fluorescence signal of emodin has been obtained
(fig. 3). It varies between 5 and 24 for diverse
conditions used. Preliminary Raman and
fluorescence studies of other non steroidal anti
inflammatory drugs (NSAIDS), in particular
ketorolac and indomethacin, in solution and
adsorbed on silver nanoparticles will also be
presented. Conclusion collected in this study
Paz Sevilla1,2
, Margarita
Hernandez2, Gonzalo
Recio3, E. Corda
2,
Raúl J. Martín-Palma3,
José V. García-Ramos2 and
Concepción Domingo2
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constitutes a first step in the design of a new drug delivery system to be used with emodin or with other
drugs like ketorolac or indomethacin.
600 700 800 9000
5000
10000
15000
20000b)
Intensity
Wavelength (nm)
a)
Figure 3. Fluorescence spectra of nanostructured porous silicon: a) loaded with the
antitumoral drug emodin, b) loaded with the antitumoral drug emodin adsorbed on silver
nanoparticles. Excitation laser wavelength used was 532 nm. All spectra were normalized to
the Raman signal from the Si at 547 nm.
References
[1] N. J. Halas, Nanomedicine, 4 (2009) 369.
[2] R. J. Martín-Palma, M. Manso-Silván, and V. Torres-Costa, J. Nanophotonics, 4 (2010) 042502.
[3] A. Muñoz-Noval, V. Sánchez-Vaquero, V. Torres-Costa, D. Gallach, V. Ferro-Llanos, J. J. Serrano, M.
Manso-Silván, J.P. García-Ruiz, F. del Pozo, and R.J. Martín-Palma, J. Biomedical Optics, 16 (2011)
025002.
[4] P. Sevilla, F. García-Blanco, J.V. García-Ramos and S. Sánchez-Cortes, Phys. Chem. Chem. Phys., 11
(2009) 8342.
[5] R. De-Llanos, S. Sánchez-Cortés, C. Domingo, J. V. García-Ramos and P. Sevilla, J. Phys. Chem. C, 115
(2011) 12419.
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Manipulation of molecular quantum
states in an STM tunneling junction
using classical metal atom inputs
IMRE, A*STAR, 3 Research Link, 117602, Singapore
Digital logic gates are basic functional units in any
digital electronic circuit performing arithmetic logic
operations. The most straightforward approach for
improving the performance of digital logic gates is
the further miniaturization of solid state transistors
as their primordial building blocks. However those
downsizing encounters several fundamental
problems at the atomic scale, i.e. leakage currents,
heat dissipation, fabrication limitations, etc. AtMol
is a project pioneering a new proposed paradigm to
implement molecular electronics and quantum
computing. The final goal of this project is to
fabricate a fully functional molecular chip, whose
chip core will be made of atom wires
interconnecting a single logic processing molecule.
A low-temperature scanning tunneling microscope
(STM) is a very suitable tool not only for surface
science but also to investigate single molecule
electronics. STM differential conductance (dI/dV)
measurement is a very effective technique to gain
access to the low lying electronic states of single
molecules. To have access to those states, a
molecule has to be electronically decoupled or
weakly coupled, i.e. physisorbed, to the metal
surface. We present here how the electron
probability distributions of molecular states are
imaged in real space using a pentacene molecule
directly adsorbed on a gold surface. [1] STM dI/dV
conductance images taken at voltages
corresponding to the resonances near the substrate
Fermi level were found to be very close to the
mono-electronic molecular orbitals (MO), in
contrast high-order resonance states images were
composed also with MO components from low-
order resonance states. dI/dV conductance maps of
other molecules will be also presented. [2,3]
Quantum states of a molecule can be modified by
light irradiation, external fields, structural
transformation, etc. Here, we show that is possible
to manipulate the quantum states of a
trinaphthylene molecule by using classical metal
atom contacts. [4] Herein two naphthylene
branches of the trinaphthylene molecule are used
to set atom input terminals and the remaining one
functions as the signal output terminal. One Au
atom in contact with an input branch carries 1-bit
of classical information input that is converted into
quantum information throughout the molecule.
The Au-trinaphthylene electronic interactions give
rise to measurable energy shifts of the molecular
electronic states demonstrating a NOR logic gate
functionality. The NOR truth table of the single
molecule logic gate was characterized by STM dI/dV
measurements. How far the quantum information
is transferred through will also be discussed. [5]
References
[1] W –H Soe, C Manzano, A De Sarkar, N
Chandrasekhar and C Joachim, Phys. Rev. Lett. 102
(2009) 176102.
[2] W –H Soe, C Manzano, H S Wong and C Joachim, J.
Phys.: Condens. Matter (2012) in press.
[3] W –H Soe, H S Wong, C Manzano, M Grisolia, M
Hliwa, X Feng, K Müllen and C Joachim, ACS Nano 6
(2012) 3230.
[4] W –H Soe, C Manzano, N Renaud, P de Mendoza, A
De Sarkar, F Ample, M Hliwa, A M Echavarren, N
Chandrasekhar and C Joachim, ACS Nano 5 (2011)
1436.
[5] C Manzano, W –H Soe, P de Mendoza, A M
Echavarren C Joachim, to be submitted.
We–Hyo Soe
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Disorder-induced randomization of
spin polarization and interfacially
protected surface states in
three-dimensional models of
topological insulators 1 CIN2 (ICN-CSIC), Campus UAB, 08193, Bellaterra (Barcelona), Spain
2 Institució Catalana de Recerca i Estudis Avançats (ICREA), 08010, Barcelona, Spain
The growing interest on topological insulators (TI)
relies on their fascinating electronic properties,
namely, a non-trivial insulating bulk which
guarantees the formation of highly robust Dirac-like
states at the surface holding a chiral spin
texture.[1-3] This new topological phase of
condensed matter is governed by strong spin-orbit
coupling and their surface states are protected
against disorder preserving time-reversal symmetry
(non-magnetic).
Here we use a three-dimensional model of TI on a
diamond lattice, described by the Fu-Kane-Mele
(FKM) Hamiltonian,[4] and show how Dirac cone
characteristics can be tuned on opposite surfaces
upon differentiation of atomic-scale surface
terminations. In particular, when the outermost
surface layers are removed, the number of Dirac
cones in the surface Brillouin zone (SBZ) changes
from three at the three equivalent M-points to a
single one at Gamma. This result extends the
applicability of the FKM model to real TI such as the
frequently studied Bi2Se3, Bi2Te3 or Sb2Te3.
More interestingly, when opposite surfaces are
geometrically differentiated by removing the
outermost layer from only one surface, Dirac cones
develop at the M-points in one surface and at the
Gammapoint in the other and remain uncoupled
and gapless down to few bulk layers (see Fig.1(b,e)
for 11 and 3 layers thickness respectively).[5,6] Our
findings are consistent with recent experimental
observations by Bian et al.[7] and open the way to
controlled engineering of thin 3D-TI with highly
robust chiral states.
Figure 1. Band structure of slabs of various thicknesses
(layers L) and surface terminations (T1 is the default
termination and T2 is the one obtained by removing the
outermost layer as explained in the text). When opposite
surfaces are geometrically differentiated (b,e) the
surface states remain gapless down to few bulk layers.
Additionally, by introducing Anderson bulk
disorder,[8-11] we investigate the changes in the
spin texture with increasing disorder in the slab in
order to determine the extent to which the
topological protection of surface states is reduced.
As disorder strength is increased, spin polarization
becomes smaller and spread over a wider range of
vector length, evidencing randomization of the spin
texture fingerprint (see Fig. 2; blue and red arrows
correspond to the clean and disordered cases
respectively). Our findings suggest ways to analyze
the bulk crystalline quality of TI by inspecting the
spin texture features through spin-resolved ARPES
experiments.
David Soriano1,
Frank Ortmann1 and
Stephan Roche1,2
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Figure 2. Spin texture of a T2-T2 slab (12 layers) in
presence (red) and in absence (blue) of bulk Anderson
disorder. The randomization of the spin texture in
presence of bulk disorder is evident.
Acknowledgements. This work is supported by the
TRAIN2 project of the SUDOE Territorial
Cooperation Programme.
References
[1] J. E. Moore, Nature, 464 (2010) 194.
[2] [2] M. Z. Hasan and C. L. Kane, Rev. Mod.
Phys., 82 (2010) 3045.
[3] X.-L. Qi and S.-C- Zhang, Rev. Mod. Phys., 83
(2011) 1057.
[4] L. Fu, C. L. Kane and E. J. Mele, Phys. Rev. Lett.,
98 (2007) 106803.
[5] Y. Zhang, C.-Z. Chang, C.-L. Song, L.-L. Wang, X.
Chen, J.-F. Jia, Z. Fang, X. Dai, W.-Y. Shan, S.-Q.
Shen, Q. Niu, X.-L. Qi, S.-C. Zhang, X.-C. Ma and
Q.-K. Xue, Nature, 464 (2010) 194.
[6] A. A. Taskin, S. Sasaki, K. Segawa and Y. Ando,
arXiv:1204.1829.
[7] G. Bian, X. Wang, Y. Liu, T. Miller and T. C.
Chiang, Phys. Rev. Lett., 108 (2012) 176401.
[8] A. M. Black-Schaffer and A. V. Balatsky, Phys.
Rev. B, 85 (2012) 121103(R).
[9] G. Schubert, H. Fehske, L. Fritz and M. Vojta,
Phys. Rev. B, 85 (2012) 201105(R).
[10] J. Henk, A. Ernst, S. V. Eremeev, E. V. Chulkov,
I. V. Maznichenko and I. Mertig, Phys. Rev.
Lett., 108 (2012) 206801.
[11] H. Beidenkopf, P. Roushan, J. Seo, L. Gorman, I.
Drozdov, Y. S. Hor, R. J. Cava and A. Yazdani,
Nature Phys., 7 (2011) 939.
[12] D. Soriano, F. Ortmann and S. Roche
(submitted)
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 181
Atomically precise construction and
electronic properties of dangling-
bond nanostructures on hydrogen
passivated Ge(001) surface 1 Centre for Nanometer-Scale Science and Advanced Materials (NANOSAM),
Department of Physics, Astronomy, and Applied Computer Science, Jagiellonian
University, Reymonta 4, PL 30-059, Krakow, Poland 2 Institute of Materials Research and Engineering, 3 Research Link,
Singapore 117602, Singapore 3 Department of Chemical and Biomolecular Engineering, National University of
Singapore, 4 Engineering Drive 4, Singapore 117576, Singapore 4 Nanosciences Group & MANA Satellite, CEMES-CNRS
29 rue Jeanne Marvig, F-31055 Toulouse, France
We report on studies concerning preparation of
well organized atomic wires and 2D nanopads by
tip-induced hydrogen desorption from hydrogen
passivated Ge(001) surface. Dangling-bond (DB)
nanostructures on the passivated surface are
fabricated using atomically precise STM tip-induced
dimer-by-dimer hydrogen desorption. We have
developed new, very efficient protocol allowing for
at will fabrication of pre-designed DB structures.
Their geometrical structure is characterized with
atomic resolution by means of LT-STM. High
resolution STM images of wires of different
orientation and lengths are in good agreement with
ESQC/SGFM calculations. Furthermore, the
electronic properties of the fabricated
nanostructures are examined by scanning tunneling
spectroscopy (STS) measurements allowing for
acquisition of the density of states spatial
distribution, which can be measured successfully
with a lateral resolution reaching an individual
dangling-bond. Deeper understanding of
experimental observations is provided by
calculations of surface electronic structure and
electron transport properties performed with semi-
empirical method fitted to first principles density
functional theory (DFT). Based on the example of
short DB wires we discuss the effect of through
surface and through space electronic coupling
between the created DBs, which results in
narrowing of the surface band gap with increasing
DB wire length.
Marek Kolmer1,
Szymon Godlewski1,
Bartosz Such1,
Hiroyo Kawai2,
Mark Saeys2,3
,
Christian Joachim2,4
and
Marek Szymonski1
182 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Efficient biexciton emission
in single CdSe nanocrystals
LP2N, Université de Bordeaux, Institut d’Optique Graduate School & CNRS,
351 cours de la libération, 33405 Talence, France
Quantum-confined nanoparticles have been
increasingly investigated over the past decade due
to the superior efficiency and tunability of their
emission wavelength from the ultraviolet to the
near infra red. Among those nanoparticles, colloidal
CdSe nanocrystals (NC) are particularly attractive
for many applications such as nanoscale
electronics, laser technology, quantum
cryptography, and biological fluorescent labeling.
A detailed understanding of the NCs band-edge
exciton fine structure is crucial for these
applications. While intensive experimental and
theoretical work has been performed to describe
the size dependence of the exciton fine structure in
nearly spherical NCs, the shape dependence has
received much less attention despite recent
advances in NC growth methods which lead to a
greater control over shape distribution. Pioneering
theoretical and experimental investigations [1, 2]
have indicated that the shape dependence of NCs
can be as important as the size dependence in
terms of tuning their electronic and optical
properties. The elucidation of these shape effects
remains an experimental challenge which can be
addressed by the optical study of individual NCs,
where ensemble averaging over shape and size
distributions is suppressed.
Shape and size effects also govern the optical
response of NCs in the multiexcitonic regime,
where potential applications such as optical gain
are envisaged [3]. Despite the important role that
biexcitons play in the optics of NCs, it has been
practically impossible to observe the biexciton
recombination line in the PL of CdSe NCs under
continuous wave excitation, because of efficient
nonradiative Auger recombination [4].
This presentation will be focused on our recent
magneto-optical and time-resolved spectroscopic
investigations of single commercial qdot655
streptavidin conjugates NCs (comprising a core of
CdSe capped by a ZnS layer) as a function of
temperature. The remarkable photostability of
these NCs at low temperature led us to unveil the
spectral and temporal signatures of the emission
from the lowest exciton-fine-structure states [5,6],
trion emission [7] and biexciton emission [8].
Because of the NCs shape distribution, we find
various band-edge exciton fine structures that are
consistent with theoretical predictions for
elongated NCs. Furthermore, contrarily to what
was anticipated for “standard” CdSe-based core
shell NCs, we show evidence for spectral and
temporal signatures of highly efficient radiative
biexcitonic recombinations in this type of NCs.
Special attention will also be paid to the attractive
trion (charged exciton) emission properties for
potential applications in quantum information
processing.
References
[1] A. L. Efros et al., Physical Review B 54, 4843
(1996).
[2] J. T. Hu et al., Science 292, 2060 (2001).
[3] V. I. Klimov et al., Science 290, 314 (2000).
[4] V. I. Klimov et al., Science 287, 1011 (2000).
[5] L. Biadala et al., Physical Review Letters 103,
037404 (2009).
[6] L. Biadala et al., Physical Review Letters 105,
157402 (2010).
[7] Y. Louyer et al., Applied Physics Letters 96,
203111 (2010).
[8] Y. Louyer et al., Nano Letters 11, 4370 (2011).
Philippe Tamarat,
Yann Louyer, Mark Fernée,
Louis Biadala and
Brahim Lounis
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Figure 1. Emission spectrum of a single CdSe/ZnS nanocrystal at 2 K, showing evidence for strong radiative biexciton
recombination.
184 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Microemulsions as reaction media
for the synthesis of bimetallic
nanoparticles
Physical Chemistry Department, University of Vigo, E-36200 Vigo, Spain
Bimetallic nanoparticles are particularly attractive
due to their properties often differ markedly from
either of the constituent metals. Nowadays it is well-
known that the design and control of spatial
arrangement of both metals in bimetallic
nanoparticles are critical for exploiting their
potential applications. The properties of bimetal
nanoparticles strongly depend on their size,
structure and morphology, so it is of the utmost
importance to fully elucidate the mechanism
underlying the nucleation and growth of
nanoparticles. The fact that the nucleus evolves to a
particle by accumulating new layers implies that the
differences in nucleation rates of both metals would
strongly affect the metals segregation and final
nanoparticle sizes.
Because the synthetic route seems to be crucial to
determine final sizes and structures of bimetallic
nanoparticles, our study is focused on a concrete
method: the reverse microemulsion route. This
method is one of the most important methods to
control the particle size, because the surfactant-
stabilized droplets provide a microenvironment for
the preparation of nanoparticles by exchanging their
contents and preventing the excess aggregation of
particles. But microemulsion itself is a very
complicated system, and the dynamics of
intermicellar exchange plays an important role in the
kinetics [1, 2]. In line with our ongoing effort to study
the formation of simple and bimetallic nanoparticles
in microemulsions, we have aimed here to
investigate the nucleation and growth of bimetallic
nanoparticles and to provide a detailed insight into
the factors affecting nanoparticle structure and size.
The main concept used to describe nucleation is
related to the critical radius. Above this size, it is
favorable for the new phase to form; below this size,
the clusters will tend to dissolve rather than grow.
Monte Carlo simulations were carried out to
investigate the influence of critical nucleus sizes on
the structure and sizes of final bimetallic
nanoparticles. Because bimetallic particles are
composed by two different metals (A and B), which
can need a different minimum number of atoms to
form a stable nucleus, the algorithm distinguish two
critical nucleation numbers (nA* and nB*). In addition,
the possibility of heterogeneous nucleation (nucleus
composed by different metals) has also been
considered by including a new parameter (nAB*),
defined as the minimum number of metal atoms (A
or B) inside the same droplet needed to form a
heterogeneous nucleus capable of further growth.
In relation to the nanoparticle structure, core-shell
structures are expected when one metal reduces
faster than the other [3]. The study reveals that,
keeping equal the reduction rates of the two metals,
the final structure is also sensitive to changes in the
critical nucleus numbers, because these parameters
determine the rate of nucleation. Figure 1A shows
simulation results using equal reduction rates, a low
value of concentration (⟨cA⟩=⟨cB⟩=4 molecules of
reactant per droplet), a rigid film (f=5, kex=1) and
different critical nucleus sizes (nA* =1, nB* =9, nAB*
=4). In this figure the number of particles containing
different percentages of one of the metals (A: faster
nucleation metal) is monitored from the
nanoparticle core to the outside (layer by layer). One
can observe that the inner layers are composed by
the metal which nucleates faster, and composition
shows a progressive improvement towards a mix of
both metals as the process advances (from the inner
to the outer layers). Finally, the outer layers show an
enrichment in the slower nucleation metal.
Therefore this kind of structure can be considered a
core-shell, although it was obtained simulating two
metals with the same reduction rate. An increase in
the difference between nucleation rates of both
C. Tojo and F. Barroso
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metals gives rise to a better segregation of metals in
the final nanoparticle. Likewise, as long as the
formation of heterogeneous seeds is faster, the
degree of alloying is greater. In addition, it is
observed that the difference in nucletion rates of
both metals is not the only parameter to determine
the metals segregation, playing the interdroplet
channel size a relevant role. In agreement with
experimental observations, the results also suggest
that the metal segregation can be avoid by using a
more flexible surfactant (see figure 1). These results
allow us to tune the experimental conditions for
designing specific bimetallic structures.
In relation to the nanoparticle sizes, three different
experimental behaviours have been found:
bimetallic nanoparticles can be significatively smaller
(negative deviation [4-7]), larger (positive deviation
[8]) or equal than individual monometallic
nanoparticles (no deviation [9, 10]). Because these
results were ascribed to a difference in the
nucleation process, we have carried out computer
simulations to study how nanoparticle sizes change
by using different combinations of the three critical
nucleus numbers. Our results show that a negative
deviation is obtained when heterogeneous critical
size nAB*, is smaller than the two homogeneous ones
(nA* and nB*), i.e., heterogeneous nucleation rate is
the fastest nucleation. On the contrary, to obtain
positive deviations the heterogeneous nucleation
must be slower than the homogeneous ones. Both
kind of deviations were obtained only if a rigid
surfactant film was used. Also relevant to the
discussion is the observation that no kind of
deviation could be obtained when different
reduction rates ratios were simulated. Therefore,
the only factor affecting nucleation which can
explain the sizes deviations is the different rate in
heterogenous and homogeneous nucleation. Direct
comparison between experimental and simulation
results is not possible, because to the best of our
knowledge, no experiment has ever directly
measured the size of the critical nucleus.
The simulation results are expected to contribute to
developing advanced strategies for the design
nanostructured particles.
References
[1] R.P. Bagwe, K.C. Khilar, Langmuir, 16 (2000) 905.
[2] M.A. López-Quintela, C. Tojo, M.C. Blanco, L.
García-Río, J.R. Leis, Curr. Opin. Colloid Interface.
Sci., 9 (2004) 264.
[3] C. Tojo, M. de Dios, M.A. López-Quintela, J. Phys.
Chem. C, 113 (2009) 19145.
[4] M. Wu, D. Chen, T. Huang, Langmuir, 17 (2001)
3877.
[5] A. Habrioux, W. Vogel, M. Guinel, L. Guetaz, K.
Servat, B. Kokoh, N. Alonso-Vante, Phys. Chem.
Chem. Phys., 11 (2009) 3573.
[6] M. Wu, D. Chen, T. Huang, Chem. Mater., 13
(2001) 599.
[7] M. Wu, L. Lai, Coll. Surf.A, 244 (2004) 149.
[8] J. Santhanalakshmi, P. Venkatesan, J. Nanopart.
Res., 13 (2011) 479.
[9] L.M. Magno, W. Sigle, P.A.v. Aken, D.G.
Angelescu, C. Stubenrauch, Chem. Mater., 22
(2010) 6263.
[10] F.J. Vidal-Iglesias, J. Solla-Gullón, V. Montiel, J.M.
Feliu, A. Aldaz, J. Power Sources, 171 (2007) 448.
Figure 1. Number of particles versus the percentage of one of the products (A), from the nanoparticle
core to the outside (layer by layer) using different surfactant flexibilities, and remaining constant
critical sizes (nA* =1, nB* =9, nAB*=4), concentration ⟨cA⟩=⟨cB⟩=4, ⟨cR⟩=8, and reduction rates vA=vB.
0
50
100
150
200
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8910
number of particles
layers
% metal A
A
f=5
B
f=30 C
f=90
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20
30
40
50
60
70
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layers
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20
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layers
% metal A
B
f=30C
f=90
very flexible filmflexible film
rigid film
186 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Small molecule organic
photovoltaics at the nanoscale
McGill University, Montreal, Canada
Organic photovoltaics (OPVs) are a sustainable
method of solar energy harvesting with possible
fabrication advantages over more developed
inorganic semiconductor solar cells. However, the
power conversion efficiency of OPV devices is
currently about 8.6%, compared to over 20% for
crystalline silicon and up to 43.5% for triple junction
inorganic solar cells [1-4]. The structure of solar
harvesting device active layers is crucial to
performance [5-7], but little is currently known
about the specific loss mechanisms responsible. We
present a preliminary study of structure-function
relationships in thin films of organic photovoltaic
materials by simultaneous non-contact atomic
force microscopy (NC-AFM) and Kelvin probe force
microscopy (KPFM).
Thin films of small electron donor and electron
accepter molecules were thermally evaporated on
KBr (001) surfaces under ultra-high vacuum. Local
contact potential difference and topography were
mapped with simultaneous KPFM and NC-AFM to
investigate corresponding optoelectronic and
structural properties at the nanometre scale. Light
may be coupled into the UHV AFM system to
illuminate samples during imaging, thus allowing
characterization of active OPV materials during the
generation of excitons and charge carriers. Our
early results demonstrate that combined NC-AFM
and KPFM is a powerful approach to studying
fundamental physical processes in photovoltaic
power generation. Understanding structure-
function relationships in OPVs will contribute to the
advancement of renewable energy light harvesting
devices that are clean, efficient and affordable.
Figure 1. Illustration depicting possible structure-
dependent OPV efficiency loss mechanisms under
investigation. (a) Charge flow dependent on molecular
anisotropy and bottleneck structure, (b) recombination
loss structure and the influence of defects.
References
[1] L. Kazmerski, Best Research-Cell Efficiencies Report, National Renewable Energy Laboratory (2011).
[2] S. H. Park, A. Roy, S. Beaupre, S. Cho, N. Coates, J.S. Moon, D. Moses, M. Leclerc, K. Lee, A.J. Heeger,
Nature Photonics 3 (2009) 297.
[3] Y. Liang, Z. Xu, J. Xia, S.T. Tsai, Y. Wu, G. Li, C. Ray, L. Yu, Adv. Mater. 22 (2010) E135.
[4] Martin A. Green, Keith Emery, Yoshihiro Hishikawa and Wilhelm Warta, Prog. Photovolt: Res. Appl. 18
(2010) 346.
[5] P.G. Nicholson and F.A. Castro, Topical Review, Nanotechnology 21 (2010) 492001.
[6] A. Liscio, V. Palermo and P. Samori, Accounts of Chemical Research 43 (2010) 541.
[7] D.C. Coffey and D.S. Ginger, Nature Materials 5 (2006) 735.
J.M. Topple,
Z. Schumacher,
A. Tekiel and P. Grutter
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Figure 2. Volmer-Weber growth of islands of CuPc (electron donor) and PTCDI (electron
accepter) molecules on KBr (001). (a,c) 3D-rendered topography imaged by NC-AFM,
(b,d) local contact potential difference imaged by KPFM.
188 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Atomistic models of charge
separation and recombination in
organic photovoltaics interfaces
Department of Chemistry,
University of Warwick, U.K.
The key process in organic photovoltaics cells is the
separation of an exciton, close to the
donor/acceptor interface into a free hole (in the
donor) and a free electron (in the acceptor). In an
efficient solar cell, the majority of absorbed
photons generate such hole-electron pairs but it is
not clear why such a charge separation process is
so efficient in some blends (for example in the
blend formed by poly(3-hexylthiophene) (P3HT)
and a C60 derivative (PCBM)) and how can one
design better OPV materials. The electronic and
geometric structure of the prototypical
polymer:fullerene interface (P3HT:PCBM) is
investigated theoretically using a combination of
classical and quantum simulation methods. It is
shown that the electronic structure of P3HT in
contact with PCBM is significantly altered
compared to bulk P3HT. Due to the additional free
volume of the interface, P3HT chains close to PCBM
are more disordered and, consequently, they are
characterized by an increased band gap. Excitons
and holes are therefore repelled by the interface.
This provides a possible explanation of the low
recombination efficiency and supports the direct
formation of “quasi-free” charge separated species
at the interface. This idea is further explored by
using a more general system-independent model
Hamiltonian. This talk will discuss how and when a
combination of computational and theoretical
models can truly contribute to organic electronics
and will provide few examples of genuine material
properties predictions based on computational
models.
References
[1] T. Liu, D.L. Cheung and A. Troisi A, Phys. Chem.
Chem. Phys. 2011, 13, 21461.
[2] D.P. McMahon, D.L. Cheung, Troisi A, J. Phys.
Chem. Lett. 2011, 2, 2737.
[3] A. Troisi, Chem. Soc. Rev. 2011, 40, 2347.
[4] A. Troisi, Organic Electronics 2011, 12, 1988.
Alessandro Troisi, Tao Liu,
Domenico Caruso,
David L. Cheung and
David P. McMahon
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Present and perspectives on
dissemination and training in
nanotechnology in IberoAmerica:
Red NANODYF – CYTED
Mechanical Engineering Department, ETSI-ICAI Universidad Pontificia Comillas
Coordinator of NANODYF Network, Area 6 Science and Society, CYTED Program
Promoting the assimilation of contents of Nanotechnology involves action in dissemination, and formal
education in schools and universities. Iberoamerican countries have not specific plans in this important line
of action, which will result in a delay of their citizens compared to other regions. IberoAmerica cannot be
excluded from this process of dissemination and training in Nanotechnology because the future economy
trends will be structured around advances in nanotechnology, and because there is already a significant
Iberoamerican presence in research and development in Nanotechnology. So, that is the purpose and
mission of the "Jose Roberto Leite" Network of Dissemination and Education in Nanotechnology (NANODYF)
from the CYTED Program, which in its first year of work (2011) has detected what the current state of the
Outreach and Training nanotechnology in a group of countries representing the Iberoamerican region is; and
it aims to draw a future strategy to improve and enhance areas that are weak or even absent in the region.
Joaquín Tutor Sánchez
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Superconductivity at
adatom/molecule-induced silicon
surfaces and interfaces National Institute for Materials Science,
1-1, Namiki, Tsukuba, Ibaraki 305-0044, Japan
The state-of-the-art nanotechnology has enabled
fabrication of ultrathin superconductors of high
crystallinity and with atomically controlled
thicknesses and interfaces. This has opened ways to
tune superconductivity [1,2] and to investigate the
thinnest crystalline layers for its emergence [3,4]. Notably, superconductivity was found to exist for
silicon surface reconstructions with metal adatoms
[5], which are the ultimate forms of thin epitaxial
films. This finding is, however, based on
spectroscopic evidence of superconducting energy
gaps observed by scanning tunneling microscopy
(STM). The very existence of supercurrent through
these surfaces has not been clarified yet and
important information such as critical current
density has been missing.
We have performed direct and macroscopic
electron transport measurements on a silicon
surface reconstruction with In adatoms (Si(111)-
(√7×√3)-In) in UHV at low temperatures [6]. The
superconducting transition is evidenced by
observations of the zero resistance state and of I −
V characteristics exhibiting sharp and hysteretic switching below 2.8 K ( ≡ Tc) (see Fig.1 and Fig.2).
This macroscopic supercurrent also shows a
significant robustness; the two-dimensional (2D)
critical current density J2D,c is estimated to be as
high as 1.8 A/m at 1.8 K. If the thickness of Si(111)-
(√7×√3)-In is assumed to be double the covalent
radius of In (= 0.30 nm), this corresponds to a 3D
critical current density of 6.1×109 A/m2, comparable to those of practical bulk
superconductors. The precise values of Tc and J2D,c
are dependent on sample preparation, suggesting
the importance of crystallinity of the surface
reconstruction layer. The observed temperature
dependence of critical current density J2D,c indicates
that the surface atomic steps serve as strongly
coupled Josephson junctions. The analysis based on
the Josephson junction model using the standard
Ambegaokar-Baratoff equation [7] allows us to
obtain the resistance of the atomic step. The value
is found to be consistent with that deduced from normal sample resistance.
Figure 1. Temperature dependence of zero bias
dependence of the Si(111)-(√7×√3)-In reconstruction.
The insets show the configurations of the four-terminal
measurements and an STM image of the sample surface.
The present study demonstrates that various
surface reconstructions of silicon and related
semiconductors could be used as practical
superconducting materials. To achieve this aim,
however, the surface metal-adatom layer should be
passivated and buried under a capping layer while the superconductivity remains intact, which poses a
new technical challenge. We present a trial for
passivation of surface superconducting layer with
molecular assembly [8]. We find that Co-
phthalocyanine molecules can be assembled in a
Takashi Uchihashi
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highly ordered fashion on the Si(111)-( √7×√3)-In
surface by a simple sublimation method, while the
resulting layer still exhibits a signature of
superconducting transition. The fabrication of a molecular interface could also be used to tune the
properties of superconductivity by modifying the
phonon spectrum and by introducing magnetic
moments into molecules [9].
Figure 2. Temperature dependence of I-V characteristics
of the same sample, from which critical current Ic can be
determined. The inset shows that temperature
dependence of Ic.
References
[1] Y. Guo et al., Science 306 (2004) 1915.
[2] M. M. Özer et al., Nature Phys. 2 (2006) 173.
[3] S. Qin et al., Science 324 (2009) 1314. [4] C. Brun et al., Phys. Rev. Lett. 102 (2009)
207002.
[5] T. Zhang et al., Nature Phys. 6 (2010) 104.
[6] T. Uchihashi et al., Phys. Rev. Lett. 107, 207001
(2011); also see Viewpoint in Physics 4, 92
(2011).
[7] V. Ambegaokar and A. Baratoff, Phys. Rev.
Lett. 10 (1963) 486.
[8] B. N. Cotier et al., Appl. Phys. Lett. 78 (2001)
126. [9] T. Gang et al., Nature Nanotech. 7 (2012) 232.
192 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Microstructural change of li(NiCo)O2
based materials of Li ion battery
during charge and discharg
TOYOTA Central Research & Development Laboratories Inc.,
480-1192 Yokomichi, Nagakute, Aichi Japan
1. Introduction
During charge and discharge of lithium-ion
batteries with Li(NiCo)O2 based positive active
materials, electrochemical reaction with lithium
intercalation /deintercalation proceeds reversibly.
The performance of Li(Ni,Co)O2 materials has been
studied by many authors. For example, we have
reported the fading mechanism of lithium ion
batteries with on LiNi0.8Co0.15Al0.05O2 as the positive
material and pointed out that the reaction and
diffusion resistances of positive electrode
drastically increased during durability test at high
temperatures. It was revealed that the
microstructural change of positive material played
a important role for resistance increase. In this
presentation, the microstructural change of
LiNi0.8Co0.15Al0.05O2 material investigated by various
methods, such as electrochemical techniques,
STEM, EELS, and XAFS. The cylindrical cells (18650-
type) of LiNi0.8Co0.15Al0.05O2 and artificial graphite
with carbonate electrolyte were used for durability
tests at high temperatures. The electrodes taken
out of the cells before and after durability tests
were evaluated by using various methods. The
LiNi0.8Co0.15Al0.05O2 materials before and after 1
cycle were also evaluated by STEM-EELS to
compare with the materials after long durability
test.
2. STEM analysis
The microstructural change near grain boundaries
before and after 1 cycle observed by using low
magnification STEM is shown in Fig.1. The grain
boundaries have thin grain boundary layers which
produce bright contrast indicate by arrows in Fig.1
(a). As shown in this figure, the thickness of some
grain boundary layers (indicated by arrows in b)
increased drastically and some microcracks are
found at triple points and grain boundaries.
According to the observation by high resolution
STEM, EELS and ED, it was revealed that the crystal
structure changes from ordered layer structure
(bulk) to disordered rock-salt structure (surface)
through partially ordered structure. The thickness
of grain boundary layer changed from about 5 nm
before first cycle to about 25 nm after first cycle.
This means that phase transition occurred
especially near at grain boundary (surface) during
intercalation / deintercation of lithium.
Figure 1. Low magnification STEM images fresh (a) and
after first cycle. The thickness of the grain boundary
layer (white contrast indicate by arrows) increased
drastically after first cycle [8].
3. XAFS analysis
The determination of the Ni valence before and
after durability test was conducted by using XAFS
method. The Ni K-edge spectra (XANES) after
durability test are shifted to lower energy. Fig.2
shows Ni valence determined by the energies from
the half-step heights of the Ni K-edge spectra as a
function of x in Li1-xNi0.8Co0.15Al0.05O2. As shown in
this figure, the Ni valence after durability test
Yoshio Ukyo, Yoji Takeuchi
and Yoshinari Makimura
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decreased, especially near surface (CEY).In my
presentation, the fading mechanism of Li-ion
battery with Li1-xNi0.8Co0.15Al0.05O2 will be discussed
in detail based on the results obtained.
Figure 2. The dependence of Ni valence before and after
cycle test at high temperature on SOC (x in
Li1-xNi0.8Co0.15Al0.05O2) [2].
References
[1] Y. Itou et al, J. Power sources, 146 (2005) 39.
[2] T. Nonaka et al, J. Electrochem. Soc., 154
(2007) A353.
[3] T. Sasaki et al, J. Electrochem. Soc., 154 (2007)
A289.
[4] S. Muto et al, J. Electrochem. Soc., 154 (2007)
A371.
[5] T. Sasaki et al, J. Electrochem. Soc., 158 (2011)
A1214.
[6] T. Nonaka et al, J. Power sources, 162 (2006)
1329.
[7] H. Kondo et al, J. Power sources, 174 (2007)
1131.
[8] S. Zheng et al, J. Electrochem. Soc., 158 (2011)
A357.
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Monitoring the oxygen content in
graphene oxide
Universidad de Alicante, 1Chemical Engineering Department,
University of Alicante, 03080 Alicante, Spain
The chemical derivation of graphene oxide
emerged as an easy route to obtain atomically thin
carbon sheets with the aim to obtain graphene in a
large scale. This graphene oxide (G-O) is decorated
with different oxygen groups that disrupt the
electronical properties of pristine graphene. The
real structure of graphene oxide has not yet been
fully understood, same as its predecessor, the
graphite oxide, which has been studied over
hundred years. Most of the studies, based in bulk
analysis of the graphene oxide such as TGA or XPS,
stated C/O ratios of 2:1 and variable oxygen
contents that range from 20 to 33% [1].
We have developed a particular synthesis method
to produce graphene oxide from helical ribbon
carbon nanofibers (HR-CNF). Our studies of the
quantification of the oxygen content comprised XPS
and TGA of the bulk powder and EDS and EELS of
single G-O sheets. XPS results were consistent with
the literature providing C/O ratios up to 2, while
the analysis of the sheets showed much less oxygen
content and, therefore, a higher C/O ratio. This
difference between the bulk and the sheet analysis
agrees with some recent studies that state that
most of the oxidation of the graphene oxide is due
to some debris attached to the sheets and not to
the oxygen covalently bonded [2].
This revelation indicates that the existing models of
graphene oxide, based on the results of bulk
analysis, should be submitted to debate. The
knowledge of the structure could lead to a better
enhancement of the properties of the graphene
oxide.
Here, we monitor by different techniques the
oxygen content in powder and exfoliated samples
of graphene oxide. We tried to find the
composition if a single graphene oxide sheet and
compared it with the content in the all bulk.
References
[1] Bagri, A., C. Mattevi, M. Acik, Y.J. Chabal, M.
Chhowalla, and V.B. Shenoy, Structural
evolution during the reduction of chemically
derived graphene oxide. Nat Chem, 2010. 2(7):
p. 581-587.
[2] Rourke, J.P., P.A. Pandey, J.J. Moore, M. Bates,
I.A. Kinloch, R.J. Young, and N.R. Wilson, The
Real Graphene Oxide Revealed: Stripping the
Oxidative Debris from the Graphene-like
Sheets. Angewandte Chemie International
Edition, 2011. 50(14): p. 3173-3177.
Helena Varela-Rizo,
Iluminada Rodriguez-
Pastor, Gloria Ramos-
Fernández
Ignacio Martín-Gullón
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Postsynthetic asymmetric transformation
of boronic-acid-protected gold
nanoclusters studied by magnetic
circular dichroism (MCD) and electronic
circular dichroism (ECD)
Graduate School of Material Science, University of Hyogo, Hyogo 678-1297, Japan
Investigations of monolayer-protected metal
nanoclusters, possessing typically less than 100 atoms, are
largely motivated in the past decade due to their
intriguing size-dependent physicochemical properties.
Much attention is recently paid on inducing chirality in
metal nanoclusters owing to their widespread catalytic
use of chirally-modified metal surfaces. Postsynthetic
asymmetric transformation is one of the notable
techniques for facile control of symmetry-breaking [1].
Our approach here is to use gold nanoclusters bearing an
achiral boronic acid group that can bind to chiral cis-diols
such as fructose [2]. In addition, we also apply magnetic
circular dichroism (MCD) spectroscopy to gain a better
understanding of the nanoclusters’ electronic structures
as well as their chiroptical signals induced by their surface
fructose complexation. A relationship between the MCD
and normal (induced) CD responses is also examined, both
of which distinctly stem from the cluster’s electronic
transitions. We also find that this asymmetric induction is
pH-sensitive, suggesting that the gold cluster-fructose
complex formation has a great advantage for some
biological applications.
We synthesized 3-mercaptophenylboronic acid (3-MPB)-
protected gold clusters with a mean core diameter of 1.1
nm (gel fractioned), and examined their electronic
absorption, MCD and chiroptical responses induced by the
reaction of boronic acid-chiral fructose binding (Figure 1).
Note that the mean core size of the cluster was
determined by a solution-phase SAXS measurement.
Figures 2a and 2b show absorption and MCD spectra (at a
magnetic field of –1.6 T) of the gold nanocluster
compound in methanol/aqueous buffer (pH = 10.0)
mixture, respectively. It is well known that small gold
nanoparticles (< ~2 nm) no longer support the plasmon
excitation characteristic, so the structured absorption
comes from molecule-like electronic transitions. On the
other hand, the MCD spectrum shows overall positive
features in the metal-based electronic transition region at
–1.6 T. The MCD signals were very weak at > ~500 nm,
probably arising from transitions out of the HOMO into
LUMO (essentially intraband transitions), whereas
relatively strong MCD signals were detected at higher
energy transitions (< ~500 nm) that involve more or less
character of thiolate ligands. Hence it is expected that the
MCD responses of the thiolate-protected gold clusters
would primarily arise from the electronic state mixing of
the ligands and gold atoms. Note that the sign of the MCD
signal was completely reversed when the field is switched
(+1.6 T), confirming that signatures are not from an
experimental artifact but originate from real MCD signals.
Based on the MCD features, we deem that magnetic field-
induced mixing of electronic states of the ligands and
surface gold atoms would bring about the Faraday B-term,
because (i) a ground-state Zeeman splitting (at H = 1.6 T)
is in the order of 0.2 meV (if present), smaller than the
energy of room temperature (~26 meV), so the C-term
contribution should be trivial; (ii) the MCD response does
not contain any derivative line shape with respect to the
absorption peak, so the A-term contribution would be also
negligible [3].
Figure 1. Reaction scheme for the postsynthetic binding
between surface 3-MPB and chiral fructose bearing diols in
basic solution.
Figure 2. Absorption and MCD spectra (at -1.6 T) of the gold
nanocluster compound. Deconvoluted Gaussian band fits of
the electronic absorption and MCD spectra are also shown.
Hiroshi Yao and
Masanori Saeki
196 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
TNT2012
Ab
st
ra
ct
s
We next performed spectral deconvolution analysis of
both the absorption and MCD data to quantitatively
estimate accurate transition energies and their spectral
linewidths in the nanocluster since the MCD features
must correspond to electronic transitions (even
unresolved) in the electronic absorption. The Gaussian
fits of MCD as well as electronic absorption spectra are
also shown in Figure 2. For deconvoluting the
experimental data, we assumed that the analysis is
constrained by the requirement that a “single set” of
Gaussian components be used for the fitting of both
the absorption and the MCD spectra. For the excellent
(satisfactory) agreement between the measure and
calculated spectra, eight Gaussian components were
necessary. Importantly, the two different spectral
patterns have made the spectral deconvolution
analysis successful.
The pristine gold nanocluster had no optical activity.
However, D-/L-fructose addition to the nanocluster
solution altered CD responses. Figure 3a shows the CD
spectra of the gold nanocluster compound in the
presence of D-/L-fructose at pH=10.0. Note that
fructose did not induce significant absorption changes
of the gold nanocluster, strongly indicating that
complexation between the surface 3-MPB ligand and
chiral fructose hardly influenced the electronic states of
the clusters, and consequently, the gold core
rearrangement or size growth was unlikely to take
place upon complexation. On the other hand, the
nanocluster showed an appreciable Cotton effect with
complicated coupling patterns when complexed with
D- or L-fructose (that is, asymmetric induction).
Additionally, an almost perfect mirror-image
relationship was obtained in the region of metal-based
electronic transitions, implying enantiomeric
complexation.
To gain a better understanding of the structure (shape)
of CD spectra, we compare them with the peak-
separated bands obtained by the deconvolution
analysis. Figure 3b shows the induced CD and the
deconvoluted absorption spectra of the gold
nanocluster with D-fructose (10–3
M) plotted against
energy in wavenumber. For the guide of eyes, vertical
dash lines are drawn at the same energy positions. The
induced CD response is distinctly related to the peak-
separated bands; for example, the deconvoluted
spectra of 2, 3, 5, 6, and 7 exhibited negative, positive,
negative, positive, and negative peaks in the CD
response, respectively (see Figure 3b). The band 4
showed (+/–) split-type CD signal, implying an
interaction between the inclusive electronic transitions.
The spectrum 1 (the lowest energy component) seems
to be CD silent. In conclusion, the induced CD
signatures can be successfully correlated with the
isolated (separated) electronic transitions obtained by
deconvolution analysis based on the absorption and
MCD spectra. This spectral analysis is expected to
benefit better understanding of the electronic states
and the origin of the optical activity in chiral metal
nanoclusters.
Figure 3. (a) Effects of D-L- fructose on the CD spectrum of
the 3-MPB-protrctrd gold nanocluster in the methanolic
base solution. Green and red curves indicate the spectra
obtained upon addition of D- and L-fructose, respectively.
Mirror imagen relationship can be seen between them. (b)
Electronic absorption and CD spectra of the gold cluster in
the presence of chiral D-fructose (10-3
M). The data were
plotted against wavenumber. The deconvoluted spectra
with Gaussian function are also shown for ease of
comparison. (c) CD spectra of the nanocluster in the
presence of D-/L-fructose (10-3
M) in the methanolic acid
solution (pH = 1.68). Green and red curves indicate the
spectra obtained upon addition of D- and L-fructose,
respectively.
At the end, to confirm that the induced CD responses
are controllable by external parameters, we examined
pH-dependent optical activity of the 3-MPB-protected
gold cluster in the presence of chiral fructose. The
binding constant of the anionic boronate-diol is very
much larger than that of the neutral boronic acid-diol
[2], so that significant decomposition of the complexes
is highly expected in acidic conditions. Figure 3c shows
(induced) CD spectra of the gold nanocluster
compound in the presence of D-/L-fructose (10–3
M) in
methanol/aqueous oxalate buffer (pH=1.68). In
contrast to Figure 3a, no CD signals were detected,
suggesting no complexation of surface 3-MPB moieties
with chiral fructose. Interestingly, optical activity of the
gold nanoclusters can be simply controlled by external
parameters such as the pH value. This method will be a
powerful strategy to quantitatively induce optical
activity in a controlled manner.
References
[1] Yao, H. Kitaoka, M.; Sasaki, A. Nanoscale, 4
(2012) 955.
[2] Yao, H.; Saeki, M.; Kimura, K. J. Phys. Chem. C,
114 (2010) 15909.
[3] Stephens, P. J. Ann. Rev. Phys. Chem., 25 (1974)
201.
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 197
Laser heating control with polarized
light in isolated multi-walled carbon
nanotubes
Faculty of Physics, Warsaw University of Technology,
Koszykowa 75, 00-662 Warsaw, Poland
We are proposing a novel method of laser heating
control only through change in polarization of the
incident light, keeping its power density constant
[1]. The idea combines antenna effect found in
isolated multi-walled carbon nanotubes and the
possibility of their heating by light illumination. To
observe this we used Raman spectroscopy
technique (see fig. 1), where the heating manifests
itself in a pronounced downshift of the Raman G
and 2D lines as a function of the polarization angle
(see fig. 2). To our knowledge, this is the first
experimental demonstration of polarization
dependent heating effect in carbon nanotubes
probed by Raman spectroscopy or by any other
technique. Interpretation of the observed
phenomena will be discussed.
Figure 1. (a) Schematic of the experimental setup used
for exploring the dependence of the inelastic scattering
amplitude and phonon energy on the angle φ between
the carbon nanotube axis and the direction of the
electric field vector of the incident and scattered light.
(b) Raman spectrum from an isolated multiwalled
nanotube. (c) Atomic force microscopy image of isolated
MWCNT (d~ 30 nm) on the SiO2/Si substrate.
Our method can be useful in field electron emission
devices or in selective nanotubes heating and
destruction. It can also be extended to other one
dimensional nanoobjects, if only certain conditions
are fulfilled. We expect that the effect presented
here can be found in other high aspect ratio nano-
objects, if only localization of the electronic states
is high enough and/or they stay within the
electrostatic limit.
Figure 2. Angular evolution of G and 2D band positions
for two polarization configurations (VV and VH). Four
data series in a plot (a) acquired for the different laser
power densities (p1 >p2 >p3 >p4) prove the thermal origin
of the Raman shift change. Experimental data (open
symbols) were fitted with the cos2(φ) function (lines).
References
[1] M. Zdrojek, J. Judek, M. Wąsik, Phys. Rev. Let.
108, 225501 (2012)
Mariusz Zdrojek,
Jarosław Judek and
Michał Wąsik
Late Abstracts
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 199
Optical antennas: nanoscience
meets quantum optics
Department of Physics, Friedrich-Alexander University Erlangen-Nürnberg
& Max Planck Institute for the Science of Light,
Günther-Scharowsky-Str. 1 /Bldg. 24,
91058 Erlangen, Germany
The ultimate control of light-matter interaction is
achieved when a single emitter strongly interacts
with a single photon. A manipulation at the level of
single quanta is not only of fundamental interest
but is of special importance for emerging quantum
technologies, such as quantum information
processing. In this talk I will first briefly review our
experimental progress on the interaction of
strongly focused photons with a single molecule [1,
2]. Then I will discuss how optical antennas can be
used to enhance light-emitter interaction and how
the emission properties of a single emitter can be
dramatically altered. Two types of antennas are
presented. With a metallic nanoantenna [3], we
experimentally achieved a two orders of magnitude
reduction in the fluorescence lifetime of a single
molecule [4]. In another experiment we embedded
a single organic molecule in a planar dielectric
antenna, which directs the emission towards the
collection optics. We realized a single-photon
source with near-unity collection efficiency and a
record count rate of 50x106 photons per second
[5]. With the current design we collect 96% of the
photons emitted by a single molecule. Metallo-
dilectric antennas promise photon collection rates
exceeding 99% [6].
References
[1] J. Huang et al., Nature 460, 76 (2009).
[2] Y. Rezus et al., Phys. Rev. Lett. 108, 093601
(2012).
[3] H. Eghlidi et al., Nano Lett. 9, 4007 (2009).
[4] K.G. Lee et al., arXiv:1208.1113v1 (2012).
[5] K.G. Lee et al., Nat. Phot. 5, 166 (2011).
[6] X.-W. Chen et al., Opt. Lett. 36, 3545 (2011).
Stephan Götzinger
200 | s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 T N T 2 0 1 2 m a d r i d ( s p a i n )
Environmental Effects
in Carbon Nanotube and
graphene-based Transistors
Département de Chimie, Université de Montréal, Montréal, Canada
Charge transfer doping by atmospheric gas is
ubiquitous in carbon-based field-effect transistors
(FETs), but this important phenomenon is yet
poorly understood. This talk will mainly discuss our
recent investigation on the origin of air doping and
on its signatures in the electrical, optical and
thermoelectric properties of carbon nanotube and
graphene devices.
Figure 1. Transfer characteristics for a 1 μm long
individual SWNT FETs in air. (a) A device on SiO2 and (b)
on parylene. In black is the forward gate voltage scan
and in red the reverse scan. The source-drain bias
voltage was Vsd = -1 V.
By using both carbon nanotube (Figure 1) and
graphene layers (Figure 2) as testbeds, we first
measured the influence of the chemical nature of
the substrate and the impact of different gas
exposure on the switching behaviour of both
nanoscale and thin-film FETs. Our studies revealed
that electrochemical charge transfer doping by the
water/oxygen redox couple is the underlying
mechanism behind the environmental effects in
most nanodevices (Figure 3). A solution to control
the air doping using plastic substrates was provided
and the kinetics of the charge transfer process was
monitored using graphene FETs [1,2]. The results
are quantitatively described using the Marcus-
Gerischer theory on charge transfer. Here we will
present the results and conclusions of our studies
and provide hint for controling the air-doping effect
in nanotube [1] and graphene devices [2,3].
Figure 2. Air effect on graphene FET with different
substrates. (A) Graphene on SiO2 and (B) graphene on
parylene. — (Red) Transfer characteristics of graphene
FETs measured in vacuum at room temperature after a 4
hour anneal at 400K. — (Cyan) Characteristics measured
after 30 minutes in air.
In a second study, we report the observation of the
optical signatures of doping and disorder in the
mid-infrared (MIR) absorption spectra of single-
walled carbon nanotubes (SWNTs) [4]. An
asymmetric line shape of the SWNT phonon modes
at ~870 and ~1600 cm-1
is characteristic of a Fano
resonance (Figure 4). This kind of resonance is
indicative of the presence of a strong e-ph
interaction and stems from the scattering of an
electronic continuum onto a phonon discrete
mode. The π phase shift of the wavefunction in the
neighborhood of the resonance creates destructive
interferences, which are seen as a dip in the
spectrum. According to theoretical calculations, the
bands at ~870 and ~1600 cm-1
are ascribed to oTO
and iTO infrared active phonon modes, respectively
Richard Martel
T N T 2 0 1 2 m a d r i d ( s p a i n ) s e p t e m b e r 1 0 - 1 4 , 2 0 1 2 | 201
TNT2012
Ab
st
ra
ct
s
[5]. A supplementary mode is observed at
~1260 cm-1
, which corresponds to a defect mode,
the so-called "D-band" in Raman spectroscopy. Our
results are in agreement with previous studies of
SWNTs in the MIR, though prior works failed to
recognize the role of e-ph interactions on these
infrared bands [6]. We also found that the e-ph
coupling broadens the phonon modes, which also
shifts to higher energy compared to the uncoupled
state. Finally, the influence of defects on the MIR
cross-section of Fano resonances was explored by
functionalization of SWNTs with bromophenyl
moieties. We measured that the absorption cross-
section increases when defects are induced in the
wall in comparison to undamaged SWNTs in the
same doping state. We therefore propose that the
Fano resonances are activated in two ways: First,
increasing the number of charge carriers leads to
an increase in the number of scattering events and
in intraband continuum absorption; second, the
creation of defects lowers the symmetry and
relaxes the selection rules. Similar Fano resonances
in single layer graphene will also be discussed.
Figure 3. Electron-transfer mechanism within the
Marcus-Gerischer theory. Schematic of the
water/oxygen redox couple density of states (DOS) for
an equivalent concentration of oxidizing and reducing
species and a comparison with the SWNT DOS (left) and
graphene DOS (right). The arrow indicates the direction
of the charge transfer reaction.
In a third study, P-doping by air exposure and N-
doping by local potassium (K) deposition was used
to prepare a suspended carbon nanotube film
having a PN doping profile between two metal
contacts. The electrical response of this PN device
was studied using laser excitation and temperature
gradients. The device response is best described in
terms of a thermal mechanism that is independent
of the nanotube-metal barrier. Moreover, we show
using estimates of the local Seebeck coefficients
that a PN junction in a suspended nanotube film
behaves as a thermopile. The performances of the
novel nanotube thermopile will be presented and
compared to state-of-the-art SWNT bolometers [7].
Figure 4. MIR spectra of an intrinsic and doped SWNT
film. Arrows indicate the phonon modes and the
presence of the Fano resonance. Inset: NIR-vis spectra of
the SWNT film.
This work was done in collaboration with Pierre
Lévesque, François Lapointe, Carla M. Aguirre,
Benoit Cardin-St-Antoine, Patrick Desjardins, David
Ménard and T. Szkopek.
References
[1] C. M. Aguirre, P. Levesque, M. Paillet, F.
Lapointe, B. C. St-Antoine, P. Desjardins and R.
Martel, Adv. Mat.. 21, 3087-3091 (2009).
[2] S. S. Sari, P. Lévesque, C. M. Aguirre, J.
Guillemette, R. Martel and T. Szkopek, Appl.
Phys. Lett. 95, 242104 (2009).
[3] P. L. Lévesque, S. S. Sabri, C. M. Aguirre, J.
Guillemette, M. Siaj, P. Desjardins, T. Szkopek,
R. Martel, Nano Letters, 11, 132-135 (2011).
[4] F. Lapointe, E. Gaufrès, I. Tremblay, N. Y-Wa
Tang, P. Desjardins and R. Martel, Phys. Rev.
Lett. 109, 097402 (2012).
[5] Jeon, G. S. & Mahan, G. D. Phys. Rev. B 72
155415 (2005).
[6] Bantignies, J.-L. et al. Phys. Rev. B 74 195425
(2006).
[7] B. C. St-Antoine and D. Ménard, Nano Letters,
11, 609-613 (2011); B. C. St-Antoine, David
Ménard and R. Martel, Nano Research, 5, 73-
81 (2012).
Posters list:
alphabetical ord
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authors
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topic
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ogr
aph
y R
esi
st"
stu
de
nt
S. C
arra
sco
,F. N
avar
ro-V
illo
slad
a, M
.C.
Cap
el-
Sán
che
z, J
.L. G
arcí
a Fi
err
o, M
.C.
Mo
ren
o-B
on
di,
C.A
. Bar
rio
s
Ca
rto
ixa
, X
av
ier
Spai
n
Oth
er
"Co
nd
uct
ance
Qu
anti
zati
on
in R
esi
stiv
e S
wit
chin
g"
sen
ior
Shib
ing
Lon
g, C
arlo
Gag
li, R
icca
rdo
Ru
rali,
En
riq
ue
Mir
and
a, D
avid
Jim
én
ez,
Ju
lien
Bu
ckle
y, M
ing
Liu
an
d J
ord
i Su
ñé
Ce
rpa
, A
risb
el
Spai
n
Nan
om
agn
eti
sm a
nd
Spin
tro
nic
s
"Hys
tere
sis
loo
ps
and
mag
ne
tic
susc
ep
tib
ility
fo
r d
iffe
ren
t
ori
en
tati
on
an
gle
of
ori
en
ted
car
bo
n n
ano
tub
es
usi
ng
VSM
an
d
SQU
ID"
sen
ior
Dan
iel C
alle
,Eliz
abe
tta
Ago
stin
elly
,
Gas
par
e V
arva
ro, V
ivia
na
Ne
gri,
Seb
asti
án
Ce
rdán
, Pal
om
a B
alle
ste
ros
Ch
an
dra
vil
as,
Pra
sha
nt
Ind
ia
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"Siz
e D
ep
en
de
nt
Dif
fere
nti
al Im
mu
ne
Re
spo
nse
wit
h P
oly
-ε-
cap
rola
cto
ne
Nan
op
arti
cle
s-A
n in
vit
ro s
tud
y"
stu
de
nt
Pra
shan
t, C
.K.,
Mad
hu
sud
an B
ha
tt, M
ano
j
Gau
tam
, A.K
.Din
da
Ch
oi,
Do
o-S
un
Ko
rea
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Co
lori
ng
of
inje
ctio
n m
old
ed
pla
stic
pla
te b
y su
rfac
e
nan
ost
ruct
ure
s w
ith
ou
t p
igm
en
t"
sen
ior
Ye
on
g-E
un
Yo
o, J
ae-S
un
g Y
oo
n
De
la
Pri
da
, V
icto
r M
an
ue
l
Spai
n
Nan
om
agn
eti
sm a
nd
Spin
tro
nic
s
"Ele
ctro
pla
tin
g an
d m
agn
eto
-str
uct
ura
l ch
arac
teri
zati
on
of
mu
ltila
yere
d C
o5
0N
i 50/C
o8
0N
i 20 n
ano
wir
es
fro
m s
ingl
e
ele
ctro
che
mic
al b
ath
in a
no
dic
alu
min
a te
mp
late
s"
sen
ior
V. V
ega
, L. I
gle
sias
, J. G
arcí
a, D
. Gö
rlit
z, K
.
Nie
lsch
, E. D
íaz
Bar
riga
-Cas
tro
, R.
Me
nd
oza
-Ré
sen
de
z, A
. Po
nce
, C. L
un
a
De
hli
ng
er,
Ma
ël
Fran
ce
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Op
tica
l an
d s
tru
ctu
ral p
rop
ert
ies
of
Al d
op
ed
Zn
O n
ano
-
stru
ctu
red
film
s fo
rme
d b
y So
l-G
el p
roce
ssin
g"
sen
ior
Car
ole
Fau
qu
et,
An
na
Re
yme
rs, V
lad
imir
Ge
vorg
yan
, Ala
in R
angu
is, D
amie
n
Ch
aud
anso
n, A
rtak
Kar
ape
tyan
an
d
Wla
dim
ir M
arin
e
De
ng
, C
he
nx
ing
Fran
ce
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
Nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Ob
serv
atio
n o
f lo
w-f
ield
mag
ne
tore
sist
ance
in g
rap
he
ne
at
roo
m
tem
pe
ratu
re"
stu
de
nt
Lin
Xia
oya
ng,
Li W
eiw
ei,
Kai
li Ji
ang,
Daf
iné
Rav
elo
son
a, C
lau
de
Ch
app
ert
, We
ish
en
g
Zhao
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Día
z G
arc
ía,
Ele
na
Spai
n
Nan
om
agn
eti
sm a
nd
Spin
tro
nic
s "S
pin
se
lect
ive
tra
nsp
ort
th
rou
gh h
elic
al m
ole
cula
r sy
ste
ms"
se
nio
r R
. Gu
tie
rre
z, R
. Raa
man
an
d G
. Cu
nib
ert
i
Do
mè
ne
ch G
arc
ía,
Be
rta
Spai
n
Nan
oC
he
mis
try
"De
velo
pm
en
t o
f n
ew
Po
lym
er-
Me
tal-
Nan
oco
mp
osi
tes
bas
ed
on
ac
tiva
ted
fo
ams
and
te
xtile
fib
ers
an
d t
he
ir c
atal
ytic
eva
luat
ion
."
stu
de
nt
K. Z
iegl
er,
J. M
acan
ás, F
. Car
rillo
, M.
Mu
ño
z, D
.N. M
ura
vie
v
Do
shi,
Nil
ay
U
nit
ed
Ara
b
Em
irat
es
Nan
ofa
bri
cati
on
to
ols
&
nan
osc
ale
inte
grat
ion
"N
ano
fab
rica
tio
n o
f n
ano
scal
ed
inte
grat
ed
cir
cuit
ch
ips"
st
ud
en
t
Eb
rah
imiN
eja
d,
Sa
lma
n
Iran
N
ano
mat
eri
als
for
En
erg
y "C
om
pre
ssiv
e B
uck
ling
of
Bo
ron
Nit
rid
e N
ano
tub
es
wit
h H
ydro
gen
Sto
rage
" st
ud
en
t A
li Sh
oku
hfa
r, A
min
Ho
sse
ini-
Sad
egh
,
Ab
olf
azl Z
are
-Sh
ahab
ad
i
En
cule
scu
, Io
nu
t
Ro
man
ia
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"In
flu
en
ce o
f m
eta
llic
nan
ost
ruct
ure
s o
n t
he
op
tica
l pro
pe
rtie
s o
f
dye
-do
pe
d p
oly
me
r th
in f
ilms"
se
nio
r E
. Mat
ei,
I. E
ncu
lesc
u, C
. Tra
utm
ann
Ev
an
ge
lou
, S
ofi
a
Gre
ece
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Eff
ect
s o
f a
Pla
smo
nic
Nan
ost
ruct
ure
on
Ke
rr N
on
line
arit
y in
a
Fou
r-Le
vel Q
uan
tum
Sys
tem
" st
ud
en
t V
assi
lios
Yan
no
pap
as, E
mm
anu
el P
asp
alak
is
Fa
teix
a,
Sa
ra
Po
rtu
gal
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Eff
ect
of
no
ble
me
tal n
ano
par
ticl
es
on
th
e g
lass
tra
nsi
tio
n
tem
pe
ratu
re o
f p
oly
(t-b
uty
lacr
ylat
e)
com
po
site
s"
stu
de
nt
An
a L.
Dan
iel-
da-
Silv
a, N
oé
mi J
ord
ão, A
na
Bar
ros-
Tim
mo
ns,
Tit
o T
rin
dad
e
Fig
ue
rola
, A
lbe
rt
Spai
n
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Go
ld-C
atal
yze
d G
row
th o
f C
ollo
idal
Cad
miu
m C
hal
coge
nid
e
Wo
rm-l
ike
Nan
ost
ruct
ure
s"
sen
ior
Víc
tor
Fern
ànd
ez-A
ltab
le a
nd
An
dre
a Fa
lqu
i
Fil
ik,
Ha
ya
ti
Tu
rke
y N
ano
Ch
em
istr
y "P
rep
arat
ion
of
Pla
tin
um
Nan
op
arti
cle
s-G
rap
he
ne
Mo
dif
ied
Ele
ctro
de
an
d S
en
siti
ve D
ete
rmin
atio
n o
f P
arac
eta
mo
l"
sen
ior
Gam
ze Ç
eti
nta
ş, A
siye
Asl
ıhan
Ava
n,
Serk
an N
aci K
oç,
İsm
ail B
oz
Flo
rica
, C
am
eli
a
Ro
man
ia
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Ele
ctri
cal p
rop
ert
ies
of
ZnO
sin
gle
nan
ow
ire
s co
nta
cte
d b
y FI
BID
and
EB
L"
stu
de
nt
Ge
org
ia Ib
ane
scu
, Ele
na
Mat
ei,
Nic
ole
ta
Pre
da,
Mo
nic
a E
ncu
lesc
u, M
aria
Eu
gen
ia
To
imil
Mo
lare
s, Io
nu
t E
ncu
lesc
u
Fra
nk
ov
a,
Jan
a
Cze
ch
Re
pu
blic
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"In
flu
en
ce o
f si
lve
r n
ano
par
ticl
es
on
in v
itro
wo
un
d h
eal
ing
mo
de
l"
sen
ior
Ad
éla
Gal
and
áko
vá, H
ana
Vág
ne
rová
,
Bo
hu
mil
Zále
šák
an
d J
itka
Ulr
ich
ova
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Fu
lco
, U
mb
ert
o
Bra
zil
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Ele
ctro
nic
Tra
nsp
ort
in Q
uas
ipe
rio
dic
Gra
ph
en
e p
–n
–p
Ju
nct
ion
s"
stu
de
nt
E.L
. Alb
uq
ue
rqu
e a
nd
M.S
. Vas
con
celo
s
Ga
lan
dá
ko
vá
, A
dé
la
Cze
ch
Re
pu
blic
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"Bio
logi
cal e
ffe
cts
ind
uce
d b
y si
lve
r an
d g
old
nan
op
arti
cle
s: in
vitr
o s
tud
y."
sen
ior
Jan
a Fr
anko
vá, K
lára
Hab
arto
vá, B
oh
um
il
Zále
šák,
Jit
ka U
lric
ho
vá
Ga
ldik
as,
Arv
aid
as
Lith
uan
ia
Nan
oC
he
mis
try
"Mo
de
ling
of
Dif
fusi
on
Pro
cess
in N
ano
size
d P
ero
vski
te L
aCo
O3
Po
wd
er
Cat
alys
ts"
sen
ior
N. B
ion
, S. R
oye
r, D
. Du
pre
z, D
. Sid
abra
Ga
rcía
-Ga
rcía
, E
nri
qu
e
Spai
n
Hig
h s
pat
ial r
eso
luti
on
spe
ctro
sco
pie
s u
nd
er
SPM
pro
be
"Te
rah
ert
z T
ime
Do
mai
n S
pe
ctro
sco
py
for
mo
lecu
les
insp
ect
ion
:
wat
er
vap
or
and
dru
gs"
stu
de
nt
Yah
ya M
ou
bar
ak M
ezi
ani,
Jesú
s E
nri
qu
e
Ve
lázq
ue
z-P
ére
z an
d J
aim
e C
alv
o-G
alle
go
Ga
rrig
a,
Ro
sa
Spai
n
Nan
oC
he
mis
try
"Go
ld N
ano
par
ticl
e D
eco
rati
on
of
Car
bo
n N
ano
tub
es
and
Gra
ph
en
e:
Syn
the
sis,
Ph
ysic
al-C
he
mic
al C
har
acte
riza
tio
n, a
nd
Ap
plic
atio
ns"
sen
ior
An
dré
s Se
ral-
Asc
aso
, Asu
nci
ón
Lu
qu
in,
Mar
ian
o L
agu
na,
Ge
rmán
F. d
e la
Fu
en
te
and
Ed
gar
Mu
ño
z
Ga
spa
r, V
ito
r P
ort
uga
l N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"Ce
ll In
tern
aliz
ing
and
pH
-re
spo
nsi
ve C
hit
osa
n N
ano
par
ticl
es
for
Imp
rove
d D
eliv
ery
of
DN
A B
iop
har
mac
eu
tica
ls"
stu
de
nt
F. S
ou
sa, R
O L
ou
ro, J
A Q
ue
iro
z, IJ
Co
rre
ia
Ga
va
Ma
rin
i, V
an
de
rle
ia
Bra
zil
Nan
oC
he
mis
try
"Ze
in n
ano
par
ticl
es
as a
car
rie
r sy
ste
m f
or
terp
ine
n-4
-ol"
se
nio
r Si
lvia
Mar
ia M
arte
lli, C
lari
ce F
ed
oss
e
Zorn
io,T
hia
go C
aon
, Clá
ud
ia M
aria
O
live
ira
Sim
õe
s a
nd
Val
dir
So
ldi
Gic
qu
el-
Gu
ézo
, M
au
d
Fran
ce
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Ph
oto
nic
s b
ase
d o
n c
arb
on
nan
otu
be
s"
sen
ior
Q.
Gu,
F.
Gri
llot,
S. L
oua
lich
e, J
. Le
Pou
liqu
en,
T. B
atte
, O
.Deh
aese
, A
. Le
Co
rre,
L. B
ram
erie
, D
. B
osc
,L.
Bo
dio
u, J
.-C
. Si
mo
n, Y
. B
atti
e, A
.
Lois
eau,
B. L
. Lia
ng,
D.L
. Huf
fake
r
Go
me
z, A
ran
cha
Spai
n
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Co
ntr
olle
d s
ynth
esi
s o
f si
nan
ow
ire
s o
n s
i su
bst
rate
s"
stu
de
nt
T. C
amp
o, F
. Már
qu
ez, E
. Eliz
ald
e, C
. Mo
ran
t
Gó
me
z-M
ed
ina
, R
aq
ue
l
Spai
n
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"No
n-c
on
serv
ativ
e e
lect
ric
and
mag
ne
tic
op
tica
l fo
rce
s o
n
sem
ico
nd
uct
or
par
ticl
es"
se
nio
r M
. Nie
to-V
esp
eri
na
s an
d J
. J. S
áe
nz
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Go
nzá
lez,
Im
an
ol
Spai
n
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Nan
oco
mp
osi
tes
bas
ed
on
po
ly(e
the
r im
ide
) b
y th
e a
dd
itio
n o
f a
po
ly(b
uty
len
e t
ere
ph
thal
ate
)/ca
rbo
n n
ano
tub
e m
aste
rbat
ch:
Ele
ctri
cal c
on
du
ctiv
ity
and
me
chan
ical
pe
rfo
rman
ce"
sen
ior
José
Ign
acio
Egu
iazá
bal
Go
nzá
lez-
Arr
ab
al,
Ra
qu
el
Spai
n
Nan
om
ate
rial
s fo
r E
ne
rgy
"H d
iffu
sio
n in
nan
oe
stru
ctu
red
as
com
par
ed
to
mas
sive
W"
sen
ior
N. G
ord
illo
, M. P
aniz
o-L
aiz,
A. R
ive
ra, F
.
Mu
nn
ik, K
. Sar
avan
an a
nd
J. M
. Pe
rlad
o
Go
nzá
lez-
Sa
nta
nd
er,
Cla
ra
Spai
n
Th
eo
ry a
nd
mo
de
llin
g at
the
nan
osc
ale
"L
oca
lizat
ion
of
stat
es
on
gra
ph
en
e-t
ype
latt
ice
s "
stu
de
nt
F. D
om
íngu
ez-
Ad
ame
, R. A
. Rö
me
r
Gro
ult
, H
ug
o
Spai
n
Nan
oC
he
mis
try
"Mic
ella
r ap
pro
ach
fo
r th
e d
esi
gn o
f n
ew
up
-co
nve
rtin
g
nan
op
ho
sph
ors
an
d s
up
erp
aram
agn
eti
c n
ano
par
ticl
es
for
op
tica
l im
agin
g an
d in
viv
o M
RI"
st
ud
en
t J.
Ru
iz-C
abe
llo a
nd
F. H
err
anz
Gry
m,
Jan
C
zech
R
ep
ub
lic
Nan
ost
ruct
ure
d a
nd
n
ano
par
ticl
e b
ase
d
mat
eri
als
"Liq
uid
-ph
ase
ep
itax
ial g
row
th o
n n
ano
po
rou
s su
bst
rate
s"
sen
ior
Du
šan
No
hav
ica,
Pe
tar
Gla
dko
v
Gu
err
ero
Co
ntr
era
s, C
arl
os
Luis
Spai
n
Nan
om
ate
rial
s fo
r E
ne
rgy
"Nan
ocr
ysta
ls in
th
e M
anu
fact
ure
of
Targ
et
for
Ine
rtia
l C
on
fin
em
en
t Fu
sio
n."
se
nio
r M
ano
lo P
erl
ado
an
d S
an
tiag
o C
ue
sta-
Lóp
ez
Ha
she
m N
ia,
Aza
de
h
Iran
N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"Eff
icie
nt
Ge
ne
Del
iver
y N
ano
vect
ors
Bas
ed o
n F
un
ctio
nal
izat
ion
Of
Sin
gle
wal
l Car
bo
n N
ano
tub
es (
SWN
T) w
ith
Po
lyet
hyl
en
imin
e (P
EI)"
st
ud
en
t M
.Ram
eza
ni,
M. R
ahim
izad
eh
, H. E
shgh
i, K
h. A
bn
oo
s
He
rmo
sa,
Cri
stin
a
Spai
n
Nan
oC
he
mis
try
"So
lve
nt-
ind
uce
d D
ela
min
atio
n o
f a
Mu
ltif
un
ctio
nal
Tw
o
Dim
en
sio
nal
Co
ord
inat
ion
Po
lym
er"
st
ud
en
t
A. G
alle
go, O
. Cas
tillo
, I. B
erl
anga
, C.
Gó
me
z, E
. Mat
eo
, J. I
. Mar
tín
ez
, F. F
lore
s,
A. H
ou
lto
n, B
. R. H
orr
ock
s, C
. Gó
me
z N
avar
ro, J
. Gó
me
z-H
err
ero
, S. D
elg
ado
and
F. Z
amo
ra
Hü
tte
l, A
nd
rea
s K
.
Ge
rman
y
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Sin
gle
wal
l car
bo
n n
ano
tub
es
as h
igh
ly s
en
siti
ve n
ano
-
ele
ctro
me
chan
ical
hyb
rid
sys
tem
s: d
rivi
ng,
bra
kin
g, d
ete
ctio
n"
sen
ior
D. S
chm
id, P
. Sti
ller
and
C. S
tru
nk
Ibra
him
, Im
ad
Ge
rman
y
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Gro
wth
of
hig
h y
ield
me
talli
c-fr
ee
ho
rizo
nta
lly a
lign
ed
sin
gle
wal
l
carb
on
nan
otu
be
s n
ucl
eat
ed
fro
m f
ulle
ren
e"
stu
de
nt
Alic
ja B
ach
mat
iuk,
Be
rnd
Bü
chn
er,
Mar
k H
. R
üm
me
li, G
ian
au
relio
Cu
nib
ert
i
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Ilie
, A
de
lin
a
Un
ite
d
Kin
gdo
m
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"No
n-C
ova
len
t B
iofu
nct
ion
aliz
atio
n o
f G
rap
he
ne
wit
h C
age
-lik
e
Mu
lti-
En
zym
e C
om
ple
xes
for
Sen
sin
g"
sen
ior
Ab
ee
r A
lsh
amm
ari,
Mar
eik
e
G.
Po
sne
r,
Ab
his
he
k U
pad
hya
y,
Fran
k M
arke
n, S
tefa
n B
agb
y
Ima
mo
glu
, G
am
ze
Tu
rke
y
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Th
e E
ffe
ct o
f E
lect
roch
em
ical
Me
tho
ds
on
Th
e S
hap
e o
f Zi
nc
Oxi
de
Nan
ost
ruct
ure
s"
stu
de
nt
Y.S
ahin
, E. S
uva
ci
Ing
ua
nta
, R
osa
lin
da
Ital
y N
ano
mat
eri
als
for
En
erg
y "H
igh
eff
icie
ncy
ele
ctro
de
s b
ase
d o
n n
ano
stru
ctu
red
mat
eri
als
for
en
erg
y d
evi
ces"
se
nio
r Se
ren
a R
and
azzo
, M
aria
Ch
iara
Mis
tre
tta,
Sa
lvat
ore
Pia
zza,
Car
me
lo S
un
seri
Iña
rre
a,
Jesú
s Sp
ain
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Off
-re
son
ance
mag
ne
tore
sist
ance
sp
ike
in ir
rad
iate
d u
ltra
cle
an
2D
ES"
se
nio
r
Iña
rre
a,
Jesú
s Sp
ain
T
he
ory
an
d m
od
elli
ng
at
the
nan
osc
ale
"Mic
row
ave
-in
du
ced
re
sist
ance
osc
illat
ion
s an
d z
ero
-re
sist
ance
stat
es
in 2
D b
ilaye
r sy
ste
ms"
se
nio
r G
lori
a P
late
ro
Jon
es,
Sa
rah
Ire
lan
d
Th
eo
ry a
nd
mo
de
llin
g at
the
nan
osc
ale
"Th
e E
ffe
ct o
f V
acan
cy D
efe
cts
on
Ele
ctro
n S
catt
eri
ng
in C
arb
on
Nan
otu
be
s"
stu
de
nt
G. G
ree
ne-
Din
iz, G
. Fag
as, M
.G. H
aver
ty, S
.
Shan
kar,
C. M
arti
nez
-Lac
amb
ra, J
.C. G
reer
Ko
sak
ov
skii
, G
erm
an
Ru
ssia
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Qu
antu
m E
ffe
cts
At
Fie
ld E
mis
sio
n F
rom
Car
bo
n Q
uas
i-1
D
Cat
ho
de
s"
stu
de
nt
Gu
lyae
v Y
u.V
., K
osa
kovs
kaya
Z.Y
a., B
lago
v
E.V
.,La
tysh
ev
Yu
.I.,
Orl
ov
A.P
., S
mo
lovi
ch
A.M
.
Kra
sod
om
ski,
Wo
jcie
ch
Po
lan
d
Nan
oC
he
mis
try
"Mo
dif
ied
gra
ph
en
e a
nd
gra
ph
ite
oxi
de
dis
pe
rsio
ns
in p
etr
ole
um
frac
tio
ns"
se
nio
r M
ich
ał K
raso
do
msk
i, M
ich
ał W
ojt
asik
, K
amil
Po
myk
ała
Ku
dri
n,
Ale
xe
y
Ru
ssia
N
ano
mag
ne
tism
an
d
Spin
tro
nic
s
"Th
e f
eat
ure
s o
f ca
rrie
r tr
ansp
ort
in t
he
fe
rro
mag
ne
tic
sem
ico
nd
uct
or
qu
antu
m w
ell
stru
ctu
res"
se
nio
r O
. Vik
hro
va, Y
u. D
anilo
v, I.
Kal
en
tie
va, B
.
Zvo
nko
v
Lad
o T
ou
riñ
o,
Isa
be
l
Spai
n
Th
eo
ry a
nd
mo
de
llin
g at
the
nan
osc
ale
"Mo
lecu
lar
mo
de
ling
of
aro
mat
ic in
tera
ctio
ns
be
twe
en
pyr
en
e
de
riva
tive
s an
d c
arb
on
nan
otu
be
s"
sen
ior
Viv
ian
a N
egr
i, Se
ba
stiá
n C
erd
án a
nd
Pal
om
a B
alle
ste
ros
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Lap
rise
-Pe
lle
tie
r, M
yri
am
C
anad
a N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"Me
sop
oro
us
Silic
a N
ano
par
ticl
es
(MSN
s) a
s M
RI/
PET
Du
al-
Mo
dal
ity
Imag
ing
Pro
be
s"
stu
de
nt
Jean
-Lu
c B
rid
ot,
Ré
my
Gu
ille
t-N
ico
las,
Fre
dd
y K
leit
z ,M
arcA
nd
ré F
ort
in
Leiv
a,
An
ge
l
Ch
ile
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Th
in F
ilms
of
Po
lye
lect
roly
tes
wit
h A
dso
rbe
d G
old
Nan
op
arti
cle
s"
sen
ior
Mar
cela
Urz
úa,
Max
imili
ano
Pin
o a
nd
D
eo
dat
o R
adic
´
Leó
n,
Na
tali
a
Ve
ne
zue
la
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Sh
ell
stru
ctu
res
in a
lum
iniu
m n
ano
con
tact
s at
ele
vate
d
tem
pe
ratu
res"
se
nio
r Jo
sé
Luis
C
ost
a-K
räm
er,
C
arlo
G
ue
rre
ro
and
Mar
ise
l Día
z
Léto
urn
ea
u,
Ma
thie
u
Can
ada
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"Pla
sma-
liqu
id E
lect
roch
em
istr
y :
a Fa
st M
eth
od
fo
r Sy
nth
esi
zin
g
Mag
ne
tic
Nan
op
arti
cle
s"
stu
de
nt
Ch
rist
ian
Sar
ra-B
ou
rne
t, M
yria
m L
apri
se-
Pe
lleti
er,
Mar
c-A
nd
ré F
ort
in
Lig
he
zan
, Li
lia
na
R
om
ania
N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"Th
erm
al p
rop
ert
ies
of
the
S-l
aye
r p
rote
in f
rom
Lac
tob
acill
us
saliv
ariu
s"
stu
de
nt
Ral
itsa
Ge
org
ieva
an
d A
dri
an
Ne
agu
Lim
, Jo
ng
So
o
Spai
n
Nan
om
agn
eti
sm a
nd
Spin
tro
nic
s "F
luct
uat
ion
re
lati
on
s fo
r sp
intr
on
ics"
se
nio
r R
osa
Lo
pe
z an
d D
avid
San
che
z
Lóp
ez,
Ke
nia
A.
Spai
n
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"An
tifo
late
s-M
od
ifie
d Ir
on
Oxi
de
Nan
op
arti
cle
s fo
r T
arge
tin
g
Can
cer
Ce
lls"
stu
de
nt
M. N
. Piñ
a, J
. Mo
rey,
R. A
lem
any,
B. O
.
Vö
gle
r, F
. M. L
. Bar
celó
Lori
te,
Isra
el
Ge
rman
y
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Stu
dy
of
the
tra
nsp
ort
pro
pe
rtie
s fr
eq
ue
ncy
de
pe
nd
en
ce o
f
mu
ltila
yer
grap
he
ne
by
Imp
ed
ance
Sp
ect
rosc
op
y"
sen
ior
A. B
alle
star
, J. B
aryo
la-Q
uiq
uia
, P.
Esq
uin
azi
Luci
o,
Ma
ria
Isa
be
l
Spai
n
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"Ne
w s
ele
ctiv
e d
rugs
bas
ed
on
car
bo
n n
ano
ho
rns"
st
ud
en
t G
iulio
Fra
cass
o,
Mar
co C
olo
mb
atti
, M
aría
An
ton
ia H
erre
ro,
Mau
rizi
o P
rato
an
d E
ster
V
ázq
uez
Lun
a,
Ca
rlo
s
Me
xico
N
ano
mag
ne
tism
an
d
Spin
tro
nic
s "M
icro
stru
ctu
ral a
nd
Mag
ne
tic
Pro
pe
rtie
s o
f H
em
atit
e S
ub
mic
ron
P
seu
do
-Cu
be
s O
bta
ine
d b
y N
ano
crys
tal O
rie
nte
d A
ttac
hm
en
t"
sen
ior
R. M
en
do
za-R
esé
nd
ez
Lam
iaa
, M
.A.A
li
Spai
n
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"To
xici
ty s
tud
ies
of
po
lym
er
bas
ed
su
pe
rpar
amag
ne
tic
iro
n o
xid
e
nan
op
arti
cle
s "
stu
de
nt
Vic
tor
Sorr
ibas
, Mar
tin
Gu
tie
rre
z, R
osa
C
orn
ud
ella
, Jo
sé A
nto
nio
Mo
ren
o, R
afae
l
Piñ
ol,
Lie
rni G
abilo
nd
o, A
nge
l Mill
án,
Fern
an
do
Pal
acio
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Ma
kh
sud
a,
Ab
du
saly
am
ov
a
Taj
ikis
tan
N
ano
Ch
em
istr
y "T
he
pre
par
atio
n a
nd
inve
stig
atio
n o
f p
rop
ert
ies
of
Er 2
O3"
sen
ior
Kh
.Kab
gov,
F.S
har
ipo
v, J
u.M
. Yu
, M.S
hu
lga
Ma
lla
via
, R
ica
rdo
Spai
n
Nan
ofa
bri
cati
on
to
ols
&
nan
osc
ale
inte
grat
ion
"Pro
po
sal o
f a
low
-co
st, m
ask-
less
pro
ced
ure
fo
r p
atte
rnin
g
ele
ctro
de
s o
f o
rgan
ic d
evi
ces
at n
ano
scal
e u
sin
g e
lect
ro-
dis
char
ges"
sen
ior
A. L
. Alv
are
z, C
. Co
ya, J
. Jim
en
ez-
Tri
llo ,
M.
Gar
cía-
Ve
lez,
G. A
lvar
ado
Ma
ne
ed
ae
ng
, A
tth
ap
ho
n
Th
aila
nd
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Siz
e-C
on
tro
llab
le C
alci
um
Car
bo
nat
e C
ryst
als
by
Ho
mo
logo
us
Seri
es
of
An
ion
ic S
urf
acta
nts
" se
nio
r A
dri
an
E. F
loo
d, S
uch
itra
Ph
ith
akso
em
sak
Ma
rco
s E
ste
ba
n,
Ra
qu
el
Ge
rman
y N
ano
Ch
em
istr
y "“
Liga
nd
-Fre
e”
Me
tal-
Nan
op
arti
cle
s in
Ion
ic L
iqu
ids"
st
ud
en
t F.
M. A
lbe
rti,
D. M
arq
uar
dt,
H. M
eye
r, C
.
Ru
tz, K
. Sch
ütt
e, C
. Vo
llme
r, C
. Jan
iak
Ma
sut,
Re
mo
Can
ada
Nan
om
ate
rial
s fo
r E
ne
rgy
"Nan
ost
ruct
ure
d t
he
rmo
ele
ctri
c al
loys
ob
tain
ed
by
me
chan
ical
allo
yin
g fo
llow
ed
by
ho
t e
xtru
sio
n o
r b
y m
icro
wav
e s
inte
rin
g "
sen
ior
M.K
. Ke
shav
artz
, J. A
rre
guin
-Zav
ala,
D.
Vas
ilevs
kiy
and
S. T
ure
nn
e
Ma
tei,
Ele
na
Ro
man
ia
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Eff
ect
of
the
de
po
siti
on
co
nd
itio
ns
on
th
e p
rop
ert
ies
of
mag
ne
tic
nan
ow
ire
s"
sen
ior
Ion
ut
En
cule
scu
,Cam
elia
Flo
rica
, M
on
ica
En
cule
scu
, Vic
tor
Ku
ncs
er,
Mar
ia E
uge
nia
To
imil
Mo
lare
s
Ma
uri
z, P
au
lo
Bra
zil
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Op
tica
l tra
nsm
issi
on
sp
ect
ra in
Fib
on
acci
ph
oto
nic
mu
ltila
yers
wit
h m
irro
r sy
mm
etr
y"
stu
de
nt
M.L
. Vas
con
celo
s an
d E
.L. A
lbu
qu
erq
ue
Ma
zela
, W
ojc
iech
Po
lan
d
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Eva
luat
ion
of
carb
on
nan
otu
be
s -
oil
dis
pe
rsio
n s
tab
ility
" se
nio
r W
ojc
iech
Kra
sod
om
ski,
Mic
hał
Paj
da,
Kam
il P
om
ykał
a, L
esz
ek
Zie
mia
ńsk
i
Me
le,
Da
vid
Fran
ce
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Hig
h F
req
ue
ncy
Ep
itax
ial G
rap
he
ne
Fie
lds
Eff
ect
Tra
nsi
sto
rs
(GFE
T)
on
SiC
" st
ud
en
t E
. Pic
ho
nat
, S. F
régo
nè
se, A
. Ou
erg
hi a
nd
H
. Hap
py
Me
nd
oza
-Re
sén
de
z, R
aq
ue
l
Me
xico
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Gre
en
Syn
the
sis
of
Silv
er
Nan
op
arti
cle
s M
ed
iate
d b
y B
ee
Pro
du
cts"
se
nio
r N
.O. N
uñ
ez,
C. L
un
a
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Mir
asm
ou
ri,
Mo
sle
m
Iran
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Th
e s
urf
ace
Pla
smo
n\'
s fr
eq
ue
nci
es
of
two
Me
talli
c N
ano
sph
ere
s
by
Blo
ch-J
en
sen
Hyd
rod
ynam
ical
Mo
de
l"
sen
ior
F.E
bra
him
i,V.E
bra
him
i
Mo
ha
jeri
, S
oh
a
Iran
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Ele
ctro
de
po
siti
on
of
Po
lyan
ilin
e n
ano
wir
es"
se
nio
r A
. Do
lati
, E.J
abb
ari
Mo
rey
, Je
ron
i
Spai
n
Nan
oC
he
mis
try
"Ch
em
ical
re
me
dia
tio
n:
Squ
aram
ide
Mag
ne
tic
Iro
n N
ano
par
ticl
es
for
Re
mo
val o
f To
xic
Me
tals
ion
s in
Wat
er"
se
nio
r M
aría
de
las
Nie
ves
Piñ
a an
d K
en
ia A
.
Lóp
ez
Mu
ná
rriz
, Ja
vie
r
Spai
n
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Sp
in-d
ep
en
de
nt
tran
spo
rt in
gra
ph
en
e n
ano
rib
bo
ns
wit
h a
pe
rio
dic
arr
ay o
f fe
rro
mag
ne
tic
stri
ps"
st
ud
en
t C
. G
aul,
A.
V.
Mal
ysh
ev,
P.
A.
Ore
llan
a, C
.
A. M
ülle
r an
d F
. Do
mín
gue
z-A
da
me
Mu
sta
fa,
Gh
ula
m
Au
stri
a
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Nan
op
arti
cle
s an
d n
ano
com
po
site
s as
VO
C r
eco
gnit
ion
mat
eri
als"
se
nio
r M
un
awar
Hu
ssai
n, P
ete
r A
Lie
be
rze
it
Na
eim
i, A
ten
a
Spai
n
Nan
om
agn
eti
sm a
nd
Spin
tro
nic
s
"Co
pp
er
(II)
Te
tras
ulf
on
ate
d P
hth
alo
cyan
ine
Imm
ob
ilize
d o
n
Sup
erp
aram
agn
eti
c N
ano
par
ticl
es"
se
nio
r A
bd
olr
eza
Re
zae
ifar
d, M
aaso
um
eh
Ja
farp
ou
r
Ore
lla
na
, P
ed
ro
Ch
ile
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Fan
o a
nd
An
dre
ev
Re
fle
ctio
n in
Qu
antu
m d
ots
" se
nio
r A
na
Mar
ía C
alle
, Mó
nic
a P
ach
eco
Ozo
gu
t, U
gu
r C
an
Tu
rke
y
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Sh
ape
an
d S
ize
Co
ntr
olle
d Z
nO
Par
ticl
es
and
Th
eir
Cyt
oto
xic
Be
hav
iou
r"
sen
ior
Ban
u B
aru
tca,
Ke
nan
Isik
, En
de
r Su
vaci
, A.
Tan
su K
op
aral
, Yu
cel S
ahin
Pa
laci
os,
Pa
blo
Sp
ain
N
ano
mat
eri
als
for
En
erg
y "T
he
ore
tica
l stu
dy
of
ban
d a
lign
me
nt
in n
ano
-po
rou
s Zn
O
inte
ract
ing
wit
h s
ub
stit
ute
d P
hth
alo
cyan
ine
s"
sen
ior
P. W
ahn
ón
, B
. Mar
i
Pa
rk,
Ky
ou
ng
-Ge
un
Ko
rea
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Sy
nth
esi
s o
f n
ano
-siz
ed
SiC
an
d S
i/Si
C f
rom
sili
con
an
d c
arb
on
po
wd
ers
by
no
n-t
ran
sfe
rre
d a
rc t
he
rmal
pla
sma"
st
ud
en
t Ji
n-W
o K
im, J
ae-K
ang
Kim
, San
g-K
i Kan
g,
Ye
on
-Tae
Yu
Pa
rt,
Ma
rko
Est
on
ia
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"No
vel m
eth
od
in s
ynth
esi
s o
f Y
SZ m
icro
tub
es
and
th
eir
app
licat
ion
as
ALD
su
bst
rate
s"
stu
de
nt
Ke
ijo R
iikjä
rv, K
elli
Han
sch
mid
t, A
ile
Tam
m, H
ugo
Män
dar
,Gu
nn
ar N
urk
,Kau
po
Ku
kli,
Tan
el T
ätte
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Pe
llic
o S
áe
z, J
ua
n
Spai
n
Nan
oC
he
mis
try
"Syn
the
sis
& F
un
ctio
nal
izat
ion
of
Fe3O
4 N
ano
par
ticl
es
for
Mag
ne
tic
Par
ticl
e Im
agin
g”
stu
de
nt
J. R
uiz
-Cab
ello
, S. V
ein
tem
illas
-Ve
rdag
ue
r,
M. P
ue
rto
Mo
rale
s, I.
Ro
drí
gue
z, F
. H
err
anz
Pe
ralt
a,
Ma
yra
V
en
ezu
ela
N
ano
fab
rica
tio
n t
oo
ls &
nan
osc
ale
inte
grat
ion
"A T
hre
e d
ime
nsi
on
al e
-be
am li
tho
grap
hy
tech
niq
ue
fo
r th
e
con
stru
ctio
n o
f h
igh
de
nsi
ty m
icro
an
d n
ano
coils
" st
ud
en
t J.
L. C
ost
a-K
ram
er
, E. M
ed
ina,
A. D
on
oso
Pé
rez-
Ga
rrid
o,
An
ton
io
Spai
n
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Gra
ph
en
e s
tru
ctu
res
wit
h c
ircu
lar
shap
e:
a st
ud
y o
f th
e in
flu
en
ce
of
top
olo
gica
l de
fect
s in
tra
nsp
ort
pro
pe
rtie
s"
sen
ior
Est
he
r Jó
dar
an
d F
ern
and
o R
oja
s
Ph
ila
nd
er,
Gh
ou
wa
a
Sou
th A
fric
a N
ano
Ch
em
istr
y "P
rop
ert
ies
of
Van
adiu
m D
ioxi
de
Co
atin
gs f
or
Smar
t W
ind
ow
Ap
plic
atio
ns"
st
ud
en
t M
. Maa
za a
nd
E. I
wu
oh
ag
Po
nz,
Fe
rna
nd
o
Spai
n
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
m
ate
rial
s
"A n
ano
pla
tfo
rm b
ase
d o
n s
elf
-ass
em
ble
d p
lan
t-m
ade
n
ano
par
ticl
es
wit
h m
ult
iple
ap
plic
atio
ns"
se
nio
r Fl
ora
Sán
che
z, C
arm
en
Man
silla
, P
ablo
Ibo
rt, S
ol C
ue
nca
, Mar
ta A
guad
o, C
ésa
r F.
Cru
z, Iv
on
ne
Go
nzá
lez
Pro
en
ca,
Ma
ria
na
P
ort
uga
l N
ano
mag
ne
tism
an
d
Spin
tro
nic
s
"Cro
sso
ver
be
twe
en
mag
ne
tic
reve
rsal
mo
de
s in
ord
ere
d a
rray
s o
f
ele
ctro
de
po
site
d n
ano
tub
es"
st
ud
en
t C
. T
. So
usa
, J.
E
scri
g,
J.
Ve
ntu
ra,
M.
Váz
qu
ez,
J. P
. Ara
újo
Ra
hm
an
, M
oh
am
ma
d M
ah
bu
bu
r
Spai
n
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"3D
nan
ost
ruct
uri
ng
of
nan
op
oro
us
ano
dic
alu
min
a fo
r p
ho
ton
ic
app
licat
ion
s"
stu
de
nt
Ger
ard
Mac
ias
Sotu
ela,
Mar
ia A
lba,
Llu
ís F
.
Mar
sal,
Jose
p P
alla
rès
and
Jo
sep
Fer
ré-
Bo
rru
ll
Re
zan
ka
, P
av
el
Cze
ch
Re
pu
blic
N
ano
Ch
em
istr
y "S
yste
mat
ic c
ircu
lar
dic
hro
ism
stu
dy
of
syst
em
s co
nta
inin
g
cyst
ein
e a
nd
silv
er
nan
op
arti
cle
s"
sen
ior
Jaku
b K
okt
an, a
nd
Vla
dim
ír K
rál
Ric
cia
rdi,
Ro
be
rto
N
eth
erl
and
s N
ano
Ch
em
istr
y "H
ete
roge
ne
ou
s ca
taly
sis
insi
de
a m
icro
reac
tor
con
tain
ing
acid
-
fun
ctio
nal
ize
d p
oly
me
r b
rush
es"
st
ud
en
t Ju
rria
an H
usk
en
s, W
ille
m V
erb
oo
m
Ric
o-G
arc
ía,
José
Ma
ría
Spai
n
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Eff
ect
of
sho
rt-r
ange
ord
er v
s. lo
ng-
ran
ge d
iso
rder
on
th
e ef
fect
ive
pro
per
ties
of
a 1
D "
met
amat
eria
l" c
hai
n o
f re
son
ant
par
ticl
es "
se
nio
r Jo
sé M
anu
el L
óp
ez-
Alo
nso
, A
sho
d
Ara
dia
n
Riv
era
Gil
, P
ila
r
Ge
rman
y N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"Po
lym
eri
c C
apsu
les
as m
ult
ifu
nct
ion
al t
oo
l fo
r in
trac
ellu
lar
ion
co
nce
ntr
atio
n"
sen
ior
Mo
ritz
Naz
are
nu
s, S
um
aira
Ash
raf,
Wo
lfga
ng
J. P
arak
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Ro
dri
go
, C
eci
lia
Spai
n
Nan
om
agn
eti
sm a
nd
Spin
tro
nic
s
"Dis
en
tan
glin
g th
e m
agn
eto
resi
stan
ce r
esp
on
se t
hro
ugh
th
e
mag
ne
tiza
tio
n r
eve
rsal
in m
agn
eti
c m
ult
ilaye
rs"
stu
de
nt
P. P
ern
a, M
. Mu
ño
z, J
. L. P
rie
to, A
.
Bo
llero
, J. L
. F. C
uñ
ado
, M. R
om
era,
J.
Ake
rman
n, E
. Jim
én
ez,
N. M
iku
sze
it, V
.
Cro
s, J
. Cam
are
ro a
nd
R. M
iran
da
Ro
drí
gu
ez
Ro
drí
gu
ez,
Pe
dro
Spai
n
Nan
oO
pti
cs
Nan
oP
ho
ton
ics
Pla
smo
nic
s
"Ph
on
on
s C
on
trib
uti
on
to
th
e In
frar
ed
an
d V
isib
le S
pe
ctra
of
II-V
I
Sem
ico
nd
uct
or
Nan
osh
ells
" st
ud
en
t C
. Kan
yin
da-
Mal
u a
nd
R.M
. de
la C
ruz
Ro
drí
gu
ez-
Ca
bo
, B
orj
a
Spai
n
Nan
oC
he
mis
try
"Ph
osp
ho
niu
m-b
ase
d io
nic
liq
uid
s fo
r th
e f
orm
atio
n o
f
nan
op
arti
cle
s"
stu
de
nt
Iago
Ro
drí
gue
z-P
alm
eir
o,
Ad
riá
n S
ánch
ez,
Eva
Ro
dil,
An
a So
to, A
lbe
rto
Arc
e
Ro
jas,
Fe
rna
nd
o
Spai
n
Gra
ph
en
e /
Car
bo
n
nan
otu
be
s b
ase
d
nan
oe
lect
ron
ics
and
fie
ld
em
issi
on
"Ge
ne
tic
Alg
ori
thm
s in
th
e c
on
tro
l an
d d
esi
gn o
f ch
arge
on
e q
ub
it
qu
antu
m g
ate
s in
cir
cula
r gr
aph
en
e q
uan
tum
do
ts"
sen
ior
Gib
rán
A
mp
arán
an
d
An
ton
io
Pé
rez-
Gar
rid
o
Ru
ng
nim
, C
ho
mp
oo
nu
t
Th
aila
nd
N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"In
sigh
t in
to m
ole
cula
r d
ynam
ics
pro
pe
rtie
s o
f ge
mci
tab
ine
anti
can
cer
dru
gs lo
ade
d in
sid
e a
n o
pe
n-e
nd
ed
sin
gle
-wal
led
carb
on
nan
otu
be
"
stu
de
nt
Uth
um
po
rn A
rsaw
ang,
Th
anya
da
Ru
ngr
otm
on
gko
l an
d S
up
ot
Han
no
ngb
ua
Sa
ba
ter,
Ca
rlo
s
Spai
n
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"In
vest
igat
ion
of
Pla
stic
an
d E
last
ic D
efo
rmat
ion
s o
f G
old
Nan
ow
ire
s u
nd
er
Un
iaxi
al S
trai
n w
ith
Po
int-
Co
nta
ct S
pe
ctro
sco
py"
st
ud
en
t T
aman
aco
Fra
nci
squ
ez
and
Car
los
Un
tie
dt
Sa
inz,
Ra
qu
el
Spai
n
Nan
oC
he
mis
try
"Co
lloid
al s
tab
ility
of
Gra
ph
en
e O
xid
e a
nd
de
riva
tive
s in
wat
er"
se
nio
r R
od
rigu
ez-
Tap
iad
or
M.I
., A
lcáz
ar C
.,
Mo
ren
o R
. an
d F
err
ito
R.
Sa
lun
di,
Aig
i
Est
on
ia
Oth
er
"De
velo
pm
en
t o
f h
igh
pe
rfo
rman
ce e
lect
ro-o
pti
cal f
ilms
by
sol-
gel
me
tho
d"
stu
de
nt
M. T
imu
sk, M
. Jär
vekü
lg, R
. Lõ
hm
us,
I.
Kin
k an
d K
. Sa
al
Sa
nta
ma
ría
, P
ab
lo
Spai
n
Nan
ost
ruct
ure
d a
nd
n
ano
par
ticl
e b
ase
d
mat
eri
als
"Im
pro
ved
me
chan
ical
an
d b
arri
er
pro
pe
rtie
s o
f am
orp
ho
us
po
lyam
ide
film
s b
y th
e a
dd
itio
n o
f a
hig
hly
exf
olia
ted
nan
ocl
ay"
stu
de
nt
Jose
Ign
acio
Egu
iazá
bal
Se
min
ov
ski,
Yo
ha
nn
a
Spai
n
Th
eo
ry a
nd
mo
de
llin
g at
the
nan
osc
ale
"Fir
st P
rin
cip
les
calc
ula
tio
ns
of
SnS 2
laye
red
se
mic
on
du
cto
r, t
akin
g
into
acc
ou
nt
the
Van
de
r W
aals
inte
ract
ion
s."
stu
de
nt
Pab
lo P
alac
ios,
Pe
rla
Wah
nó
n, a
nd
R
icar
do
Gra
u-C
resp
o
Se
ren
a,
Pe
dro
A.
Spai
n
Th
eo
ry a
nd
mo
de
llin
g at
the
nan
osc
ale
"To
war
ds
a m
ole
cula
r d
ynam
ics
de
scri
pti
on
of
the
me
chan
ical
pro
pe
rtie
s o
f an
tib
od
ies
as m
eas
ure
d w
ith
a f
orc
e m
icro
sco
pe
" se
nio
r J.
G. V
ilhe
na,
Ric
ard
o G
arcí
a, R
ub
én
Pé
rez
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Sh
am
ma
, R
eh
ab
Egy
pt
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"A n
ove
l nan
ove
sicu
lar
carr
ier
syst
em
fo
r o
cula
r d
eliv
ery
of
clo
trim
azo
le"
stu
de
nt
Mo
na
Bas
ha
Ah
me
d a
nd
Sam
eh
Ho
ssan
Eld
il
Sh
ay
an
i R
ad
, M
ary
am
Iran
N
ano
bio
tech
no
logi
es
&
Nan
om
ed
icin
e
"Ch
arac
teri
zati
on
an
d in
vit
ro e
valu
atio
n o
f m
icro
leak
age
an
d
anti
bac
teri
al p
rop
ert
ies
of
pre
par
ed
Zn
O a
nd
Zn
O:A
g n
ano
seal
ers
"
stu
de
nt
Ah
amd
Ko
mp
anya
, Ali
Kh
ors
and
Zak
a,
Maj
id A
bri
sham
ia, M
arya
m J
avid
ib, M
aje
d
Mo
rtaz
avib
Slo
va
k,
Pe
tr
Cze
ch
Re
pu
blic
Nan
ob
iote
chn
olo
gie
s &
Nan
om
ed
icin
e
"Nan
oco
mp
osi
te c
arb
on
mat
eri
al –
silv
er
nan
op
arti
cle
s:
Pre
par
atio
n a
nd
an
tib
acte
rial
act
ivit
y"
stu
de
nt
Dr.
Kvi
tek
Lib
or
So
corr
o,
Ab
ian
Spai
n
Nan
ob
iote
chn
olo
gie
s &
N
ano
me
dic
ine
"Im
mu
no
glo
bu
lin G
se
nso
r b
y m
ean
s o
f lo
ssy
mo
de
re
son
ance
s in
du
ced
by
a n
ano
stru
ctu
red
po
lym
eri
c th
in-f
ilm d
ep
osi
ted
on
a
tap
ere
d o
pti
cal f
ibe
r"
stu
de
nt
Jesu
s M
. Co
rre
s, Ig
nac
io D
el V
illar
, Fr
anci
sco
J. A
rre
gui,
Ign
acio
R. M
atia
s
So
ne
, B
ert
ran
d
Sou
th A
fric
a N
ano
stru
ctu
red
an
d
nan
op
arti
cle
bas
ed
mat
eri
als
"Nan
ost
ruct
ure
d t
un
gste
n t
rio
xid
e t
hin
film
s b
y aq
ue
ou
s ch
em
ical
gro
wth
fo
r ap
plic
atio
ns
in g
as s
en
sin
g an
d e
lect
roch
rom
ism
" st
ud
en
t T
. Mal
we
la, L
. Vay
ssie
res,
E. I
wu
oh
a an
d
M. M
aaza
Sp
aso
jev
ic,
Vo
jisl
av
Yu
gosl
avia
N
ano
mag
ne
tism
an
d
Spin
tro
nic
s
"Mag
ne
tic
pro
pe
rtie
s o
f n
ano
stru
ctu
red
Ca 1
-xG
dxM
nO
3 o
bta
ine
d
by
glyc
ine
-nit
rate
pro
ced
ure
" se
nio
r V
. Ku
sige
rski
, M. R
osi
c, J
. Bla
nu
sa, M
. Per
ovi
c,
A. M
rako
vic,
B. A
nti
c, a
nd
B. M
ato
vic
Sze
pie
nie
c, M
ark
Ir
ela
nd
T
he
ory
an
d m
od
elli
ng
at
the
nan
osc
ale
"In
flu
en
ce o
f E
lect
ron
Co
rre
lati
on
s o
n Q
uas
ipar
ticl
e E
ne
rgie
s an
d
Life
tim
es"
st
ud
en
t Ir
en
e Y
eri
skin
, Jim
Gre
er
Su
ny
ol,
Jo
an
Jo
sep
Spai
n
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Nan
ocr
ysta
llin
e m
agn
eti
c sh
ape
me
mo
ry a
lloys
: N
i-M
n-(
In,S
n)"
se
nio
r L.
Esc
od
a, J
. Sau
rin
a, A
. Car
rillo
, E. B
osc
h,
B. H
ern
and
o
Th
ue
som
ba
t, P
ak
vir
un
T
hai
lan
d
Ris
ks-t
oxi
city
-re
gula
tio
ns
"Eff
ect
of
Silv
er
Nan
op
arti
cle
s o
n R
ice
Ory
za S
ativ
a L.
KD
ML
10
5
see
dlin
gs"
stu
de
nt
Ch
adch
awan
Su
pac
hit
ra, H
ann
on
gbu
a
Sup
ot
and
Aka
sit
San
on
g
Um
ala
s, M
ad
is
Est
on
ia
Nan
ost
ruct
ure
d a
nd
n
ano
par
ticl
e b
ase
d
mat
eri
als
"Syn
the
sis
of
ZrC
-TiC
nan
ost
ruct
ure
s"
stu
de
nt
Val
ter
Re
ed
o, A
nts
Lõ
hm
us
and
Irin
a H
uss
ain
ova
Vil
ão
Ra
mo
s, G
ina
Po
rtu
gal
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Ele
ctri
cal c
on
du
ctiv
ity
and
re
lati
ve p
erm
itti
vity
of
15
nm
Al 2
O3-
wat
er
nan
ofl
uid
s"
stu
de
nt
R. I
gle
sias
, M.A
. Riv
as, F
. Co
elh
o a
nd
T.P
.
Igle
sia
s
authors
authors
authors
authors
country
country
country
country
topic
topic
topic
topic
poster title
poster title
poster title
poster title
student
student
student
student
senior
senior
senior
senior
Vä
lbe
, R
au
l
Est
on
ia
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"Pre
par
atio
n o
f R
-me
thyl
Imid
azo
lium
-So
diu
m H
exa
flo
rosi
licat
e
Co
mp
lex
Cry
stal
s"
stu
de
nt
Val
ter
Re
ed
o, U
no
Mäe
org
, An
dre
s H
oo
p,
An
ts L
õh
mu
s
We
bst
er,
Me
liss
a
Au
stra
lia
Nan
ost
ruct
ure
d a
nd
nan
op
arti
cle
bas
ed
mat
eri
als
"De
tect
ing
oil
see
ps
in s
eaw
ate
r, s
en
sin
g b
acte
ria
in m
ilk, a
nd
ide
nti
fyin
g d
ise
ase
sta
tes
fro
m a
pat
ien
t’s
uri
ne
: N
ew
ap
plic
atio
ns
for
gold
nan
op
arti
cle
ch
em
ire
sist
ors
"
sen
ior
Bu
rkh
ard
Rag
use
, Le
ch W
iecz
ore
k, E
dit
h
Ch
ow
, Jam
es
S. C
oo
pe
r, L
ee
J. H
ub
ble
Ya
ma
mo
to,
Ko
he
i
Jap
an
Low
dim
en
sio
nal
mat
eri
als
(nan
ow
ire
s, c
lust
ers
,
qu
antu
m d
ots
, etc
.)
"Th
erm
al C
on
du
ctan
ce C
alcu
lati
on
s o
f Si
lico
n N
ano
wir
es"
st
ud
en
t H
iro
yuki
Is
hii,
N
ob
uh
iko
K
ob
ayas
hi
an
d
Ke
nji
Hir
ose
Ya
tsk
iv,
Ro
ma
n
Cze
ch
Re
pu
blic
Nan
ost
ruct
ure
d a
nd
n
ano
par
ticl
e b
ase
d
mat
eri
als
"In
flu
en
ce o
f Zn
O s
urf
ace
po
lari
ty o
n t
he
ele
ctro
ph
ore
tic
de
po
siti
on
of
me
tal n
ano
par
ticl
es.
" se
nio
r Ja
n G
rym
Ye
risk
in,
Ire
ne
Ire
lan
d
Th
eo
ry a
nd
mo
de
llin
g at
the
nan
osc
ale
"Ele
ctro
ne
gati
vity
an
d E
lect
ron
Cu
rre
nts
in M
ole
cula
r T
un
ne
l
Jun
ctio
ns"
st
ud
en
t S.
McD
erm
ott
, R. J
. Bar
tle
tt, G
. Fa
gas
and
J.C
. Gre
er
Yu
, Y
eo
nta
e
Ko
rea
Nan
om
ate
rial
s fo
r E
ne
rgy
"Lig
ht
scat
teri
ng
eff
ect
of
nan
o-s
ize
d h
ollo
w T
iO2 la
yer
on
con
vers
ion
eff
icie
ncy
of
DSS
C"
sen
ior
Kye
on
gju
n K
o, K
yeo
ngg
eu
n P
ark
Yo
use
fi,
Ela
he
Ir
an
Nan
ofa
bri
cati
on
to
ols
&
nan
osc
ale
inte
grat
ion
"M
orp
ho
logy
stu
dy
of
the
ele
ctro
de
po
site
d p
lati
nu
m n
ano
tub
e"
stu
de
nt
A. D
ola
ti, I
. Im
anie
h
Zv
ato
ra,
Pa
ve
l
Cze
ch
Re
pu
blic
N
ano
Ch
em
istr
y "S
tru
ctu
ral a
nd
mag
ne
tic
pro
pe
rtie
s o
f n
ano
crys
talli
ne
La1
-xSr
xMn
O3
+d"
stu
de
nt
Mir
osl
av V
eve
rka,
Pav
el V
eve
rka,
Kar
el
Kn
íže
k, K
are
l Záv
ěta
, On
dře
j
Kam
an,V
lad
imír
Krá
l, E
tie
nn
e D
ugu
et,
G
razi
ella
Go
glio
an
d E
mil
Po
llert
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