electroless deposition of multi-functional zinc oxide surfaces displaying photoconductive,...
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Dynamic Article LinksC<Journal ofMaterials Chemistry
Cite this: J. Mater. Chem., 2012, 22, 3859
www.rsc.org/materials PAPER
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Electroless deposition of multi-functional zinc oxide surfaces displayingphotoconductive, superhydrophobic, photowetting, and antibacterialproperties
T. J. Wood,a G. A. Hurst,a W. C. E. Schofield,a R. L. Thompson,a G. Oswald,a J. S. O. Evans,a G. J. Sharples,b
C. Pearson,c M. C. Pettyc and J. P. S. Badyal*a
Received 30th August 2011, Accepted 3rd January 2012
DOI: 10.1039/c2jm14260k
Electroless growth of zinc oxide has been accomplished using palladium catalysts coordinated to pulsed
plasma deposited poly(4-vinylpyridine) nanolayers. Four different and concurrent functional
properties have been identified, which encompass photoconductivity, superhydrophobicity, photo-
switchable wetting, and bacterial killing.
1. Introduction
Zinc oxide is a transparent semiconductor with wurtzite
(hexagonal close packed) crystal structure and a bandgap of�3.3
eV. It exhibits many desirable properties, which include ultravi-
olet light absorption,1 photoconductivity,2–10 photocatalysis,11–15
photowettability,16,17 piezoelectricity,18 antibacterial behav-
iour,19,20 and wound-healing.21 These find technological appli-
cation in thin film transistors,22–26 dye-sensitized solar cells,27–32
kinetic energy harvesters,33–35 transparent electrodes in liquid
crystal displays,36 sunblock,37 fabric protection,38 and medical
dressings.39 Often zinc oxide is utilised as thin films, which have
been produced by RF sputtering,40–43 chemical vapour deposi-
tion,44–48 vapour diffusion catalysis,49 spray pyrolysis,50–53 elec-
trodeposition,54–56 sol–gel synthesis,57–60 or pulsed laser
deposition.61–63 Inherent limitations of such methods can include
their substrate-dependence (e.g. requirement for conducting or
physically robust substrates),54,61 and often harsh process
conditions (e.g. high temperatures40,44,49,50,57 or oxidative chem-
ical environments54,56). Therefore a strong demand exists for
a more universal approach towards generating zinc oxide
surfaces, particularly with a view towards future adoption of the
material’s multifunctional attributes for application in the
emerging field of wearable electronics (fibertronics).
Electroless deposition of zinc oxide is potentially attractive
given that it proceeds at mild temperatures (less than 50 �C), isinexpensive, and produces highly crystalline films.64 It entails
aDepartment of Chemistry, Science Laboratories, Durham University,Durham, DH1 3LE, England, UKbSchool of Biological and Biomedical Sciences, Biophysical SciencesInstitute, Science Laboratories, Durham University, Durham, DH1 3LE,England, UKcSchool of Engineering and Computing Sciences, Science Laboratories,Durham University, Durham, DH1 3LE, England, UK
This journal is ª The Royal Society of Chemistry 2012
reduction of palladium(II) centres to palladium(0) by
dimethylaminoborane:65–67
Pd2+ + (CH3)2NHBH3 / Pd0 + 2H+ + (CH3)2NBH2
which is followed by the reaction between zinc nitrate and
dimethylaminoborane in the presence of the palladium(0) cata-
lyst (where dimethylaminoborane reduces the nitrate).64,68
Effectively palladium(0) catalyzes the oxidation of
dimethylaminoborane:
(CH3)2NHBH3 + 2H2O / HBO2 + (CH3)2NH2+ + 5H+ + 6e�
leading to the corresponding reduction of nitrate ions (which
causes a local rise in pH):
NO3� + H2O + 2e� / NO2
� + 2OH�
This increase in pH triggers the growth of zinc oxide according to
the following acid–base reaction:69
Zn2+ + 2OH� / ZnO + H2O
Previously, the catalytic palladium centres were introduced by
the application of Pd/Sn colloids onto the surface followed by
acid washing for the removal of tin64—this harsh process is not
suitable for many substrates (e.g. textiles). Instead, given that
palladium centres can be coordinated to nitrogen-containing
heterocycles such as pyridine via electron lone pair interac-
tion,70–72 the aforementioned solution phase chemistry should in
principle be transferrable to a surface by utilizing immobilized
pyridine rings. Pulsed plasmachemical deposition of poly(4-
vinylpyridine) is one potential way for tethering pyridine groups
onto solid surfaces.72 This comprises modulating an electrical
discharge in the presence of gaseous precursors containing
polymerizable carbon-carbon double bonds.73 Mechanistically,
J. Mater. Chem., 2012, 22, 3859–3867 | 3859
Scheme 1 Palladium catalyst seeding of pulsed plasma deposited
poly(4-vinylpyridine) films followed by electroless growth of zinc oxide.
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there are two distinct reaction regimes corresponding to the
plasma duty cycle on- and off-periods (typical timescales are of
the order of microseconds and milliseconds respectively).
Namely, monomer activation and reactive site generation at the
surface occur during each short burst of plasma (via VUV irra-
diation, ion, or electron bombardment) followed by conventional
carbon-carbon double bond polymerization proceeding in the
subsequent extended off-time (in the absence of any VUV-, ion-,
or electron-induced damage to the growing film). Extremely high
levels of precursor structural retention within the deposited
nanolayer can be achieved, thereby yielding specific functional-
ities at the surface. Furthermore, by programming the pulsed
plasma duty cycle, it is possible to control (i.e. tailor) the surface
density of desired chemical groups. The obtained functional films
are covalently attached to the underlying substrate via free
radical sites generated at the interface during the onset of plasma
exposure. Other distinct advantages include the fact that the
plasmachemical approach is quick (single-step), solventless,
energy-efficient, and the reactive gaseous nature of the electrical
discharge provides conformality to a whole host of substrate
materials and complex geometries (e.g. microspheres, fibers,
tubes, etc.).74 Effectively, any surface which relies on a specific
functionality for its performance can, in principle, be produced
by the aforementioned pulsed plasmachemical methodology.
Examples devised in the past include: anhydride,75 carboxylic
acid,76 amine,77 cyano,78 epoxide,79 hydroxyl,80 halide,81 thiol,82
furfuryl,83 perfluoroalkyl,84 perfluoromethylene,85 and tri-
fluoromethyl86 functionalized surfaces. In this article we describe
the utilisation of pulsed plasmachemical deposition of poly(4-
vinylpyridine) films for the immobilization of catalytic palladium
species required for the electroless growth of zinc oxide with
a view to providing multifunctionality (photoconductivity,
superhydrophobicity, photo-switchable wetting, and antibacte-
rial activity), Scheme 1.
2. Experimental
Pulsed plasmachemical deposition was undertaken in a cylin-
drical glass reactor (4.5 cm diameter, 500 cm3 volume, 1 � 10�3
mbar base pressure, leak rate better than 1.7 � 10�9 mol s�1). A
copper coil (4 mm diameter, 10 turns) wound around the reactor
was attached to a 13.56 MHz radio frequency (RF) power supply
via an L–C matching unit. The whole apparatus was enclosed in
a Faraday cage. The chamber was evacuated using a 30 L min�1
rotary pump attached to a liquid nitrogen cold trap and the
system pressure monitored with a Pirani gauge. A pulse signal
generator was used to trigger the RF power generator and an
oscilloscope monitored the pulse shape. Prior to deposition, the
glass reactor was cleaned by scrubbing with detergent, rinsing in
acetone, oven drying, and then running a 40 W continuous wave
air plasma for 30 min. Next, silicon (100) wafers (Silicon Valley
Microelectronics Inc.), glass coverslips (VWR International
Ltd), or nonwoven polypropylene cloth pieces (Corovin GmbH)
were inserted into the chamber, and the system pumped back
down to base pressure. At this stage, the reactor was purged with
4-vinylpyridine precursor (+95%, Sigma-Aldrich, further puri-
fied with three freeze-pump-thaw cycles) at a pressure of 0.2
mbar for 5 min followed by ignition of the electrical discharge.
The optimum duty cycle for pyridine ring retention was on-
3860 | J. Mater. Chem., 2012, 22, 3859–3867
period ¼ 100 ms and off-period ¼ 4 ms in combination with peak
power ¼ 40 W.72 Upon completion of deposition, the precursor
was allowed to continue to flow through the system for a further
5 min in order to quench any trapped reactive sites contained
within the deposited film.
The pulsed plasma poly(4-vinylpyridine) functionalized
surfaces were then immersed into an aqueous catalyst solution
containing 2 mM palladium(II) chloride (+99.999%, Alfa Aesar),
3.0 M sodium chloride (+99.5%, Sigma), and 0.5 M sodium
citrate dihydrate (+99%, Aldrich) (which had been adjusted to
pH 4.5 with citric acid monohydrate (+99%, Aldrich)) for 12 h,
and subsequently washed in deionized water.72 Next, the palla-
dium(II) chloride immobilized surfaces were placed into an
aqueous chemical bath containing 0.05 M zinc nitrate (+98%,
Sigma-Aldrich) and 0.05 M dimethylaminoborane (+97%,
Sigma-Aldrich) at pH 6.5 and a temperature of 323 K for 2 h.64
Following zinc oxide growth, the surface was rinsed with
deionized water. Control samples of pulsed plasma poly(4-
vinylpyridine) placed into zinc nitrate–dimethylaminoborane
solution at slightly alkaline pH (pH 8.5, adjusted with sodium
hydroxide solution) showed no deposition. The deposited zinc
oxide films passed the Scotch tape adhesion test for all of the
substrates employed.
Film thickness measurements were carried out using a spec-
trophotometer (nkd-6000, Aquila Instruments Ltd.). Trans-
mittance and reflectance curves across the 300–1000 nm
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wavelength range were fitted to a Cauchy model for dielectrics
using a modified Levenberg-Marquardt method.87 The pulsed
plasma poly(4-vinylpyridine) deposition rate was measured to be
15 � 2 nm min�1.
X-ray photoelectron spectroscopy (XPS) characterization of
the functionalized substrates was carried out using a VG Escalab
spectrometer equipped with an unmonochromated Mg-Ka X-
ray source (1253.6 eV) and a concentric hemispherical analyzer
operating in constant analyzer energy mode (pass energy ¼ 20
eV) with the photoelectrons collected at a take-off angle of 12�
from the substrate normal. Elemental compositions were calcu-
lated using sensitivity factors derived from chemical standards:
C(1s):O(1s):N(1s):Pd(3d):Zn(2p) equals 1.00:0.36:0.57:0.05:0.05.
All binding energies were referenced to the C(1s) hydrocarbon
peak at 285.0 eV. The core level spectra were fitted to a linear
background.
Fourier transform infrared (FTIR) analysis of the deposited
films was undertaken using a Perkin-Elmer Spectrum One
spectrometer equipped with a liquid nitrogen cooled MCT
detector. Reflection-absorption (RAIRS) measurements utilized
a variable angle accessory (Specac Ltd) set at 66� fitted with
a KRS-5 polarizer to remove the s-polarized component. All
spectra were averaged over 128 scans at a resolution of 4 cm�1.
Depth profiling measurements were undertaken by the Ruth-
erford backscattering technique using a 4He+ ion beam (5SDH
Pelletron Accelerator). Backscattered 4He+ ions were detected
with 19 keV resolution using a PIPS detector.
X-ray diffraction patterns of electrolessly deposited zinc oxide
layers (1 mm thick, mounted on a silicon (100) substrate) were
collected using a powder diffractometer (Bruker d8) equipped
with a Cu tube (1.5418 �A wavelength), and a linear position-
sensitive detector (Lynx Eye with a Ni filter). Data were collected
from 5–65� 2q with a step size of 0.02�.The electrolessly deposited zinc oxide layers were imaged with
an optical microscope (Olympus BX40) fitted with a �50
magnification lens.
For the photochemical studies, ultraviolet light from a low
pressure Hg-Xe arc lamp running at 100 W (Oriel Corporation,
model 6136, emitting a strong line spectrum in the 240–600 nm
region88) was focused onto deposited zinc oxide films at a focal
length of 30 cm.
Electrical conductivity measurements were made using a pair
of parallel silver electrodes (6 mm length and separated by 1 mm)
painted onto the zinc oxide film which had been deposited onto
a non-conducting glass substrate. The electrical conductivity
behaviour of the zinc oxide films was found to be ohmic both
prior to and following UV exposure (0–200 V range). In the case
of UV-response curves, a constant voltage of 10 V was applied
and the electric current measured with a Keithley 2400
SourceMeter.
Sessile drop water contact angle measurements were per-
formed at ambient temperature using a video capture apparatus
in combination with a motorized syringe (VCA2500XE, A.S.T.
Products Inc.) dispensing a 2 mL droplet size. High purity water
(B.S. 3978 grade 1) was employed as the probe liquid.
Antibacterial testing was carried out according to a modified
form of the Japanese Industrial Standard Protocol.89 A bacterial
cell culture (wild-type Escherichia coli K-12 lab strain W3110)
grown to an A650nm of 0.4 was applied in minimal salts buffer
This journal is ª The Royal Society of Chemistry 2012
onto zinc oxide coated nonwoven polypropylene cloth and
uncoated controls. Samples were incubated for 24 h at 37 �C in
a moist, dark environment. Excess culture and cloth were
transferred to a 2 ml spin column and centrifuged at 9000 rpm
for 2 min to maximise recovery. The recovered culture was
vortexed to resuspend cells; tenfold dilutions were performed
and spotted onto LB agar. Plates were incubated overnight at
30 �C, after which the number of colonies were counted. To
control for cell absorption onto samples, the above procedure
was repeated with 1 min exposure of bacteria on coated and
uncoated cloth.
3. Results
3.1 Zinc oxide deposition
XPS characterization of pulsed plasma deposited poly(4-vinyl-
pyridine) layers confirmed the presence of only carbon and
nitrogen at the surface, with no Si(2p) signal showing through
from the underlying silicon substrate, Table 1. Furthermore,
a good correlation was found to exist between the atomic
percentages calculated for the precursor (theoretical) and pulsed
plasma deposited poly(4-vinylpyridine) films, which is consistent
with a high level of structural retention.72 Immersion into pal-
ladium(II) chloride solution gave rise to the appearance of
Pd(3d5/2) and Pd(3d3/2) signals at 338.3 eV and 343.5 eV
respectively and a Cl(2p) peak at 198.8 eV. This can be taken as
being indicative of PdCl2 complexation to the poly(4-vinyl-
pyridine) surface (the presence of the O(1s) peak at 532.7 eV is
due to water absorption from the aqueous palladium(II) chloride
solution90), Fig. 1 and Scheme 1.
For the 4-vinylpyridine monomer, the following infrared band
assignments can be made:91 vinyl C]C stretching (1634 cm�1),
aromatic quadrant C]C stretching (1597 cm�1 and 1548 cm�1),
aromatic semicircle C]C and C]N stretching (1495 and 1409
cm�1 respectively), and ]CH2 wag (927 cm�1), Fig. 2. All of
these bands were discernible following pulsed plasma deposition
apart from the vinyl carbon-carbon double bond features (which
disappear during polymerization). This is consistent with the
high level of structural retention associated with pulsed plasma
deposition.
Control samples of pulsed plasma deposited poly(4-vinyl-
pyridine) without palladium(II) chloride seeding gave rise to the
absence of electroless zinc oxide growth, which highlights the key
role of the immobilized palladium catalyst. In contrast, zinc
oxide films were clearly visible to the naked eye for the palladium
catalyst seeded pulsed plasma deposited poly(4-vinylpyridine)
films. Only zinc, oxygen and a trace amount of carbon (due to
atmospheric adsorption) were detectable by XPS, Fig. 1 and
Table 1. The O:Zn value is higher than the expected stoichio-
metric ratio, this can be attributed to adsorbed oxygen on the
surface as well as due to oxygen content present in any adsorbed
hydrocarbon impurities.92–94 The absence of N(1s) and Pd(3d)
signals confirmed complete coverage of the catalyst seeded
poly(4-vinylpyridine) layer by zinc oxide. Ion beam analysis
determined the zinc oxide film growth rate to be 230� 20 nm h�1.
The thickness of the ZnO films could be controlled by varying the
period of substrate immersion into the electroless deposition
solution.
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Table 1 XPS elemental compositions
Surface % C % N % Pd % Cl % O % Zn
4-Vinylpyridine (theoretical) 87.5 12.5 0.0 0.0 0.0 0Pulsed plasma poly(4-vinylpyridine) 87.3 � 0.5 11.8 � 0.5 0.0 0.0 0.9 � 0.5 0Palladium(II) seeded pulsed plasma poly(4-vinylpyridine)
63.3 � 0.5 8.3 � 0.5 2.9 � 0.2 5.5 � 0.5 20.0 � 0.5 0
Deposited zinc oxidea 5.0 � 0.9 0.0 0.0 0.0 63.0 � 0.8 32 � 1Deposited zinc oxide after 750 s UVexposurea
5.5 � 0.9 0.0 0.0 0.0 62.5 � 0.8 32 � 1
a No discernible difference was observed in the XPS core level peak shapes.
Fig. 1 XPS spectra of: (a) pulsed plasma deposited poly(4-vinyl-
pyridine); (b) pulsed plasma deposited poly(4-vinylpyridine) seeded with
palladium(II) chloride; (c) electroless zinc oxide growth onto palladium(II)
chloride seeded pulsed plasma deposited poly(4-vinylpyridine).
Fig. 2 Infrared spectra of: (a) 4-vinylpyridine monomer; and (b) pulsed
plasma deposited poly(4-vinylpyridine) (* denotes polymerizable alkene
bond absorbances in precursor).
Fig. 3 X-ray diffraction analysis of 500 nm thick zinc oxide film elec-
trolessly grown onto palladium seeded pulsed plasma deposited poly(4-
vinylpyridine).
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X-ray diffraction characterisation showed peaks at 31.9, 34.5,
36.3, 47.6, 56.6, and 62.9, which are consistent with zinc oxide in
the wurtzite structure (hexagonal close packed), Fig. 3. Rietveld
refinement confirmed that the ratio of peak intensities matches
that expected for wurtzite zinc oxide.95 Therefore the films are
polycrystalline and randomly oriented. Peak widths measured
for the powder diffraction patterns suggest a minimum crystallite
size of 25 nm; although a number of other parameters, including
lattice strain, can also be contributing factors.
Optical microscopy showed a roughened surface correspond-
ing to the different crystalline faces, Fig. 4.
3.2 Surface multifunctionality
During UV irradiation, zinc oxide films deposited onto flat non-
conducting glass pieces exhibited a marked increase in electrical
conductivity rising from a dark conductivity value of 10�7 mS
cm�1 up to 1.5 mS cm�1 after 750 s, Fig. 5. The electrical
conductivity was observed to slowly decay following termination
of UV exposure. In the case of storage under ultra high vacuum
This journal is ª The Royal Society of Chemistry 2012
Fig. 4 Optical microscope image of zinc oxide film electrolessly grown
onto palladium seeded pulsed plasma deposited poly(4-vinylpyridine).
Fig. 5 500 nm thick zinc oxide grown by electroless deposition onto
non-conducting glass: (a) electrical conductivity and equilibrium water
contact angle following UV irradiation in air (switched off at 750 s); and
(b) equilibrium water contact angle recovery of zinc oxide film following
UV light extinction at 750 s (offset to time ¼ 0 h).
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(pressure < 10�8 mbar), photoconductivity was retained
following a period of weeks, whilst UV irradiation under vacuum
gave rise to an increase in electrical conductivity.3
High water contact angle values of 150�, but with a large
contact angle hysteresis were measured for zinc oxide coated flat
silicon substrates, Table 2. Exposure of these surfaces to UV
radiation in air resulted in a significant drop in the equilibrium
water contact angle attributable to surface hydrophilicity, Table
2 and Fig. 5. Exposure to higher intensity UV light over the same
period of time caused the contact angle to drop below 20�.Following termination of UV exposure, the contact angle slowly
recovers to its original value of 150� over a period of around 3
weeks, Fig. 5. However, when such zinc oxide coated silicon
wafers, which had been exposed to UV in air, were stored under
ultra high vacuum conditions (<10�8 mbar), there was no
recovery in contact angle (i.e. remained at 60� over a period of 4
weeks). Also, UV irradiation of zinc oxide coated samples under
ultra high vacuum conditions or pure O2 (rather than in air)
produced no discernible change in the contact angle (i.e.
remained at 150�). These control experiments highlight that
contact angle decay during UV exposure and subsequent
hydrophobic recovery upon UV termination involve surface
reaction with air. The XPS C(1s) envelope corresponding to
small amounts of adsorbed hydrocarbon species (285.0 eV) did
not change, Fig. 6.
Electroless growth of zinc oxide onto pulsed plasma poly(4-
vinylpyridine) coated non-woven polypropylene substrates gave
rise to superhydrophobicity (high equilibrium water contact
angles, exceeding 150�, in combination with low contact angle
hysteresis96), Table 2. In this case, the water repellency of the zinc
oxide surface was not found to be perturbed by exposure to UV
radiation, Table 2.
Zinc oxide coated polypropylene cloth pieces also displayed
significant antibacterial activity (up to a log kill of 2.9) towards
the Gram-negative bacterium, Escherichia coli, Table 3. Control
samples of the polypropylene cloth pieces exhibited no antibac-
terial activity, whereas a reduction of only log 0.2 was observed
following exposure to the pulsed plasma poly(4-vinylpyridine)
coated cloth. This small drop can be attributed to the absorption
(rather than killing) of cells onto the hydrophilic layer, since
a similar result was obtained following a 1 min incubation period
(as opposed to 24 h).
4. Discussion
Pulsed plasmachemical deposition is an established technique for
the functionalization of surfaces.73 Film thickness can be easily
controlled, and the process is solventless, conformal, as well as
being substrate-independent; thereby making it well-suited for
application to three-dimensional substrates such as textiles. In
this study, XPS and infrared analyses have shown that a variety
of substrates can be coated with structurally well-defined poly(4-
vinylpyridine) layers (in marked contrast to earlier high power
continuous wave plasma polymers derived from 4-vinyl-
pyridine97). Subsequent seeding with catalytic palladium centres
provides for the localised electroless growth of zinc oxide. An
additional benefit of this approach is that the functional polymer
nanolayer serves to protect the underlying substrate material
from subsequent chemical processing steps (in this case the
J. Mater. Chem., 2012, 22, 3859–3867 | 3863
Table 2 Water contact angle measurements for zinc oxide coated substrates
Substrate
Water Contact Angle/�
Equilibrium Advancing Receding Hysteresis
Silicon wafer 150 � 1 152 � 1 35 � 1 117 � 2Silicon wafer after 750 s UV in air 60 � 1 65 � 1 7 � 1 58 � 2Silicon wafer after 750 s UV in UHV 150 � 1 152 � 1 35 � 1 117 � 2Silicon wafer after 750 s UV in O2 149 � 1 151 � 1 35 � 1 116 � 2Nonwoven 154 � 1 154 � 1 154 � 1 0 � 2Nonwoven after 750 s UV in air 154 � 1 154 � 1 154 � 1 0 � 2
Fig. 6 XPS C(1s) envelope of electrolessly deposited zinc oxide onto
silicon wafer: (a) no UV exposure, and (b) 750 s UV exposure.
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oxidising and reducing agents contained within the zinc oxide
electroless deposition solution). The growth of zinc oxide in the
hexagonal wurtzite structure is not unexpected, since it is the
most thermodynamically stable form at ambient pressure and
temperature.98
The semiconducting nature of zinc oxide stems from natural
doping (n-type) in the form of interstitial singly charged zinc
cations (Zn+), which lie close to the conduction band, and so can
be easily thermally ionized (to Zn2+ + e), thus supplying electrons
to the conduction band.99,100 The aforementioned excess elec-
trons leaving behind interstitial Zn+ can become trapped at the
surface by adsorbed oxygen (O2(ads)) to give O2�(ads) species.
101–103
Zinc oxide coated pulsed plasma poly(4-vinylpyridine) films
display photoconductivity during UV light exposure, Fig. 5.
Contributions to the shape of the photoconductivity curve can be
split into fast reversible (electron promotion from valence to
Table 3 Antibacterial activity against the Gram-negative bacterium, Escher
Substrate Fraction
Uncoated 1Pulsed plasma poly(4-vinylpyridine) 0.6 � 0.Zinc oxide 0.0012 �Zinc oxide irradiated with UV light 0.009 �
3864 | J. Mater. Chem., 2012, 22, 3859–3867
conduction band), and slow irreversible (surface chemistry of
adsorbed species).94 In addition, when zinc oxide is exposed to
UV photon radiation with energy greater than or equal to its
bandgap (3.3 eV) electron promotion from the valence band to
the conduction band leads to electron-hole pair formation. These
electrons can also become trapped by physisorbed oxygen at the
surface to form chemisorbed O2�(ads) up to a self-limiting
concentration of O2�(ads) due to electrostatic repulsion between
O2�(ads) at the surface.103 Such O2
�(ads) species are capable of
attracting holes from the bulk, which migrate towards the surface
to combine with the O2�(ads) species leading to the formation of
a surface vacancy and photodesorption of molecular
oxygen:3,103,104
ZnO + hn / ZnO + e-h (electron-hole pair)
e + O2 (ads) / O2�(ads)
h + O2�(ads) / O2 (g)[ + ,
Following the loss of molecular oxygen from the surface via
desorption, further electrons promoted from the valence band to
the conduction band during UV irradiation are no longer able
to become trapped by adsorbed oxygen, and instead contribute
to electrical conductivity. Conversely, readsorption of oxygen
onto the surface for instance after the termination of photo-
desorption leads to a decay in conductivity,3 Fig. 5. Therefore in
the case of zinc oxide films, the shift in equilibrium between
oxygen desorption and readsorption processes will dominate the
shape of the photoconductivity rise and decay curves due to the
inherent high surface area of the deposited material.6 In the case
of storage under vacuum following termination of UV irradia-
tion, photoconductivity was retained over a period of weeks,
which is consistent with the electrical conductivity decay mech-
anism being governed by molecular oxygen adsorption.3
Reversible wettability was also observed following UV irra-
diation of zinc oxide coated flat substrates. Clean zinc oxide
ichia coli, for nonwoven cloth
of Cells Recovered After 24 h Log Kill
03 0.20.0009 2.9
0.005 2.0
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surfaces are hydrophilic105,106 (equilibrium water contact angles <
35�, along with many other metal oxides107), but in ambient
conditions they are known to attract amphiphilic, carbon-con-
taining contaminants present in the atmosphere.16,105,106 These
adspecies act like surfactants with the hydrophilic domain
attracted towards the zinc oxide surface (bonding via electron
lone pair interaction with the electron depletion layer at the zinc
oxide surface108,109); the hydrophobic domain of the carbon-
containing species is therefore responsible for the widely
observed hydrophobicity of zinc oxide surfaces in ambient
conditions.16 Two mechanisms are proposed in the literature for
the UV-induced switch to hydrophilicity of zinc oxide surfaces:
firstly, the UV light induces a photocatalytic reaction at the zinc
oxide surface resulting in removal of carbon contaminants (as in
the case of titanium dioxide self-cleaning surfaces110); or
secondly, the UV light leads to desorption of molecular oxygen
from the zinc oxide surface followed by dissociative water
adsorption.16 The lack of change in carbon: oxygen: zinc XPS
elemental ratios and C(1s) envelope shapes of the zinc oxide
surface before and after UV irradiation suggests that the first
mechanism is unlikely to be the predominant factor, Table 1 and
Fig. 6. Photodesorption of O2(g) from the zinc oxide surface
creates vacancies, which can allow water molecule (present in the
ambient air) adsorption. The necessity for water to be present
during UV exposure (as demonstrated by the control experi-
ments, where contact angle did not drop for zinc oxide surfaces
which were UV irradiated under ultra high vacuum or pure
oxygen and subsequently exposed to air, Table 2) indicates
a photo-assisted dissociative water adsorption mechanism,
Scheme 2. Where the photogenerated hydroxide groups are
responsible for the surface switching from hydrophobic to
hydrophilic.16,17,111 The contact angle fully recovers over a matter
of weeks following extinction of UV irradiation (the exact
duration depending upon UV intensity), Fig. 5. Verification of
oxygen readsorption processes underpinning the reversible
surface wetting behaviour back towards hydrophobic recovery
was achieved by observing the lack of contact angle increase for
Scheme 2 Mechanism illustrating change in adsorbed species on zinc
oxide surface during UV irradiation followed by subsequent oxygen
readsorption over time (literature references numbered in brackets).
This journal is ª The Royal Society of Chemistry 2012
when zinc oxide was UV irradiated in air (on flat substrate) and
then stored under ultra high vacuum for extended periods of
time. Therefore, in air, the water adsorbed at the surface during
photoirradiation is thermodynamically displaced by oxygen
species over a period of time.16 The speed at which this happens
(leading to recharged hydrophobicity) is slow, and determines
the long hydrophobicity recovery times seen for zinc oxide.16
This photochemical contact angle decay observed for UV expo-
sure in air and reversal afterwards shows no correlation to the
fast (purely electronic) bulk electron photoconduction processes,
due to the far slower oxygen desorption and readsorption surface
chemistry processes, Scheme 2.
Zinc oxide displays similar surface chemistry during UV
irradiation to that reported for titanium dioxide (another metal
oxide semiconductor with a comparable bandgap). It is postu-
lated that molecular oxygen adsorbs at titanium dioxide surface
defect sites,112,113 and it then traps a photogenerated electron to
become O2�(ads) species.
114,115 In a similar fashion to zinc oxide,
such O2�(ads) species undergo photodesorption as O2(g) from
TiO2 surfaces during UV irradiation.116 Therefore, the same
behaviour is observed for both zinc oxide and titanium dioxide
surfaces in relation to photoconductivity and photo-switchable
wetting.117–119
By depositing zinc oxide onto a roughened surface (nonwoven
polypropylene), the aforementioned reversible wettability
changes for flat substrates (silicon wafers or glass coverslips)
were not observed; water contact angle hysteresis became negli-
gible, Table 2. Theoretical studies predict that for ideal surfaces
(where the water droplet is in contact with all of the surface)
water contact angle hysteresis should increase with roughness
reaching a maximum beyond which the liquid is unable to
completely wet the whole surface.120,121 At this point, surface
wetting obeys the Cassie-Baxter relationship,122 where the
roughness is so great that air becomes trapped during liquid-
surface contact giving rise to incomplete wetting. In the present
study, it is the rough texture (visible to the naked eye) of
deposited zinc oxide films, which leads to the high equilibrium
water contact angle, Fig. 4. Furthermore, by changing the
substrate from two-dimensional (flat) to porous three-dimen-
sional (nonwoven), there is an enhancement of Cassie-Baxter
behaviour, culminating in very low contact angle hysteresis,
Table 2. Although in the case of zinc oxide coated nonwoven
polypropylene the surface energy will increase during UV
exposure (as described in Scheme 2), there is sufficient Cassie-
Baxter behaviour for superhydrophobicity to be sustained.123,124
Significant bactericidal effects were also measured for zinc
oxide coated polypropylene cloth substrates. Escherichia coli was
tested because it is renowned for being resistant to killing by
many conventional antibacterial surfaces.125,126 The observed
antibacterial activity in the present study is most likely attrib-
utable to the presence of oxygenated radical species on the zinc
oxide surface.127–129 For instance, oxygen radical species can be
precursors to the formation of molecules such as hydrogen
peroxide, which are toxic towards bacteria by causing damage to
the bacterial cell wall, proteins and nucleic acids.130,131 This
antibacterial mechanism does not appear to be closely linked to
the UV induced photoconduction and photowettability mecha-
nism, as seen by the continued killing of bacteria by zinc oxide
surfaces which had been UV irradiated beforehand, Table 3.
J. Mater. Chem., 2012, 22, 3859–3867 | 3865
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5. Conclusions
Palladium catalyst seeded pulsed plasma poly(4-vinylpyridine)
nanolayers have been employed for the localised electroless
growth of crystalline zinc oxide thin films whilst concurrently
protecting the underlying substrate from the reactive chemical
reagents. These zinc oxide coatings are found to display photo-
conductivity, photo-switchable wetting, superhydrophobicity,
and antibacterial properties.
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