modelling functional materials (beyond local dft) … · hybrid functionals electronic structure...
TRANSCRIPT
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FURIO CORA’
MODELLING FUNCTIONAL MATERIALS(BEYOND LOCAL DFT)
University College LondonDept of Chemistry [email protected]
PERSONAL INTEREST
SOLIDS WITH TRANSITION METAL IONS
-VERY RESPONSIVE TO ENVIRONMENT (CATALYSIS, SENSORS)
-EXTREME PROPERTIES (MICROELECTRONICS)-CHALLENGE TO THEORY
ZEOLITES, ALPOS DENSE SOLIDS
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IN THE BEGINNING …
( ) ( ) ( ) ( )1 21 1KStot 1 22 21 12
ˆ v ,E EN
xcσi σi σi ext α β
σ α,β i
ρ r ρ rn r ρ r dr dr dr ρ ρ
r
σ
ϕ ϕ−= =
= ∆ + + + ∑ ∑ ∫ ∫r r
r r r r rr
Kinetic Kinetic EnergyEnergy
Coulomb energyCoulomb energyNuclear (external) Nuclear (external) potentialpotential
ExchangeExchange--correlation correlation energyenergy
BUT !ONE ELECTRON SHOULD NOT INTERACT WITH ITSELF
REQUIRES
ElectronElectron--electron interactionelectron interaction
( ) ( ) [ ]1 21 1 2212
0E xcρ r ρ r
dr dr ρr
+ =∫r r
r rr
NOT SATISFIED IN DFT WHEN ρ ISTHE TOTAL EL. DENSITY: SELF-INTERACTION
ρρρρ = TOTAL EL. DENSITY
ELECTRONIC STRUCTURE STUDY OF SOLIDS
FURIO CORA’
ELECTRONIC STRUCTURE STUDY OF SOLIDS
FURIO CORA’
Mn
O
H
P
O
O O
Ni
f)
LOCALISED d ELECTRONS
( ) ( ) [ ]1 21 1 2212
0E xcρ r ρ r
dr dr ρr
+ =∫r r
r rr
SELF-INTERACTION TERMscales as 1/r12CRITICAL FOR LOCALISED STATES
STRONGLY CORRELATED SYSTEMS
but the problem is the EXCHANGE
MnO O
O
O
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SOLUTION STRATEGIES:
1) INTRODUCE SELF-INTERACTION IN DFT-LDA+U-SIC-LDAself-interaction is different for each electron;the SI correction must be orbital-dependent(traditional DFT only uses the TOTAL electronic density)
2) GO BEYOND DFT-Quantum Monte Carlo (QMC)-Wavefunction techniques (post-HF: MP, CI, CP)-Dynamical Mean Field Theory (DMFT)
1b) THE OLDEST QM THEORY (HARTREE-FOCK) IS INFERIOR TO DFT, BUT IS SELF-INTERACTION FREE
< I J | K L > - < I K | J L > = 0 if I=J=K=L COMBINE HF AND DFT DESCRIPTIONS:
HYBRID FUNCTIONALS
ELECTRONIC STRUCTURE STUDY OF TM PEROVSKITES
FURIO CORA’UCLUCLUCLUCL
HYBRID FUNCTIONALS
One-electron equations can be cast in the same structure
-HF hHF= t + VN(R) + j + XHFαXHF+(1-α)VX
-DFT hKS= t + VN(R) + j + VXC
Tempting to mix the two treatments, BUT! this has nofoundation in quantum mechanics, and needs to be treatedas empirical.
HYBRID FUNCTIONALS ARE GOOD IF AND ONLY IFWE ACHIEVE SYSTEMATIC IMPROVEMENTS
ELECTRONIC STRUCTURE STUDY OF TM PEROVSKITES
FURIO CORA’UCLUCLUCLUCL
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1 PARAMETER ONLY – AMOUNT OF HF EXCHANGEPRIMARY GOAL: REMOVE SELF-INTERACTION
(1 )hyb GGA GGAxc x x x x cE a E a E E= + − +
EVALUATE EFFECT OF ax (0
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DISPLACEMENT OF CHARGES DURINGFERROELECTRIC DISTORTION
M
A CUBIC PHASE2e- in O-2p AO
FE PHASE2e- in MO BOND
e-
e-
+ -
THE POLARISATION HASNUCLEAR AND ELECTRONIC CONTRIBUTIONS
ACCURACY OFHYBRID FUNCTIONALSRELATIVE IONIC SIZES, DISTORTION, POLARISATION
POLARISATION
EXPT
BEST VALUE
DISTORTION
EXPT
BEST VALUE
Ferroelectric BaTiO3
EXPT
RELATIVE IONIC SIZES
LDA,GGABEST VALUE
EXACT EXCHANGE
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MAGNETIC PEROVSKITES: KMnF3
MAPPING ONTO AN ISING SPIN HAMILTONIAN
0 0 , ,
12M ij z i z ji j
E E E E J S S≠
= + = + ∑Jse
Jd
HYBRID DFT IN THE SOLID STATE
FURIO CORA’UCLUCLUCLUCL
MAGNETIC PEROVSKITES
KMnF3
EXPT
26AFM FM
se z
E E E
J S
∆ = −
=
Jse
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UCLUCLUCLUCLUCLUCLUCLUCLBand Structures of FeO
0%HF 35%HF20%HF
BLYP functional gives a metallic solutionBLYP functional gives a metallic solution
R X M Γ F
-0.40
-0.30
-0.20
-0.10
0.00
0.10
0.20
0.30
0.40
0.50
Ha
rtre
e
R X M Γ F
-0.40
-0.30
-0.20
-0.10
0.00
0.10
0.20
0.30
0.40
0.50
Hart
ree
R X M Γ F
Ef
-0.40
-0.30
-0.20
-0.10
0.00
0.10
0.20
0.30
0.40
0.50
Ha
rtre
e
B3LYP transition between Fe3d/O2sp -Fe3dB3LYP transition between Fe3d/O2sp -Fe3d
H35B65LYP transition between Fe3d/O2sp-Fe4s
H35B65LYP transition between Fe3d/O2sp-Fe4s
Experimentally weak absorption of 0.5 eV between Fe3d/O2sp-Fe4sand stronger transition of 2.4 eV between Fe3d/O2sp-Fe3dBagus et al. PRL (1977)
Experimentally weak absorption of 0.5 eV between Fe3d/O2sp-Fe4sand stronger transition of 2.4 eV between Fe3d/O2sp-Fe3dBagus et al. PRL (1977) Alfredsson et al. PRB (2004)
TERNARY SOLIDS, ABOnEQUILIBRIUM DISTORTION
PEROVSKITES: IDEAL RATIO OF IONIC SIZESTol = (RA+RO)/(RB+RO) = √√√√2O
A
B
RATIO OF AO/BO EQUIL.BOND DISTANCES
VARIES WITH % HF EXCHANGE
DIFFERENT FUNCTIONALS GIVEDIFFERENT IONIC SIZES
COVALENCE CAN DELOCALISEELECTRONS AND REDUCE
SELF-INTERACTIONMAKES CATIONS WITH COVALENT
BONDS (B) BIGGERCaTiO3, BaTiO3, CaSO4, AlPO4 etc
EXPT
LDA,GGA
EXACT EXCHANGE
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INITIAL CONCLUSIONS- Hybrid functionals improve accuracy of DFT for solids- Best hybridisation depends on property, and isdifferent from molecular values (more localised states)
HYBRID DFT IN THE SOLID STATE
FURIO CORA’UCLUCLUCLUCL
Equil. Geom, Lattice param. 60-80(structural distortions) >601 el. properties: P, Jse 40-60Transition pressures >502nd deriv: phonons, Elast. prop 20
Property α (%)
Ref. for initial systematic workF. Corà et al, ‘The performance of hybrid density functionals in solid state chemistry’,Sructure and Bonding vol 113, 2004, 171-232.
CaCu3Ti4O12 (CCTO)
Giant dielectric constant (104 – 105) subject of debate.
Barrier layer effect?
Require semi-conducting grains/domains separated by insulating surfaces.
Mark Michel
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Bulk electronic properties:Magnetic coupling and
Spin localisation
Depend on %HF exchangenot on local DFT flavour
Bulk Structuredepends on both choice of functional and
amount of HF exchange.
Best agreement:20-60% HF exchange With PBE and BLYP functionals.
SURFACE PROPERTIES OF CCTO (Ca0.25Cu0.75TiO3)
(001) SURFACE STRUCTURE
2) ONLY ONE OF THE THREESURFACE Cu2+ IONS IS STILL INSQUARE PLANAR COORDINATION
TWO Cu2+ IONS ARE NOT INSTABLE COORDINATION1) IN LARGE WINDOW3) IN SMALL WINDOW
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DISPROPORTIONATION1) Cu1+ IN LARGE WINDOW3) Cu3+ IN SMALL WINDOW
CALCULATED ∆E2Cu2+ � Cu1+ + Cu3+ = 0.52 eV
HYBRID DFT IN THE SOLID STATE
UCLUCLUCLUCL
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SURFACE PROPERTIES OF CCTO (Ca0.25Cu0.75TiO3)
TOTAL AND PROJECTED DENSITY OF STATES
Cu DISPROPORTIONATION
GENERATES
SURFACE TRAP STATES
Cu1+ TRAPS HOLES ���� Cu2+
Cu3+ TRAPS e- ���� Cu2+
NO MOBILE CARRIER
AT THE SURFACE
HYBRID DFT IN THE SOLID STATE
UCLUCLUCLUCL
20% HF: surface disproportionationinto Cu1+ and Cu3+.
60% HF: Charge transfer from surface O2- to Cu2+, yielding Cu1+/O1- ions.
Redox chemistry creates trap states which trap mobile charge carriers.
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(001) SURFACE – CHANGE %HF
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INTERNAL BARRIER LAYER MODEL FOR CCTO
Furio Cora, Amy Poole, Andrew Wills
Prussian Blue, FeIII4(FeII(CN)6)3(H2O)6
Unit cell of Prussian Blue with iron sites
indicated
FeIII
FeII
FeIII
• Cubic Structure:
– FeIII - NC - FeII - CN - FeIII
– Lattice parameter = 10.2Å
– Space Group = Pm3m
• Colour due to charge transfer between FeIII and FeII cations
• Historically determined:– 0.008 µB ± 0.028*
*Ref: P. Day, F. Herrn, A. Ludi et al; Helvetica Chemica Acta,63, 148 (1980)
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• FeIII is paramagnetic– S=5/2
• FeII, C and N are diamagnetic– S=0 FeII ;
– But measured magnetisation (0.008±0.028µB)
• Ferromagnetic order below TC = 5.7K
Bonding in Prussian Blue
ILL-D20 Experimental output
Polarised neutron diffraction and Experimental Spin Density Maps
Spin density map {1 0 0} plane
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III
III
II
IIIII
Theoretical spin density map
{2 0 0} plane
Theoretical spin density map
{1 0 0} plane
Experimental spin density map
{1 0 0} plane
Experimental and Theoretical spin density maps
{1 0 0} plane
Spin Density Maps of Prussian Blue
Analysis of the Spin Density
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II IIIII
III
II
• Spin Density
– FeIII• Expt = 3.5 µB• Model = 4.3 µB
– FeII• Expt = 0.40 µB• Model = 0.36 µB
spin density map {2 0 0} plane
Spin Density Map
PB Model with no vacancies (only FeIII(CN)6): spin on FeII ~ 0.2 µBModel with vacancies (trans-FeIII(CN)4(H2O)2): spin on FeII ~ 0.36 µB
• Spin Density on Fe(II) depends on local environment. Range from 0.07 to 1.2 electrons (40%HF)
• Coupled to structural distortion
Spin Density Maps of Prussian Blue –Disordered vacancies
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Average value of spin density on FeII increases on increasing disorder in structure
• Spin Density FeII
• Expt = 0.40 µB• Model = 0.072 µB ordered vacancies
0.073/1.112 disordered (1)0.157/0.179 disordered (2)
Highest when there is FeIII(CN)5(H2O)Oxygen of the H2O is π donor; this
reduces the dimension in which spin can be transferred; more charge is transferred to the FeII opposite H2O
Spin Density Maps of Prussian Blue –Disordered vacancies
CONCLUSIONS
-Hybrid functionals improve accuracy of DFT for solids- Systematic trends, but- Best hybridisation depends on property, and isdifferent from molecular values (more localised states)
-Defects, surfaces and situations that break local symmetryare more challenging. Underconstrained solutions difficult to reproduce reliably with DFT; importance ofaccurate reference from experiment or modelling (post-HF)
-In general, beware of anything unusual coming from a DFTstudy!
HYBRID DFT IN THE SOLID STATE
FURIO CORA’UCLUCLUCLUCL