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FirstFirst--principles simulations of defectsprinciples simulations of defects
Chris G. Van de WalleMaterials Department, UCSB
A. Janotti, J. Lyons, J. Varley, J. Weber (UCSB)P. Rinke (FHI), M. Scheffler (UCSB, FHI Berlin)G. Kresse (U. Vienna)
. reyso , . euge auer sse or NSF, DOE
School on Computational Modeling of Materials
December 2-3, 2010Antwerp, Belgium
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Why study defects?Why study defects? Defects Vacancy
dislocations Point defects:
Native defects Impurities
Defects often determineInterstitial
the properties of materials Doping and its limitations
Device degradation Diffusion
Mediated b oint defects
Antisite
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Technological significanceTechnological significance Semiconductors
c eve g er op ng eve s p-type doping of AlN would allow UV lasers
Controllabl do e materials -t e andn-t e Oxides
Photovoltaics
CuInxGa1-xSe2 Hydrogen storage materials
Kinetics of hydrogen release in NaAlH4 Embrittlement of structural metals
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Links to experimentLinks to experiment Secondary Ion Mass Spectrometry (SIMS) Impurity concentrations (to within factor of 2)
os ron ann a on spec roscopy Most sensitive to negatively charged vacancy(-like) defects
EXAFS (extended x-ray absorption fine structure) Microscopic structure, atomic relaxations
Electron paramagnetic resonance + ENDOR Hyperfine parameters (wave functions, atomic positions)
Vibrational spectroscopy (Raman, FTIR) Local vibrational modes; sensitive to atomic positions
Deep level transient spectroscopy Electronic transition levels
Total-energy differences, not Kohn-Sham levels Photoluminescence (PL), PL excitation
Optical transition levels
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Defect calculations: geometryDefect calculations: geometry Greens functions
mp emen a on cu Non-intuitive
Surface effects
Supercells "
R. P. Messmer and G. D. Watkins, inRadiation Damage and Defects in Semiconductors(Inst. of Phys. London, 1972), No. 16, p. 255.
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Defect Formation EnergiesDefect Formation EnergiesExample: VO
+VO +2
oxide: VO oxide O2
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Defect Formation EnergiesDefect Formation EnergiesExample: VO
Fe +VO +
2
oxide: VO oxide O2 reservoir
e @ F(electronreservoir)
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FormalismFormalism Eform : formation energy
Concentration of defects or impurities:C = Nsites exp [ Eform/kT]
Example: oxygen vacancy in ZnO+ = + + +
O: energy of oxygen in reservoir, i.e.,oxygen chemical potential
EF: energy of electron in its reservoir, i.e., the Fermi level enera express onE form(Dq) = E tot(Dq) E tot(bulk)+ n i i + qE F
n i: num er o a oms e ng exc ange o orm e e ec
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Formation energyFormation energy V in ZnO
Zn-rich conditions:Zn=E tot(bulk Zn)
O=E tot(O2)+ Hf (ZnO)
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Transition levelsTransition levels Char e-state
transition levels+/0CB
VB(+/0)(2+ /+)
2+/0
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Issues...Issues... Band a roblem
DFT (LDA, GGA) Affects formationenergies and
transition levels Even for neutral chargestates, if defect-inducedKohn-Sham states are occupied with electrons
DFT/LDA band gap
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BandBand--gap corrections: Empirical correctionsgap corrections: Empirical corrections Ad hoc corrections Scissors operator
gap eve s ase on con uc on- vs. va ence- an c arac er
Delta-function(-like) term added to potential, shiftss states N. E. Christensen, Phys. Rev. B30, 5753 (1984).
D. Segev, A. Janotti, and C. G. VdW, Phys. Rev. B75, 035201 (2007). Issues
Hard to control May have unintended consequences (indirectvs . direct gaps, )
Extrapolations based on calculations that yielddifferent gaps
eren p ane-wave cu o s Different exchange-correlation functionals
. , . , . , . . , . Issue: different choices of parameter not only produce different gap,
but also different levels of accuracy for description of defect
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BandBand--gap corrections: SIC and LDA+gap corrections: SIC and LDA+ UU Physically meaningful improvements Self-interaction corrections
J. P. Perdew and A. Zunger, Phys. Rev. B23, 5048 (1981). Difficult to implement in self-consistent calculations for solids Incorporate in pseudopotentials
. , . , . ,Phys. Rev. B 52, 14316 (1995).
n n +
0.37Ec LDA+U approach
0.34
. 1.51Ev
. . . ,Appl. Phys. Lett.87, 122102(2005).
S. Lany and A. Zunger,
7.16Zn3d-band
.. . , .
Issues: Determination of U .
How to extrapolate to theexperimental gap?
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Oxygen vacancy in ZnOOxygen vacancy in ZnO
orrec e
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BandBand--gap corrections: Beyond DFTgap corrections: Beyond DFT Quasiparticle calculations
Combine DFT andG 0W0 : goo or s ruc ura proper es G 0W0: many-body perturbationtheory for defects: accurate
electron affinities in solids P. Rinke, A. Janotti, M. Scheffler,
and C. G. Van de Walle, Phys.Rev. Lett.102, 026402 (2009).
Quantum Monte Carlo Richard Hennig
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DeepDeep vs.vs. shallow defectsshallow defects
CB
VBVB
Note: dispersion Due to finite su ercell size Energetics taken care of by special-point sampling Make sure correct occupation of states
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DeepDeep vs.vs. shallow defectsshallow defects
CB
VBVB
DeepLocalized wave function
ShallowDefect-induced state is
Level (usually) far from bandedges
resonance in VB or CBNear VB or CB: only small
perturbationEffective mass state
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Alignment of Fermi levelAlignment of Fermi level
Charges are exchanged with E F, referenced to E vq = q orm tot tot
Presence of defect in supercell shifts average electrostaticpotential with respect to bulk
defect bulk
V
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Supercell size effectsSupercell size effects Neutral defects:
atomic relaxations are included, and overlap ofwave functions is small enough
Charged defects: Inbalance in electronic and
Coulomb divergence Neutralizing background
G=0 term calculatedfor neutral system
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Supercell size effectsSupercell size effects Neutralization leads to unintended terms in
Interactions with neutralizing background and
Makov-Payne correctionE L = E 2/ L C 2/L3 + O L-5
G. Makov and M.C. Payne, Phys. Rev. B51, 4014 (1995). Correct in vacuum
Effect of solid: dielectric constant
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Supercell size effectsSupercell size effects Explicit studies as a function of supercell size have
Fits to 1/L and 1/L3 terms In some cases, Makov-Payne correction satisfactory In other cases: Makov-Payne
correction makes things
significantly worse Example: V+ in diamond Shim, Lee, Lee, and Nieminen,
Phys. Rev. B 71, 035206 (2005).
With MP
MP
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Supercell size effectsSupercell size effects Need rigorous analysis of electrostatic interactions
C. Freysoldt, J. Neugebauer, and C. G. Van de Walle,Phys. Rev. Lett.102, 106402 (2009).
Coefficient of 1/L3 (quadrupole) term
Alignment term ows es ng w e erpoint charge correction(Makov-Payne) suffices or not Fails if defect state decays slowly; point-charge model
overcorrects Prescri tion for addressin this roblem
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Native point defects in ZnONative point defects in ZnO VO, VZn dominate
A. Janotti and C. G. Van de WalleZn-rich Appl. Phys. Lett.87, 122102 (2005).
S. B. Zhanget al. , Phys. Rev. B 63,075205 (2001). F. Oba et al. Ph s. Rev. B 77
245202 (2008).
VO: deep donor Also hi h formation ener in
n-type ZnO VZn: deep acceptor
Cause of reen luminescence A. F. Kohan, G. Ceder,D. Morgan, C. G. Van de Walle,
Phys. Rev. B 61, 15019 (2000)
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Native defectsNative defectsvsvs
. impurities. impurities Native defects cannot explain n -type doping
Impurities: donors?
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Interstitial Hydrogen in ZnOInterstitial Hydrogen in ZnO
2
3
( e
V )
0
1
+H
a t i o n e n
e r g
0.0 0.5 1.0 1.5 2.0 2.5 3.0
-1 F o r
EF (eV)
H+ is the only stable charge state hydrogen acts as shallow donor Unexpected! In other semiconductors hydrogen reduces the conductivity
C. G. Van de Walle, Phys. Rev. Lett.85, 1012 (2000).y y u
But: highly mobileM. G. Wardle, J. P. Goss and P. R. Briddon, Phys. Rev. Lett. 96, 205504 (2006).
unstable at temperatures where n -type conductivity is known topersist (>500 oC)Also cannot explain dependence of conductivity on oxygen partial pressure
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Substitutional h dro en in ZnOSubstitutional h dro en in ZnO Forced to reconsider the role ofhydrogen...
new physics/chemistry emerged! Substitutional hydrogen VO HO Formation energy:low
Ionization energy: small;shallow donor
i
ons s en y exp a ns epen ence on -type conductivity on oxygen partialpressure Zn
g [ X ] [n ] g [ X ] [n ][n ]
HO [Hi]
l o
[V O]
[HO][Hi][Hi]
l o
[V O][V O]
[HO][HO]
pO 21/2pO 21/2
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pp --type doping of ZnOtype doping of ZnO Nitrogen is often regarded as most suitable
hole dopant Shallow acceptor in ZnSe
Numerous reports of p -type ZnO crystals - , ,
Reliability? Reproducibility?
C.H. Park, S.B. Zhang, and S.-H. Wei, PRB 66, 073202 (2002).
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BandBand--gap corrections: Hybridgap corrections: Hybrid functionalsfunctionals Mixing of Hartree-Fock (exact exchange) and DFT
A. D. Becke, J. Chem. Phys.98, 1372 (1993). unc ona s m x n ~ o exac exc ange PBE0 J. P. Perdew, K. Burke, and M. Ernzerhof,
. . . , . J. P. Perdew, M. Ernzerhof, and K. Burke,
J. Chem. Phys. 105, 9982 (1996).
HSE Exact exchange only for short-range interactions J. Heyd, G. E. Scuseria and M. Enzernhof,
J. Chem. Phys. 118 , 8207 (2003).
a n very goo escr p on o many proper es Band gaps close to experiment
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HSE calculations forHSE calculations for ZnOZnO Hybrid functionals
include a portion ofexact exchange,correct band gap . , . . ,
and M. Ernzerhof, J. Chem.Phys. 118, 8207 (2003).
=0.36 VASP code (ver. 5.1)
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Nitrogen acceptor inNitrogen acceptor in ZnOZnO Deep acceptor Lar e ionization ener : 1.3 eV Low formation energy undern-type
conditions Localized wavefunction
NOJ. L. Lyons, A. Janotti, and C. G. Van de
Walle, Appl. Phys. Lett.95, 252105 (2009).x a on = .Planar bonds = 1.94
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Test case:Test case: NN SeSe inin ZnSeZnSe
Similar semiconductor N known shallow
Zn-rich(0/-)
acceptor in ZnSe Effective p -type dopant NSe Results agrees well with
experimental values Theor : E = 150 meV Exp.: EA = 110-130 meV
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NNOO acceptor: Experimentacceptor: Experiment
coordinate diagram Absorption:2.4 eV 1.7 eV
NO0 to CB 2.4 eV = 520 nm Zero honon line at2.1 eV
Emission:electron falling from
o O eve 1.7 eV = 730 nm
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NNOO acceptor: experimentacceptor: experiment
Localization on N atom
Directed towards axial zincneighbor
W.E. Carlos, E.R. Glaser, and D.C., , . N. Y. Garces, N. C. Giles, L. E.
Halliburton, G. Cantwell, D. B. Eason,D. C. Reynolds, and D. C. Look,
Spin density of nitrogen state(Isosurface is 5% of maximum
density)
pp . ys. e . , .
Why nitrogen cannot lead to p-type conductivity in ZnO, J. L. Lyons, A. Janotti, and C.G. Van de Walle, Appl. Phys. Lett.95, 252105 (2009).
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TiOTiO22 in GGAin GGA--PBEPBE
Rutile
- p s a esCBM - Ti d states
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Hybrid functional calculations for TiOHybrid functional calculations for TiO22
HSE functional Heyd, Scuseria, & Ernzerhof, J. Chem. Phys.118 , 8207 (2003); erratum: J. Chem. Phys.124, 219906 (2006)
H-F mixing parameter 0.20;screenin arameter = 0.2 -1 PAW, VASP 5.1
72 atom-supercell -po n s: , , . , . , . ; es e or x x cutoff: tested for up to 400 eV
A. Janotti, J. B. Varley, P. Rinke, N. Umezawa, G. Kresse, andC. G. Van de Walle, Phys. Rev. B 81, 085212 (2010).
TiOTiO l il i
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TiOTiO22 -- structural propertiesstructural properties
PBE versus H EPBE versus H E Rutile
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Band structure of TiOBand structure of TiO 22
HSE can be tuned to reproduce the exp. band gap value
Eff t f HSE l b dEff t f HSE l b d
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Effects of HSE on valence bandEffects of HSE on valence band
versus conduction bandversus conduction band(determined from surface calculations)(determined from surface calculations)
HSE lowers the VBM by 0.6 eV and raises the CBM by 0.7 eV
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SingleSingle--particle states ofparticle states of VVOO in TiOin TiO22
unrelaxed vacancy induced single-particle states are in the gap
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SingleSingle--particle states ofparticle states of VVOO in TiOin TiO22re axe versus unre axe vacancyre axe versus unre axe vacancy
GGA cannot describe relaxed vacancy in 0 and +1 charge statesoccupied states above the CBM
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SingleSingle--particle states ofparticle states of VVOO in TiOin TiO22 versus y r unc onaversus y r unc ona
relaxed VO0
and VO+
can be described in HSE
Formation energies ofFormation energies of
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Formation energies ofFormation energies ofVV in TiOin TiO22unrelaxed
formation energy of +2 and +are lowered, consistent with thean a gnmen
Fermi level (eV)
Formation energies ofFormation energies of
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Formation energies ofFormation energies ofVV in TiOin TiO22unrelaxed
formation energy of +2 and +are lowered, consistent with the
relaxed
an a gnmen
relaxation energies for +2 aresimilar in PBE and HSE
transition levels (+2/0) and (+/0)are near the CBM
Fermi level (eV)
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Oxygen vacancy in TiOOxygen vacancy in TiO 22
shallow donor - can cause conductivity
low formation energy in O-poor conditions
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Summary and OutlookSummary and Outlook The field of defects in materials is active with
direct applications for many technologicallyimportant systems Much broader than merely point defects in semiconductors
been made on crucial issues: DFT band-gap errors
Still need for deeper physicalunderstanding
e erences verv ews J. Neugebauer and C. G. Van de Walle,J. Appl. Phys.95, 3851 (2004).