First-principles study on electronic and elastic properties of BN, AlN,
and GaN
Kazuhiro Shimada, Takayuki Sota, and Katsuo Suzuki
Citation: J. Appl. Phys. 84, 4951 (1998); doi: 10.1063/1.368739
View online: http://dx.doi.org/10.1063/1.368739
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Published by the American Institute of Physics.
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JOURNAL OF APPLIED PHYSICS VOLUME 84, NUMBER 9 1 NOVEMBER 1998
depending on a strain is indispensable. However there is
little information on these properties, especially deformation
potential constants, in spite of the fact that there have been
many theoretical3–5 and experimental6–8 results on them.
In recent work by Wright,9 all the elastic constants of
AlN, GaN, and InN for both zinc-blende ~ZB! and wurtzite
~WZ! structures were obtained from first-principles calcula-
tions based on the pseudopotential method. Kim et al.10,11
reported all the elastic constants of BN, AlN, GaN, and InN
using the full potential linear muffin tin orbital ~FP-LMTO!
method. Kato and Hama12 reported their work on elastic con-
stants of WZ–AlN using the pseudopotential method.
Majewski et al.4 and Kim et al.5 have obtained the de-
formation potential constants for WZ crystal D3 and D4 in
the Bir–Pikus notation by using the FP-LMTO and pseudo-
potential methods within the local density approximation, re-
spectively. Among recent calculations for deformation po-
important role in InGaN quantum wells.13 However there are
only a few reports on the WZ piezoelectric constants14,15 and
those of ZB,16–19 and there is still no work which calculated
many physical quantities of ZB and WZ BN, AlN, and GaN
systematically, including piezoelectric constants with the
same accuracy by using the pseudopotential-plane-wave
method.
It has been known that the physical parameters of them
with the WZ structure sensitively depend on the cell shape
and the atomic geometry. Thus in calculating the above men-
tioned values of their various physical parameters, the opti-
mization of the crystal structure is indispensable.
In this article, we report on the systematic study of the
electronic and elastic properties of BN, AlN, and GaN in
both ZB and WZ structures. We have performed first-
principles calculations using the molecular dynamics method
with variable cell shapes20 to optimize their unit cell struc-
tures. To find the equilibrium positions of atoms in a strained
crystal, we have carried out first-principles molecular dy-
namics calculation. Discussions on calculated results are
given in comparison with the previous computational and
a!Also at Material Research Laboratory for Bioscience and Photonics,
Graduate School of Science and Engineering, Waseda University, Shin-
juku, Tokyo 169-8555, Japan; electronic mail: sota@elec.waseda.ac.jp
b!Also at: Kagami Memorial Laboratory for Material Science and Technol-
ogy, Waseda University, Shinjuku, Tokyo 169-8555, Japan.
First-principles study on electronic an
of BN, AlN, and GaN
Kazuhiro Shimada, Takayuki Sota,a) and Katsuo
Department of Electrical, Electronics, and Computer Engi
Shinjuku, Tokyo 169-8555, Japan
~Received 15 May 1998; accepted for publication 4 A
We have carried out first-principles total energy cal
properties of both zinc-blende and wurtzite BN, A
parameters, elastic constants, deformation potential c
effective charges, and piezoelectric constants. Lattic
first-principles molecular dynamics method with varia
crystal is also relaxed by the first-principles mole
influences the elastic constants, the deformation poten
effectively. We have calculated the wurtzite deformati
internal strain correction. The piezoelectric constants
been calculated using the Berry phase approach and w
of BN have an inverse sign in contrast to AlN and G
with results obtained herein with the previous ones.
@S0021-8979~98!07921-3#
I. INTRODUCTION
AlN and GaN are promising materials for applications
in optoelectronics in the short wavelength range, light emit-
ting diode and laser diode, and BN is for the extreme hard-
ness and high thermal conductivity electronics devices. Re-
cently there has been much interest in III nitrides and their
alloys because of the potential for fabrication of a light
emitter.1,2 These materials grown on sapphire suffer a biaxial
strain because of the lattice mismatch. In modeling these
electronics devices, knowledge of their elastic constants, de-
formation potential constants, and energy band information
4950021-8979/98/84(9)/4951/8/$15.00
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elastic properties
uzukib)
ering, Waseda University, 3-4-1 Ohkubo,
gust 1998!
lations to investigate electronic and elastic
N, and GaN. We have calculated lattice
stants, phonon frequencies at G point, Born
parameters are fully relaxed by using the
e cell shape. The internal strain in a strained
lar dynamics method. The internal strain
al constants, and the piezoelectric constants
potential constants D1 – D5 considering the
wurtzite and also zinc-blende crystals have
have found from first principles that those
. Discussions will be given in comparison
1998 American Institute of Physics.
tential constants, only Suzuki and Uenoyama3 have obtained
all of the deformation potential constants D1 – D6 at the Bril-
louin zone center based on the linearized augmented plane
wave method together with a cubic approximation. However
their calculation has not relaxed the internal strain which
plays an important role in determining the deformation po-
tential constants and the elastic constants. Their results are
not satisfactory in comparison with experimental values by
Shikanai et al.6 and by Yamaguchi et al.7,8
It has been pointed out that the piezoelectric field, aris-
ing from the residual strain due to lattice mismatch, plays an
1 © 1998 American Institute of Physics
license or copyright; see http://jap.aip.org/about/rights_and_permissions
experimental results. This work is an extension of our previ-
ous publication.21
II. COMPUTATIONAL METHOD
We have performed first-principles total energy calcula-
tions for BN, AlN, and GaN within the local density approxi-
mation ~LDA! to the density functional theory22 ~DFT!. The
pseudopotentials are generated through the Troullier–
Martins scheme23 in the nonrelativistic limit and are cast into
the Kleinman–Bylander24 separable form to save computa-
tional time and memory. For each pseudopotential, the loga-
rithmic derivatives are examined by using the criteria devel-
oped by Gonze, Stumpf, and Scheffler25 to eliminate the
appearance of unphysical states well known as the ‘‘ghost
states.’’ For exchange–correlation potential we have used
the Ceperley–Alder26 type parametrized by Perdew and
Zunger.27 The Kohn–Sham equation is solved iteratively
with the eigenvalue minimization scheme.28 The Brillouin
zone k integration has been performed by the special-points
method of Chadi and Cohen.29 We have used ten special k
points for zinc blende-structure and six special k points for
WZ structure in the irreducible wedge of the Brillouin zone.
To treat the deep N 2p and Ga 3d potential, we have to
take large energy cutoffs ~90 Ry for BN and GaN, 80 Ry for
AlN! to eliminate computational uncertainties. These cutoff
energies give good convergence of both total energy and
pressure.30
III. RESULTS
A. Structural optimization
The calculations were first carried out assuming ideal ZB
and WZ structures. For WZ structures, the axis ratio c/a
51.633 and the internal parameter u50.375 were used. The
calculated total energies and pressures for several lattice con-
stants were fitted with the empirical Murnaghan equation of
state31 to obtain equilibrium lattice constants. For ZB struc-
tures, the forces acting on atoms and the elements of the
stress tensor have converged within 1025 and 1026 Ry/a.u.3,
respectively. For WZ structures, the values of the various
physical parameters depend sensitively on the shape of the
unit cell and the atomic geometry, and, thus, structural opti-
mization is needed as mentioned before. Starting from the
resulting ideal atomic geometry, the crystal structure optimi-
TABLE I. Lattice constants of ZB–BN, AlN, and GaN in units of Å.
BN AlN GaN
Present 3.596 4.376 4.537
Other calculations 3.56–3.77a 4.33–4.42b 4.30–4.56c
Experimentd 3.615, 3.6157e 4.37, 4.38f 4.50,g 4.51h
aReferences 10, 47–55. eReference 45.
bReferences 10, 37, 56–59. fReference 66.
cReferences 10, 37, 55, 58, 60–63. gReference 67.
dReference 64. hReference 68.
4952 J. Appl. Phys., Vol. 84, No. 9, 1 November 1998
zation has been iterated using the first-principles molecular
dynamics method with variable cell shape20 until the forces
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acting on atoms and the elements of the stress tensor have
converged within 1024 and 1026 Ry/a.u.3, respectively.
Tables I and II summarize the results of our calculations
for lattice parameters. Because there are so many results for
ZB structure, we only show the range of the results. For WZ
structure, only fully relaxed calculations are listed in Table
II. Our results agree very well with the experimental data.
The lattice constants of GaN are overestimated by about 1%.
This comes from the fact that we have considered Ga 3d
electrons as valence states. If these electrons are considered
as core states, lattice constants are underestimated by a few
percent.
B. Elastic constants
The values of the elastic constants are obtained by cal-
culating the full stress tensor for small strains within the
harmonic approximation. The ZB elastic constants C11 and
C12 are obtained with the relations C115s1 /e1 , C12
5s2 /e1 , where s is the stress tensor and e is the strain
32
TABLE II. Lattice constants of WZ–BN, AlN, and GaN. a and c are in
units of Å.
BN AlN GaN
Present a 2.534 3.112 3.210
c 4.191 4.995 5.237
c/a 1.654 1.605 1.631
u 0.3738 0.3811 0.3762
Other calculationsa a 2.54 3.06 3.17
c 4.17 4.91 5.13
c/a 1.64 1.60 1.62
u 0.375 0.383 0.379
Other calculationsb a fl 3.084 3.162
c fl 4.948 5.142
c/a fl 1.604 1.626
u fl 0.3814 0.3770
Other calculationsc a 2.531 3.082 3.143
c/a 1.657 1.605 1.626
u 0.3751 0.3816 0.377
Other calculationsd a fl 3.10 3.22
c fl 4.97 5.26
u fl 0.381 0.371
Experimente a 2.558 fl fl
c 4.228 fl fl
c/a 1.656 fl fl
Experimentf a fl 3.11 3.189
c fl 4.98 5.185
c/a fl 1.60 1.626
Experimentg a fl 3.110 3.190
c fl 4.980 5.189
c/a fl 1.601 1.627
u fl 0.3821 0.377
aFP-LMTO by Kim et al., Ref. 10.
bPseudopotential LDA by Wright and Nelson, Ref. 59.
cPseudopotential LDA by Karch and Bechstedt, Refs. 91, 92.
dSIC-Pseudopotential by Vogel et al., Ref. 63.
eSoma et al., Ref. 45.
fReference 64.
gSchulz and Thiemann, Ref. 46.
Shimada, Sota, and Suzuki
tensor. Voigt notation is used for the tensorial component.
The calculation of the elastic constants C44 is not as simple
license or copyright; see http://jap.aip.org/about/rights_and_permissions
as that of C11 and C12 . For a dilation along the @111# axis,
the atomic positions in the unit cell are no longer determined
by symmetry, and one has to find the atomic positions where
the forces acting on atoms vanish. Following Nielsen and
Martin,30 C44 is determined by an independent calculation of
the forces and the stresses. Bulk moduli are obtained by us-
ing the relation B5(C1112C12)/3. Table III also lists the
values of B in square brackets calculated by Murnaghan’s
equation of state.
Experimental data of the elastic constants for the ZB
structure are available only for BN and our results are in
good agreement with the experimental data to within a few
%. The other calculations predict nearly the same value
within a few percent compared with ours except for
Sokolovskii’s results.33 Our value of internal strain param-
eter of ZB–BN is larger than the others by about 50%. For
ZB–AlN and ZB–GaN, there are no experimental data and
there are several other calculations. Our calculations are all
in good agreement with the others except for Ruiz’s results.34
In a WZ crystal, any strain makes the forces acting on
atoms finite. To delete these forces, the optimization of the
atomic position was performed by using the first-principles
TABLE III. Elastic constants, internal strain parameters, and bulk moduli of
ZB–BN, AlN, and GaN. Elastic constants and bulk moduli are in units of
GPa. The values in parentheses are calculated without internal strain correc-
tion. The values in square brackets are obtained from Murnaghan’s equation
of state.
C11 C12 C44 z B
BN Present 819 195 475 0.16 403
fl fl ~483! fl @401#
Expt.a 820 190 480 fl 400
Calc.b 837 182 493 0.1 400
fl fl ~495! fl @400#
Calc.c 830 420 450 fl 556
Calc.d 844 190 483 0.11 410
fl fl ~486! fl @386#
Calc.e 812 182 464 0.07 397
fl fl ~466! fl fl
AlN Present 313 168 192 0.56 216
fl fl ~236! fl @216#
Calc.b 304 152 199 0.6 203
fl fl ~230! fl @203#
Calc.f 348 168 135 fl 228
Calc.g 304 160 193 0.55 208
fl fl ~237! fl fl
Calc.e 294 160 189 0.57 214
fl fl ~233! fl fl
GaN Present 285 161 149 0.67 202
fl fl ~202! fl @203#
Calc.b 296 154 206 0.5 201
fl fl ~225! fl @201#
Calc.g 293 159 155 0.61 203
fl fl ~200! fl fl
aGrimsditch et al., Ref. 69.
bFP-LMTO LDA by Kim et al., Ref. 10.
cSemiempirical by Sokolovskii, Ref. 33.
dPseudopotential LDA by Rodriguez-Herna´ndez et al., Ref. 54.
ePseudopotential LDA by Karch and Bechstedt, Ref. 91.
fHartree–Fock by Ruiz et al., Ref. 34.
gPseudopotential LDA by Wright, Ref. 9.
J. Appl. Phys., Vol. 84, No. 9, 1 November 1998
molecular dynamics method. After this optimization, the
forces are converged within 1024 Ry/a.u.. Induced strains in
Downloaded 21 Nov 2011 to 221.212.116.13. Redistribution subject to AIP
calculating the values of elastic constants for WZ crystals are
e5$e100000% for C11 , C12 , and C13 , e5$00e3000% for C13
and C33 , and e5$000e4e5e6% with e45e55e6 for C44 and
C66 . The results are listed in Table IV. The values in paren-
theses are obtained without internal strain correction. It is
shown that the internal strain corrects the values of the elas-
tic constants explicitly. The bulk moduli of ZB crystals are
determined by the Murnaghan equation fitting for total ener-
gies and pressures of several lattice constants, and those of
WZ are calculated using the following relation:
B5
C33~C111C12!22~C13!2
C111C1212C3324C13
. ~1!
For WZ structure, there is only one result calculated
from first principles for all elastic constants.9 Kim et al.10,11
have calculated only C33 directly from first principles, and
other elastic constants are obtained by using Martin’s trans-
formation method.35 For BN and AlN, our results indicate
TABLE IV. Elastic constants of WZ–BN, AlN, and GaN in units of GPa.
The values in parentheses are calculated without internal strain correction.
C11 C12 C13 C33 C44 C66 B
BN Present 982 134 74 1077 388 424 401
~998! ~127! ~73! ~1076! ~397! ~436! ~402!
Calc.a 987 143 70 1020 369 422 395
AlN Present 398 142 112 383 127 128 212
~474! ~106! ~68! ~478! ~147! ~184! ~212!
Expt.b 345 125 120 395 118 110 fl
Expt.c 411 149 99 389 125 131 fl
Calc.a 398 140 127 382 96 129 218
Calc.d 380 114 127 382 109 133 207
Calc.e 396 137 108 373 116 fl 207
GaN Present 350 140 104 376 101 115 197
~420! ~110! ~66! ~448! ~119! ~156! ~197!
Expt.f 365 135 114 381 109 115 fl
Expt.g 377 160 114 209 81.4 109 fl
Expt.h 390 145 106 398 105 123 fl
Calc.a 396 144 100 392 91 126 207
Calc.e 367 135 103 405 95 fl 202
aFP-LMTO LDA by Kim et al., Ref. 10.
bTsubouchi and Mikoshiba, Ref. 15.
cMcNeil et al., Ref. 75.
dPseudopotentail LDA by Kato and Hama, Ref. 12.
ePseudopotential LDA by Wright, Ref. 9.
fBrillouin scattering by Yamaguchi et al., Ref. 79.
gResonance ultrasound by Schwarz et al., Ref. 80.
hBrillouin scattering by Polian et al., Ref. 81.
TABLE V. Deformation potential constants b and d of ZB–BN, AlN, and
GaN in units of eV. The Bir–Pikus notation is used. The values in paren-
theses are calculated without internal strain correction.
BN AlN GaN
Present Calc.a Present Calc.a Present Calc.a
b 23.41 23.4 21.44 21.4 21.62 21.6
d 23.75 23.3 25.02 25.3 24.03 23.7
(22.19) (22.3) (23.04) (23.3) (22.12) (22.4)
4953Shimada, Sota, and Suzuki
aFP-LMTO LDA by Kim et al., Ref. 10.
license or copyright; see http://jap.aip.org/about/rights_and_permissions
good agreement w
tions. For GaN, o
percent compared
C. Deformation
The values o
obtained in a wa
constants. We ha
pute the values o
spin orbit interact
dilation along the
DE52b~e32
Under a dilation
DE5
)
de4 . ~3!
lN
A
6
fl
2,j
, R
f WZ–BN, AlN, and
The values in paren-
.
D4 D5
23.32 24.30
(22.04) (23.01)
23.92 23.36
(21.94) (22.49)
(22.04) (22.59)
24.8 fl
24.10 fl
fl fl
23.25 22.85
(21.61) (22.04)
24.41 fl
23.4 23.3
23.6 fl
Expt. 22 fl fl fl fl fl
Expt.i 11 fl fl fl fl fl
4954 J. Appl. P , Sota, and Suzuki
6
Here b and d are the deformation potential constants of ZB
crystals. For WZ structure, assuming that D25D350 and
e45e55e650, a 636 strain Hamiltonian leads to three
doubly degenerated states:
E15D1e31D2~e11e2!, ~4!
E2,35Dcr1~D11D3!e31~D21D4!~e11e2!
6D5~e12e2!. ~5!
Here D2 and D3 denote the spin orbit splittings, Dcr is the
crystal field splitting, and D1 – D5 are the deformation poten-
tial constants of WZ crystals. From these equations, energy
shifts under a strain are as follows:
E1!E11D1e31D2~e11e2!, ~6!
Dcr!Dcr1D3e31D4~e11e2!. ~7!
From Eqs. ~5!, ~6!, and ~7!, D1 – D5 are obtained directly
under uniaxial strain.
The results are listed in Tables V and VI. Experimental
data are only available for WZ–GaN to our knowledge. The
values in parentheses are obtained without internal strain
correction. It can be found that the internal strain plays a
TABLE VII. Optical phonon frequencies of ZB–BN, A
of cm21.
BN
Present 1082
Experiment 1056a,b
Other calculations 1000,f 1070g,h 648,i 65
aReference 64.
bRaman data by Alvarenga et al., Ref. 65.
cRaman data by Murugkar et al., Ref. 86.
dRaman data by Tabata et al., Ref. 87.
eRaman data by Siegle et al., Ref. 88.
fPseudopotential LDA by Lam et al., Ref. 51.
gFP-LMTO LDA by Kim et al., Ref. 10.
hPseudopotential LDA by Rodriguez-Herna´ndez et al.
iMixed basis LDA by Miwa and Fikumoto, Ref. 37.
jFP-LMTO LDA by Gorczyca et al., Ref. 38.
kFP-LMTO LDA by Fiorentini et al., Ref. 89.
lPseudopotential LDA by Karch et al., Ref. 90.
mPseudopotential LDA by Wright, Ref. 9.
Downloaded 21 Nov 2011 to 221.212.116.13. Redistribution subject to AIP
significant role in calculating the deformation potential con-
stants. Especially for the ZB shear deformation potential
constant d , the WZ deformation potential constants D3 , and
D4 , the values are nearly twice as large as the values calcu-
lated without internal