Solid electrolytes for battery applications –
a theoretical perspective*
N. A. W. Holzwarth**
Wake Forest University, Winston-Salem, NC, USA, 27109
• Motivation and background information
• Overview of computational methods
• Some representative results
*Supported by NSF Grants DMR-0705239 and DMR-1105485.
**With help from Nicholas Lepley (graduate student) and
previously, Yaojun Du (postdoc).
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Materials components of a Li ion battery
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Example: Thin-film battery developed by Nancy Dudney and
collaborators at Oak Ridge National Laboratory – LiPON
(lithium phosphorus oxinitride)
From: N. J. Dudney, Interface 77(3) 44 (2008)
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Solid vs liquid electrolytes in Li ion batteries
1.
2.
3.
1.
2.
3.
Advantages
Solid electrolytes
Excellent chemical and physical
stability.
Perform well as thin film (≈1µ)
Li+ conduction only (excludes
electrons).
Advantages
2.
3.
Reduced contact area for high capacity
electrodes.
Interface stress due to electrode
charging and discharging.
Relatively low ionic conductivity.
Liquid electrolytes
Excellent contact area with high
capacity electrodes.
Can accommodate size changes of
electrodes during charge and
discharge cycles.
Relatively high ionic conductivity.
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1.
1.
2.
3.
Disadvantages
Disadvantages
Relatively poor physical and chemical
stability.
Relies on the formation of “solid
electrolyte interface” (SEI) layer.
May have both Li+ and electron
conduction.
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Motivation: Paper by N. Kayama, et. al in Nature Materials 10, 682-686 (2011)
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Motivation: Paper by N. Kamaya, et. al in Nature Materials 10, 682-686 (2011)
LiPON
RT
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Motivation: Paper by N. Kamaya, et. al in Nature Materials 10, 682-686 (2011)
Li7P3S11
RT
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Motivation: Paper by N. Kamaya, et. al in Nature Materials 10, 682-686 (2011)
Li10GeP2S12
RT
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How can computer simulations contribute
to the development of materials?
 Examine known materials and predict new materials
 Structural forms
 Relative stabilities
 Analyze vibrational modes and other experimentally
accessible properties
 Model ion migration mechanisms
 Vacancy migration
 Interstitial migration
 Vacancy-interstitial formation energies
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Summary of “first-principles” calculation methods
Electronic coordinates
Exact problem :
Atomic coordinates
H ({ri }, {R a }) Ψα ({ri }, {R a }) = Eα Ψα ({ri }, {R a })
Born-Oppenheimer approximation
Born & Huang, Dynamical Theory of Crystal Lattices,
Oxford (1954)
Density functional theory
Hohenberg and Kohn, Phys. Rev. 136 B864 (1964)
Kohn and Sham, Phys. Rev. 140 A1133 (1965)
Approximately equivalent problem :
Ground state energy : E0 (r, ρ (r ),{R a })
ρ (r ) = ∑ ψ n (r )
n
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H eff (r, ρ (r ),{R a })ψ n (r ) = ε nψ n (r )
a
E
(
,
(
),
{
})
r
r
R
δ
ρ
H eff (r, ρ (r ),{R a }) = 0
δρ (r )
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More computational details:
 2∇ 2
− Z ae2
ρ (r ' )
2
3
a
H eff (r, ρ (r ),{R }) = −
+∑
+ e ∫ d r'
+ Vxc (ρ (r ) )
a
2m
r − r'
a r−R
electron-nucleus electron-electron exchangecorrelation
Exchange-correlation functionals:
LDA: J. Perdew and Y. Wang, Phys. Rev. B 45, 13244 (1992)
GGA: J. Perdew, K. Burke, and M. Ernzerhof, PRL 77, 3865 (1996)
HSE06: J. Heyd, G. E. Scuseria, and M. Ernzerhof, JCP 118, 8207 (2003)
Numerical methods:
“Muffin-tin” construction: Augmented Plane Wave developed
by Slater  “linearized” version by Andersen:
J. C. Slater, Phys. Rev. 51 846 (1937)
O. K. Andersen, Phys. Rev. B 12 3060 (1975) (LAPW)
Pseudopotential methods:
J. C. Phillips and L. Kleinman, Phys. Rev. 116 287 (1959) -- original idea
P. Blöchl, Phys. Rev. B. 50 17953 (1994) – Projector Augmented Wave (PAW)
method
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Outputs of calculations:
Ground state energy :
E0 (r , ρ (r ),{R a })
(
min {R a } E0 (r , ρ (r ),{R a })
)
⇒ Determine formation energies
⇒ Determine structural parameters
⇒ Stable and meta - stable structures
⇒ Normal modes of vibration
ρ (r ) = ∑ ψ n (r )
n
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{ε n }
2
⇒ Self - consistent electron density
⇒ One - electron energies; densities of states
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Estimate of ionic conductivity assuming
activated hopping
:
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Public domain codes available for electronic
structure calculations
Method
Codes
Comments
LAPW
www.wien2k.at
elk.sourceforge.net
Works well for smaller unit cells;
variable unit cell optimization not
implemented. Need to choose nonoverlapping muffin tin radii and avoid
“ghost” solutions.
PAW
www.abinit.org
www.quantum_espresso.org
Works well for large unit cells (<200
atoms or so); includes variable unit
cell optimization. Need to construct
and test PAW datasets
Other efforts:
• Gerbrand Ceder’s group at MIT – Materials Project; A
Materials Genome Approach -http://www.materialsproject.org/
• Stefano Curtarolo’s group at Duke – Energy Materials
Laboratory -- http://materials.duke.edu/
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Code for generating atomic datasets for PAW calculations
Holzwarth, Tackett, and Matthews, CPC 135 329 (2001) http://pwpaw.wfu.edu
Datasets can interface with abinit, quantum-espresso, and other codes.
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Validation of calculations
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Ball and stick models of Li3PO4 crystals
O
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P
Li
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Systematic study of LiPON materials -- LixPOyNz
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Other electrolyte materials -- thiophosphate
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“Superionic conductor” Li7P3S11
Meta-stable to decomposition:
Li7P3S11Li3PS4+Li4P2S6+S


Activation energy estimate:
EA ≈ 0.2 eV (Exp. 0.1 eV)

Interstitial-vacancy
pair formation
energy Ef ≈ 0
Yamane et al, Solid State Ionics 178 1163 (2007)
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Li10GeP2S12 – preliminary results
Other simulation studies on this material:
Work by MIT group published in Dec. 2011
dx.doi.org/10.1021/cm203303y | Chem. Mater. 2012, 24, 15−17
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Constituents of Li10GeP2S12:
α* - Li3 PS4 Pbcn
β * − Li3 PS4 Pnma
γ * − Li3PS4 Pmn21
∆H = −8.12 eV
∆H = −8.28 eV
∆H = −8.36 eV
S
Li
P
Ge
Li 4 GeS4
Pnma
∆H = −10.19 eV
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**
*K. Homma et al, Solid State Ionics 182, 53-58 (2011)
**M. Murayama et al, Solid State Ionics 154-155, 789794 (2002)
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Li10GeP2S12
Space group P42/nmc (#137)
(from experiment)
c
b
b
a
S
Li
P
Ge
c
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Lattice parameters
a (Å)
8.72
8.56
8.55
Li10GeP2S12 (exp*)
Li10GeP2S12 (Calc)
Li10SiP2S12 (Calc)
c (Å)
12.63
12.23
12.16
*Kamaya et al, Nature Materials 10, 682-686 (2011)
Experimentally determined symmetry (fractional occupancy):
Space group P42/nmc (#137)
Optimized structure with full occupancy:*
Space group P42mc (#105)
( x, y , z ) → ( y , x, − z )
*Determined using FINDSYM written by Stokes, Campbell, and Hatch at Brigham Young U. –
http://stokes.byu.edu/iso/
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Calculated structure:
Space group P42mc (#105)*
Experiment structure:
Space group P42/nmc (#137)
Atom
g
x
y
z
Li(1) 16h
0.69
0.26
0.27
0.18
Li(2) 4d
1.00
0.00
0.50
Li(3) 8f
0.64
0.25
Ge(1) 4d
0.52
P(1)
4d
Atom
g
x
y
z
Li(1) 8f
1.00
0.23
0.23
0.29
0.94
Li(2) 2a/2b
1.00
0.00
0.50
0.94
0.25
0.00
Li(3) 8f
1.00
0.26
0.22
0.03
0.00
0.50
0.69
Ge(1) 2b
1.00
0.50
0.00
0.79
0.49
0.00
0.50
0.69
P(1)
2a
1.00
0.00
0.50
0.68
Ge(2) 2b
0.00
0.00
0.00
0.50
P(2)
2b
1.00
0.00
0.00
0.50
P(2)
2c
1.00
0.00
0.00
0.50
S(1)
8g
1.00
0.00
0.18
0.41
S(1) 4d/4e
1.00
0.00
0.20
0.41
S(2)
8g
1.00
0.00
0.30
0.10
S(2) 4d/4e
1.00
0.00
0.30
0.09
S(3)
8g
1.00
0.00
0.70
0.79
S(3) 4d/4e
1.00
0.00
0.70
0.78
*Wyckoff symbols for #105, coordinates
in #137 convention.
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Decomposition reactions predicted on the basis of
calculated enthalpies of formation (at zero temperature)
∆H (eV)
Li10 GeP2S12 → 2Li3 PS4 + Li 4 GeS4
0.77
Li10SiP2S12 → 2Li3 PS4 + Li 4SiS4
Li13GeP3S16 → 3Li3 PS4 + Li 4 GeS4
Li13SiP3S16 → 3Li3 PS4 + Li 4SiS4
0.74
0.55
0.62
Preliminary results for formation enthalpies from zerotemperature simulations predict all of the compounds to be
unstable with respect to their constituents.
Work continuing to investigate Li ion migration energies.
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Summary and conclusions
 Ideal research effort in materials includes close collaboration
of both simulations and experimental measurements.
 For battery technology, there remain many opportunities for
new materials development.
 Case studies carried out by our group for solid electrolyte
materials including Li phosphorus oxinitrides, Li
thiophosphates, and very preliminary results for materials
containing thiogerminates.
Some workshops for “first-principles” public domain codes
 WIEN2k Workshop 9/3/2012 Tokyo, Japan
 Quantum Espresso Workshop 6/25/2012 Penn State U.
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