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Chapter-4_________________________________________________________
_____________________________________________________________________Shyamkumar G. Khambholja / Ph.D. Thesis/ Physics/ S.P. University/ April-2012
111
Chapter 4
Finite Temperature
Thermophysical Properties of
Solids
J. Nano Ele. Phys. 3 (2011) 884.
J. Phy. Conference Series (in press).
Communicated in Chinese Physics Letters (IOP Pub.).
Communicated in Advances Materials Research.
4.1 Introduction 112
4.2 The quasi harmonic Debye model 113
4.3 Results 116
4.4 Conclusions 173
4.5 References 176
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112
4.1 Introduction
In the previous chapter, we have discussed results of the ground state and high
pressure structural and lattice mechanical properties of solids. In the present chapter,
we report the study of finite temperature thermophysical properties of carbides,
fluorides and oxides compounds. The detail of the calculations used to compute the
finite temperature thermophysical properties of solid compounds is given below.
The study of thermodynamic properties of materials is important from several
points of views. It is important not only to elucidate interactions among the particles
that are essential, but to extend our knowledge on their specific behaviors, when
undergoing several constraints such as high temperatures and/or high pressures. This
is particularly true, since from modern technology one always expects new advances
and innovation of materials to reach higher performances. With a realization of these
situations, a great deal of efforts has been made in recent years on the thermophysical
properties at an extreme environment. The thermal expansion of materials arises from
the anharmonicity of the interatomic potential. Such a change is accompanied by
change in elastic, vibrational and mechanical properties. There are mainly two issues
regarding the calculation of finite temperature thermophysical properties of materials.
The first one is the calculation of cohesive properties at ambient condition, which in
the present work is performed using plane wave pseudopotential density functional
theory as implemented in the Quantum ESPRESSO code [1]. The theoretical method
used for the calculation of cohesive properties at ambient condition is already
described in the previous chapter. Once the cohesive properties at ambient conditions
are obtained, the another issue is the inclusion of effect of temperature. The equation
of state (eos) and chemical potential are the two key thermodynamic properties of
solid. Theoretically, the determination of eos and chemical potential are obtained
using standard thermodynamic relations. According to standard thermodynamics, if
the system is held at fixed temperature T and hydrostatic pressure P, then the
equilibrium state is one that minimize the availability of the non-equilibrium Gibbs
energy, given by [2],
* ( ; , ) = ( ) ( ) + ( ; )vibG x p T E x pV x A x T+ (4.1)
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with respect to all internal configuration parameters. These configuration parameters,
gathered in the configuration vector x, include all the relevant geometric information
for the given crystal structure i.e. independent of unit cell lengths and angles of this
phase, and all the crystallographic coordinates of the atoms is non-fixed Wyckoff
positions. On the right side of above equation (4.1), the first term gives the cohesive
energy of the system. The second term gives the corresponding hydrostatic pressure
and the third term gives the vibrational Helmoltz free energy, which includes both the
vibrational contribution to the internal energy and the constant temperature condition
term. For the calculation of vibrational Helmoltz free energy, exact knowledge of
vibrational states is required. In the quasi harmonic approximation, it is given by [2],
0
1( ; ) = + ln(1 ) ( ; )
2kT
vibA x T kT e g x dω
ω ω ω∞ −
−
∫h
h (4.2)
The quasi harmonic approximation is not like the rigid harmonic approximation
[3]. But, it allows the inclusion of effect of temperature through the volume
dependence of phonon frequencies and corresponding density of states.
Thus, it is clear that for the calculation of thermodynamic properties, one requires
the exact knowledge of( )E x , ( )V x and ( ; )g x ω . Once, these quantities are obtained,
minimization of Gibbs free energy leads to all thermodynamic properties.
4.2 The quasi harmonic Debye model
The quasi harmonic Debye model starts with the calculation of cohesive
energy of the system at ambient condition. Before the quasi harmonic Debye model
starts, the multivariable surface has to be transformed into a ( )E V curve. In the
present work, the multivariable surface is transformed into a ( )E V curve, by
minimizing ( )E x for a set of fixed volumes. In the present work, calculation of
cohesive energy is performed using plane wave pseudopotential density functional
theory.
After the static calculation, equation (4.1) can be rewritten as,
* ( ( ); , ) = ( ( )) + + ( ( ); )opt opt vib optG x V p T E x V pV A x V T (4.3)
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which is a function of ( ; , )V p T only. The vibrational contribution is written in terms
of Debye model as [2],
9( ; ) = + 3 ln(1 )
8T
vibA T nkT e DT T
θθ θθ− − −
(4.4)
Here, ( )D y is the Debye integral given by,
3
30
3( ) =
1
y
x
xD y dx
y e −∫ (4.5)
Here, = yT
θ and θ is the Debye temperature and n is number of atoms. Debye
temperature in the solid is related to the average sound velocity in solids and can be
calculated from the Poisson’s ratio using the formula given by [2],
1/32 1/2 = 6 ( ) s
B
BV n f
k Mθ π σ
h (4.6)
Where, ( )f σ is given by,
1/313/2 3/22 1 1 1
( ) 3 2 + 3 1 2 3 1
fσ σσσ σ
− + + = − −
(4.7)
Poisson’s ratio is the most important input quantity in the present calculation.
Experimental values of Poisson’s ratio of carbides, fluorides and oxides are used for
the calculation of thermodynamic properties.
Adiabatic bulk modulus sB can be calculated from the static compressibility relation,
given by [2],
=
===
2
2
2
2)(
))((
))(( )( dV
VEdV
dV
VxEdVVxBxBB
optoptstaticstatics (4.8)
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By minimizing the Gibbs function, with respect to volume at given temperature, one
can obtain thermal expansion, using,
*
,
( ; , ) = 0
p T
G V p T
V
∂ ∂
(4.9)
Isothermal bulk modulus can be obtained by,
( , ) - TT
pB p T V
V
∂ = ∂ (4.10)
To simplify the process of minimization, the calculated energies are fitted to the Birch
equation of state [2]. All the calculation of the thermodynamic properties of solids are
carried out using quasi harmonic Debye model as implemented in GIBBS program,
originally created by Blanco et al [2]. In the code, three different forms of equation of
states namely, due to Vinet et al, Birch-Murnaghan et al and the spinodal are given.
Other thermodynamic properties namely, heat capacity and thermodynamic Grüneisen
parameter are calculated using following relations [2],
, /
3 / = 3 4 -
1v vib B T
TC nk D
T eθθ θ −
(4.11)
ln ( ) -
ln
d V
d V
θγ = (4.12)
More details about the algorithm of the GIBBS code can be found out in the paper by
Blanco et al [2].
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Table 4.1 List of Poisson’s ratio used in the present calculations.
Materials Poisson’s ratio References
SiC 0.216 [4]
GeC 0.16 [5]
SnC 0.21 [6]
ZrC 0.28 [7]
LiF 0.216 [8]
NaF 0.174 [9]
CaO 0.207 [10]
SrO 0.21 [11]
BaO 0.292 [12]
CdO 0.419 [13]
4.3 Results
Carbides
(1) Silicon Carbide (SiC)
Very few theoretical studies of finite temperature thermophysical properties of
SiC are available [14-17]. In an earlier work, Karch et al [14] have calculated the
thermophysical properties of 3C-SiC using density functional theory within local
density approximation (LDA) in conjunction with quasi harmonic approximation
(QHA). Vashistha et al [15] have calculated thermophysical properties of 3C-SiC
using molecular dynamics simulation. Vardachari et al [17] have calculated the
structural properties of 3C-SiC using full potential linear augmented plane wave
method (FP-LAPW). Further, they have calculated the finite temperature
thermophysical properties using harmonic approximation. We in the present work
have calculated the thermophysical properties of 3C-SiC using plane wave
pseudopotential density functional theory [1] in conjunction with quasi harmonic
Debye model [2]. The details of the ground state properties are already given in the
previous chapter. So, we report here directly the results of thermophysical properties
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of 3C-SiC. The value of Poisson’s ratio is taken from the Reference [4] and is shown
in Table 4.1. Figure 4.1 shows the calculated equilibrium lattice constants at various
temperatures along with experimental and other theoretical results. The experimental
results [18] are available in the limited range of temperature. On the other hand,
results of molecular dynamic simulation [15] are available upto the melting point
( ≈ 3100 K) of 3C-SiC. The presently calculated value of lattice constants shows a
little deviation of only from the experimental results. On the other hand, it shows very
good agreement with the molecular dynamic simulation results of Vashistha et al [15].
Moreover, the trend of the variation of lattice constant with temperature is also similar
to that of molecular dynamics results. The presently calculation of lattice constants
also indicate that at high temperatures, anharmonic effects plays prominent role.
Figure 4.1. Calculated equilibrium lattice constant of SiC at various temperatures
(full line), experimental results (dots) [18], molecular dynamics results (dots with
dashed line) [15] and results of Tang and Yip (open circle) [19].
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Figure 4.2. Thermal equation of state of ZB-SiC at ambient condition (full line), 500
K (dashed line), 1000 K (dotted line) and experimental results (filled
dots) [20].
Figure 4.2 shows the presently calculated thermal equation of state (eos) at
various temperatures along with experimental results [20] at zero temperature. All the
features of thermal expansion at finite temperatures are observed in the Figure 4.2. A
good agreement is observed. Figure 4.3 shows the presently calculated phonon
dispersion relation at ambient condition and at finite temperatures. At finite
temperatures, phonon dispersion is calculated in a quasi harmonic way. At finite
temperatures, phonons in 3C-SiC becomes soft along all symmetry directions.
However, the decrease in phonon frequencies with temperatures is not much high.
This indicates that the temperature coefficient of elastic constants should be small, as
the phonon frequencies along [100] and [110] planes are directly related to the elastic
stiffness constants. Figure 4.4 shows the quasi harmonic phonon density of states (p-
dos) of 3C-SiC at ambient conditions and at finite temperatures. At finite
temperatures, the principal peak in the p-dos shifts towards left (lower frequency
side). Also, the height of principal peak decreases with temperature, which indicates
that at finite temperatures mean frequency of vibration decrease, indicating weak
correlation among atoms at finite temperatures.
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Figure 4.3. Phonon dispersion relation along major symmetry directions for 3C-SiC
at ambient condition (full line), T=500 K (dashed line) and in T=1100 K (dotted line).
Figure 4.5 represents the calculated Gibbs free energy function at various
temperatures. It is observed that it decreases with temperature, as expected. Figure 4.6
shows the presently calculated isothermal and adiabatic bulk modulus at various
temperatures along with the corresponding results of Karch et al [14]. The trend of
variation of bulk modulus with temperature for presently calculated results and results
due to Karch et al [14] is nearly same. The deviation in the presently calculated results
and the results of Karch et al [14] may be attributed to the different treatment of ionic
motion at finite temperature and especially the thermodynamic Grüneisen parameter
as well as the use of different exchange-correlation functional. Figure 4.7 shows the
temperature dependent Debye temperature of 3C-SiC. We have used the classical
approach of quasi harmonic Debye model for calculating the thermal contribution of
lattice ions. As a result, we do not observe any quantum effect present at low
temperatures ( DT θ< ).
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Figure 4.4. Calculated quasi harmonic phonon density of states of SiC.
0 K (full line), 500 K (dashed line) and 1100 K (dotted line).
Figure 4.5. Temperature variations of Gibbs function of SiC.
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Figure 4.6. Presently calculated Isothermal (full line) and adiabatic (dashed line) bulk
modulus of SiC along with corresponding results of Karch et al [14] (filled and open
dots respectively).
Calculated and empirical results (using experimental specific heat) of temperature
dependent Debye temperature are reported by Vashistha et al [15]. They have
reported their results using well known low temperature expression of Debye
temperature in terms of specific heat, given by ( )34 / 5
12 DBv TkNC θπ= . They have
calculated specific heat using vibrational density of states. In our work, we have
directly estimated temperature dependence of Debye temperature in a quasi harmonic
way using classical approach. The results of Vashistha et al [15] are limited up to
1000 K (near to normal Debye temperature) beyond which, we believe that the Debye
temperature should decrease with temperature, due to decrease in phonon frequency
with temperature. Thus, our results provide an estimate of temperature variation of
Debye temperature at high temperatures (DT θ> ). Our presently computed values of
specific heats at constant volume and pressure are plotted in Figure 4.8 along with the
molecular dynamics results of Vashistha et al [15]. A good agreement of presently
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computed Cv is found with the molecular dynamics results. Our presently calculated
Cv is slightly higher compared to molecular dynamics results. One reason behind this
may be that we have calculated the temperature variation of specific heat using
temperature dependent Debye temperature, in order to include the effect of quasi
harmonic calculation on specific heat. Similar behavior is found for the Cp, which has
been calculated using temperature dependent thermodynamic Grüneisen parameter.
Nevertheless, overall a good agreement is achieved. Figure 4.9 shows the calculated
thermodynamic Grüneisen parameter at various temperatures. It is observed that
thermodynamic Grüneisen parameter increases parabolically with temperature.
Figure 4.7. Presently calculated Debye temperature of SiC as a function
of temperature.
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Figure 4.8. Calculated specific heat of SiC at constant volume (full line) and at
constant pressure (dashed line) along with the corresponding molecular dynamics
results of Vashistha et al [15] (filled and open circles respectively).
Figure 4.9. Calculated thermodynamic Grüneisen parameter of SiC at various
temperatures.
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(2) Germanium Carbide (GeC)
Compared to SiC, GeC is less studied. The phonon dispersion relation for SiC
is reported experimentally [21] but phonons in GeC are not reported, experimentally.
Work on structural properties of GeC at ambient and at high pressure is performed so
far by various researchers. However, studies on finite temperature thermophysical
properties are less. Sekkal et al [22] have performed molecular dynamics study using
Tersoff potential and calculated various thermodynamic properties namely Debye
temperature, thermal expansion coefficient, heat capacity and Grüneisen parameter.
Their results showed that physical properties of SiC and GeC systems are much
influenced by presence of C atoms, compared to Si and Ge atoms. In the present
work, we report the finite temperature thermophysical properties of zinc blende (ZB)
Gec using density functional theory [1] in conjunction with quasi harmonic Debye
model [2]. The value of the Poisson’s ratio is taken from Reference [5]. Figure 4.10
shows the calculated values of relative equilibrium lattice constants (/ oa a ) at various
temperatures. No experimental or any other theoretical data for the comparison are
available in literature. In the absence of any such data, presently calculated data shall
work as a useful set of data in future. Figure 4.10 also shows the corresponding
relative equilibrium lattice constants of 3C-SiC along with the results of Vashistha et
al [15]. It is observed that unlike 3C-SiC, the value of relative lattice constants
increases sharply with temperature, which indicates that ZB-GeC is a soft material
compared to 3C-SiC. Figure 4.11 shows the presently calculated thermal eos at
various temperatures. For comparison, no experimental or any theoretical data are
available in literature. However, since we have calculated this property using density
functional theory in conjunction with quasi harmonic Debye model, it will serve as a
reliable set of data for further research.
Figure 4.12 shows the calculated phonon frequencies in ZB-GeC at various
temperatures. It is observed that similar to ZB-SiC, in ZB-GeC also, phonon
frequencies become soft along all principal symmetry directions. Figure 4.13 shows
the computed quasi harmonic p-dos at elevated temperatures. The principal peak
shifts towards lower frequency side. Also, height of the principal peak is also affected
by temperature. Figure 4.14 shows the calculated Gibbs free energy function at
various temperatures. It is observed that it decreases with temperature as expected.
Figure 4.15 shows the presently calculated isothermal and adiabatic bulk modulus of
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ZB-GeC at various temperatures. The temperature coefficient of isothermal bulk
modulus is -0.0396 GPa/K, while the temperature coefficient of adiabatic bulk
modulus is -0.0651 GPa/K at high temperatures. Figure 4.16 shows the presently
calculated temperature dependent Debye temperature of ZB-GeC at various
temperatures. The temperature coefficient of Debye temperature is -0.0912 at high
temperatures. Again, as we are using the classical approach to calculate thermal
properties, we do not observe any quantum effect at low temperatures.
Figure 4.10. Lattice constant of ZB-GeC (full line) as a function of temperature
calculated using quasi harmonic Debye model. Also, shown are the results of
equilibrium lattice constant of 3C-SiC (dashed line) and molecular dynamics results
of Vashistha et al (dots) [15].
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Figure 4.11. Calculated thermal equation of state of ZB-GeC at various
temperatures.
Figure 4.12. Quasi harmonic phonon dispersion in ZB-GeC along high symmetry
directions at ambient condition (full line), at T=1000K temperature (dotted line) and
T=1500K temperature (dashed line).
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Figure 4.13. Quasi harmonic p-dos of ZB-GeC at various temperatures. 0K (full line),
1000K (dashed line) and 1500K (dotted line).
Figure 4.14. Temperature variations of Gibbs free energy function for ZB-GeC.
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Figure 4.15. Isothermal (BT) (full line) and adiabatic (Bs) (dashed line) bulk modulus
of ZB-GeC at various temperatures.
Figure 4.16. Temperature dependence of Debye temperature of ZB-GeC.
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Figure 4.17. Specific heat at constant volume (Cv) (full line) and at constant pressure
(Cp) (dashed line) for ZB-GeC.
Figure 4.18. Thermodynamic Grüneisen parameter of ZB-GeC as a function of
temperature.
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Figure 4.17 shows the presently calculated specific heats of GeC at various
temperatures. Figure 4.18 shows the calculated thermodynamic Grüneisen parameter
at various temperatures. Thermodynamic Grüneisen parameter does not increase
sharply with temperature. We observe in our study that ZB-GeC is soft material, with
relatively large thermal expansion (as compared to ZB-SiC). The full set of
thermodynamic properties of ZB-GeC is reported here for the first time. As, in the
literature, no experimental or other theoretical results for finite temperature
thermodynamic properties of ZB-GeC are available; we could not compare our
results. However, presently calculated results will serve as a useful set of data for
further research in this field.
(3) Tin Carbide (SnC)
Like SiC and GeC, SnC is also a technologically important material [22].
Thermodynamic properties of ZB-SnC are not studied till date either theoretically or
experimentally. Motivated by this fact, we in the present study represent the study of
thermodynamic properties of SnC in zinc blende structure. In previous chapter, we
have reported the ground state and high pressure properties of this material. The
Poisson’s ratio for ZB-SnC is taken from Reference [6]. Figure 4.19 shows the
calculated equilibrium lattice constant at various temperatures. Figure 4.20 shows the
presently calculated thermal equation of state (eos) of ZB-SnC at 0 K, 500 K and
1000 K temperature. It is observed that the eos at different temperatures are controlled
by cold pressure. Figure 4.21 shows the presently calculated quasi harmonic phonon
dispersion relation in ZB-SnC at 0 K and 500 K temperature. At higher temperature,
the phonon frequencies in SnC become soft along all symmetry directions. Figure
4.22 shows the presently calculated quasi harmonic p-dos at various temperatures. At
high temperatures, the peak in the phonon frequencies shifts towards lower frequency
side, showing weak correlation among atoms. Figure 4.23 shows the presently
calculated temperature dependent Gibbs free energy function. It decreases with
temperature. Figure 4.24 shows the calculated isothermal and adiabatic bulk modulus
as a function of temperature. A small hump is observed at low temperatures. The
temperature coefficient of isothermal and adiabatic bulk modulus is –0.041 GPa/K
and -0.0229 GPa/K, respectively. Figures 25, 26 and 27 respectively show the
presently calculated Debye temperature, specific heats and thermodynamic Grüneisen
parameter at various temperatures. The temperature coefficient of Debye temperature
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is -0.0245 at high temperatures. The comparative study of GeC and SnC indicates that
bulk modulus (which is related to elastic constants) of SnC decreases rapidly
compared to GeC and hence SiC. Further, the computed Debye temperature also
decreases sharply with temperature. It is observed that all the thermodynamic
properties calculated here show the characteristics features of temperature dependent
thermodynamic properties of a ceramic material. In the absence any experimental or
theoretical data for the thermodynamic properties of ZB-SnC, we could not compare
our data and hence, we could not put any concrete remark on the presently calculated
properties. It is observed in the present study that as we move from
SiC→GeC→SnC, elastic properties decrease with temperature, more rapidly. The
present results will serve as a useful set of data for further research in this field.
Figure 4.19. Calculated equilibrium lattice constants of ZB-SnC at
various temperatures.
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Figure 4.20. Thermal eos of ZB-SnC. At 0 K (full line), 500 K (dashed line) and
1000 K (dotted line).
Figure 4.21. Quasi harmonic pdc in ZB-SnC at various temperatures. At 0 K (full
line) and at 500 K (dashed line).
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Figure 4.22. Quasi harmonic p-dos of ZB-SnC at various temperatures. At 0 K (full
line) and at 500 K(dashed line).
Figure 4.23. Temperature dependent Gibbs free energy function for ZB-SnC.
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Figure 4.24. Isothermal (full line) and adiabatic (dashed line) bulk modulus of ZB-
SnC at various temperatures.
Figure 4.25. Temperature dependent Debye temperature of ZB-SnC.
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Figure 4.26. Specific heats of SnC at constant volume (full line) and at constant
pressure (dashed line).
Figure 4.27. Calculated thermodynamic Grüneisen parameter at various temperatures
for SnC.
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(4) Zirconium Carbide
Very few experimental and theoretical studies of thermodynamic properties of
cubic ZrC are available in literature [24,25]. Lawson et al [24] have studied the
thermodynamic properties of ZrC using neutron diffraction method. They have
reported thermal expansion and mean square displacement in B1-ZrC. Jun et al [25]
have studied few thermodynamic properties of ZrC using CASTEP code in
conjunction with quasi harmonic Debye model. In the present work, we report the
complete set of thermodynamic properties of B1-ZrC using plane wave
pseudopotential density functional theory [1] in conjunction with the quasi harmonic
Debye model [2]. The Poisson’s ratio of cubic ZrC is taken from Ref. [7]. Figure 4.28
shows the presently calculated equilibrium lattice constants at various temperatures
along with the experimental results of Lawson et al [24]. The presently calculated
value of equilibrium lattice constants is slightly overestimated as compared to the
experimental results. However, a good agreement is observed. Figure 4.29 shows the
presently calculated thermal eos at various temperatures. Intersection of p-V curve on
volume axis shows the volume thermal expansion and is the indication of proper
treatment of anharmonic effects. Also, one can infer from the nature of graphs for
different temperatures that eos are largely controlled by the cold pressure, which also
implies that thermal pressure is linearly increases with temperature. And its effect is
to harden the material and therefore results into the shift in p-V graph towards higher
volume side. Figure 4.30 shows the presently calculated quasi harmonic pdc of ZrC at
ambient condition and at 300 K temperature. It is observed that at finite temperatures,
the phonon frequencies along all symmetry directions become soft. Also, the rate of
change of phonon frequencies with temperature is not much high. This indicates that
the rate of change of elastic stiffness constants should not be high, as the phonon
frequencies along [100] and [110] planes are directly related to the elastic stiffness
constants. Figure 4.31 shows the presently calculated quasi harmonic p-dos at 0 K and
at 300 K temperature. Figure 4.32 shows the temperature dependent Gibbs free energy
function for ZrC. Figure 4.33 shows the calculated temperature dependent isothermal
and adiabatic bulk modulus. Figure 4.34 shows the calculated Debye temperature of
ZrC along with the experimental results [26]. As, we are using the classical approach
for inclusion of ionic motion at finite temperatures, we do not observe any quantum
mechanical effect present at low temperature. On the other hand, the experimental
values show deep in low temperature region and then increases. However, the
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experimental values are available up to limited temperature range, beyond which
Debye temperature should decrease. Figures 4.35 and 4.36 show respectively, the
specific heats and thermodynamic Grüneisen parameter at different temperatures.
Figure 4.36 also shows the experimental values [26] of thermodynamic Grüneisen
parameter of ZrC. At low temperatures, the difference between presently computed
values and the experimental values is observed. However, it is observed that at high
temperatures ( DT θ> ), presently calculated values and experimental results are nearly
same. This validates the present approach at high temperatures in case of ZrC. All the
properties calculated here, indicates that B1-ZrC is a mechanically hard material.
Figure 4.28. Calculated equilibrium lattice constant of ZrC along with the
experimental results [24].
Figure 4.29. Thermal eos of ZrC at various temperatures. At 0 K (full line), 500
K (dashed line) and at 1000 K (dotted line).
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Figure 4.30. Quasi harmonic pdc of ZrC at 0 K (full line) and at 300 K (dashed
line).
Figure 4.31. Quasi harmonic p-dos of ZrC at various temperatures. 0 K (full line) and
at 300 K (dashed line).
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Figure 4.32. Temperature dependent Gibbs function of ZrC.
Figure 4.33. Isothermal (full line) and adiabatic (dashed line) bulk modulus of ZrC at
various temperatures.
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Figure 4.34. Temperature dependent Debye temperature of ZrC along with
experimental results (dots) [26].
Figure 4.35. Specific heat of ZrC at constant volume (full line) and at constant
pressure (dashed line).
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Figure 4.36. Thermodynamic Grüneisen parameter of ZrC as a function of
temperature along with experimental results (dots) [26].
Fluorides
(1) Lithium Fluoride
Among all alkali halides and ionic crystals, LiF have found much attraction
due to its interesting physical properties. It is a material with low absorption, low
scattering factor for sample measurement through Diamond Anvil Cell (DAC). As a
result, it has found application as pressure transmitting medium as well as pressure
sensor. Structural stability of LiF up to about mega bar pressure also makes it an
important material [27]. Previously, experimental and theoretical work on LiF is
performed mostly at ambient conditions. Studies on thermophysical properties of LiF
are reported in limited range of temperature and pressure. Liu et al [27] have studied
thermophysical properties up to 37 GPa pressure and ~1000 K temperature. Most
recently, Smirnov [28] has studied various ground state properties of LiF using full
potential linear muffin tin orbital method as implemented in LMTART code with few
modifications. Further, he has studied pressure dependence of elastic constants and
structural stability under pressure. In his work, thermal contribution at finite
temperature was taken into account using modified Debye model. In the present work,
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we describe ground state and finite temperature/pressure thermophysical properties of
rock salt structured (B1) LiF using plane wave pseudopotential density functional
theory as implemented in Quantum ESPRESSO package [1] in conjunction with quasi
harmonic Debye model [2]. The value of Poisson’s ratio of LiF is taken from Ref. [8].
Figure 4.37 shows the presently calculated relative equilibrium lattice constant as a
function of temperature along with the experimental results [29]. A good agreement is
observed at low temperatures. Further, the trend of variation of lattice constants in
presently calculated values and experimental values is also same. Experimental values
are available only up to room temperature. The maximum deviation of presently
calculated values is of the order of 0.3% from the experimental results. Figure 4.38
shows the presently calculated thermal eos of LiF at various temperature along with
the room temperature experimental results [27]. A good agreement with the presently
calculated value and the corresponding experimental results is found. The high
temperature thermal eos also shows the proper inclusion of anharmonic effects in the
present calculation. Figure 4.39 shows the presently calculated quasi harmonic pdc of
LiF at 0 K and at 300 K temperature. It is observed that at higher temperatures, the
effect is to reduce magnitude of phonon frequencies along all symmetry directions.
Figure 4.40 shows the quasi harmonic p-dos at 0 K and at 300 K temperature. Again,
at high temperatures, the peak of p-dos shifts towards lower frequency side, showing
weak correlation among atoms at finite temperature. Figure 4.41 shows the presently
calculated Gibbs free energy function at various temperatures. Figure 4.42 shows the
calculated isothermal and adiabatic bulk modulus along with the experimental values
of isothermal bulk modulus [30]. The trend of variation of isothermal bulk modulus is
almost same. The presently calculated values of temperature coefficient of isothermal
bulk modulus is -0.033 GPa/K, while, the experimental value is -0.0218 GPa/K.
Figure 4.43 shows the presently calculated Debye temperature at various temperatures
along with the experimental data [30]. Again, trend of variation of Debye temperature
in the presently calculated values and the experimental one is found to be same. The
temperature coefficient of Debye temperature in the present work is -0.13, while the
experimental value is -0.15. Figure 4.44 shows the presently calculated specific heats
along with the experimental data of room temperature specific heat at constant
pressure [31]. A good agreement is found. The constant pressure specific heat
increases beyond the Dulong-Peltit limit at high temperature, showing the role of
anharmonicity at high temperatures. Figure 4.45 shows the presently calculated values
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of thermodynamic Grüneisen parameter at various temperatures along with the
experimental results [32]. Unlike experimental results, presently computed
thermodynamic Grüneisen parameter increases with temperature. On the other hand,
experimental values show first increase, then decease and then increasing values.
Such difference requires further study in this field. All the finite temperature
thermodynamic properties calculated here, shows good agreement with the
corresponding experimental data available in literature.
Figure 4.37. Calculated equilibrium lattice constants of LiF at various
temperatures.
Figure 4.38. Thermal eos of B1-LiF. At 300 K (full line), 500 K (dashed line) and at
1000 K (dotted line). Symbols are the experimental results at room temperature [27].
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Figure 4.39. Quasi harmonic pdc in B1-LiF at various temperatures. At 0 K (full line)
and at 300 K (dashed line).
Figure 4.40. Quasi harmonic p-dos at various temperatures. At 0 K (full line) and at
300 K(dashed line).
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Figure 4.41. Temperature dependent Gibbs free energy function of LiF.
Figure 4.42. Isothermal (full line) and adiabatic (dashed line) bulk modulus of B1-
LiF at various temperatures. Symbols are the experimental values of isothermal bulk
modulus [30].
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Figure 4.43. Temperature dependent Debye temperature of B1-LiF along with the
experimental results (dots with line) [30].
Figure 4.44. Specific heats of LiF at constant volume (full line) and at constant
pressure (dashed line) along with experimental constant pressure specific heat (dot)
[31].
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Figure 4.45. Calculated thermodynamic Grüneisen parameter of LiF at various
temperatures along with experimental results (dots) [32].
(2) Sodium Fluoride
Sodium fluoride is also a technologically important material having found
application in the field of high pressure physics [27]. It can be used as a pressure
transmitting medium in high pressure experiments. The study of thermophysical
properties of NaF at very low pressure is reported by Yagi et al [33] and Sato-
Sorensen [34]. Most recently Liu et al [27] have reported thermal expansion of NaF.
In the present work, we have reported the finite temperature thermophysical
properties of NaF. The Poisson’s ratio of NaF is taken from Ref. [9]. Figure 4.46
shows the relative lattice constants of NaF at various temperatures. Figure 4.47 shows
the presently calculated thermal eos of NaF at 300 K, 500 K and 1000 K along with
the room temperature experimental results [27]. A very nice agreement of the
presently computed room temperature thermal eos is found with the experimental
results. The calculated thermal eos of NaF shows that the cold pressure entirely
controls the high temperature thermal eos and is a right indication of inclusion of
anharmonic effects. Figure 4.48 shows the quasi harmonic pdc of NaF. It is observed
that the effect of the temperature is to reduce the phonon frequency along all principal
symmetry directions. Figure 4.49 shows the presently calculated quasi harmonic p-dos
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at various temperatures. The calculated p-dos at finite temperature show the effect of
weak correlation among atoms. Figure 4.50 shows the presently calculated Gibbs free
energy function at various temperatures. Figure 4.51 shows the calculated isothermal
and adiabatic bulk modulus at various temperatures. Figure 4.52 shows the presently
calculated temperature dependent Debye temperature. No experimental results are
found for comparison. Figures 4.53 and 4.54 shows the computed specific heats and
Grüneisen parameter at various temperatures along with experimental results [31],
respectively. In case of specific heats, data for only room temperature specific heat is
available. Experimental result is slightly higher. Interestingly, thermodynamic
Grüneisen parameter remains constant in the temperature range studied here. The
presently calculated value at room temperature is in close agreement with
experimental and other theoretical values. Present findings are useful set of data from
many points of view. Firstly, no such study of full set of thermodynamic properties of
NaF is reported. On the other hand, looking to the applications of NaF in the extreme
environments, presently computed results may be useful to study structure, elasticity
and vibrational response of NaF at finite temperatures and/or pressures.
Figure 4.46. Calculated equilibrium lattice constants of B1-NaF at various
temperatures.
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Figure 4.47. Thermal eos of B1-LiF. 0 K (full line), 500 K (dashed line) and at 1000
K (dotted line). Dots are the experimental results at 0 K [27].
Figure 4.48. Quasi harmonic pdc in B1-NaF at various temperatures. At 0 K (full
line) and at 300 K (dashed line).
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Figure 4.49. Quasi harmonic p-dos of NaF at various temperatures. At 0 K (full line)
and at 300 K(dashed line).
Figure 4.50. Temperature dependent Gibbs free energy function of NaF.
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Figure 4.51. Isothermal (full line) and adiabatic (dashed line) bulk modulus of B1-
NaF at various temperatures.
Figure 4.52. Temperature dependent Debye temperature of B1-NaF.
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Figure 4.53. Specific heats of NaF at constant volume (full line) and at constant
pressure (dashed line) along with experimental results [31].
Figure 4.54. Calculated thermodynamic Grüneisen parameter of NaF at various
temperatures along with experimental (filled circle) and theoretical
results (open circle) [31].
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Oxides
(1) Calcium Oxide (CaO)
Alkaline earth oxide forms a technologically important class of materials.
They have found large number of applications. CaO is a major constituent of lower
mantle and its thermo-elasticity is important for the understanding of processes
including brittle failure, flexure and propagation of elastic waves [35]. Very few
theoretical studies of finite temperature thermophysical properties of CaO are
reported. Most of these studies include the evaluation of few thermophysical
properties using one of the classical models [36, 37]. In the present work, we have
calculated thermodynamic properties of CaO using density functional theory [1] in
conjunction with the quasi harmonic Debye model [2]. The value of Poisson’s ratio of
CaO is taken from Ref. [10]. Figure 4.55 shows the presently calculated values of
relative equilibrium lattice constants as a function of temperature along with the
experimental results [38]. The authors of Ref. [38] have reported the relative lattice
constants with respect to room temperature. We have reported the relative lattice
constants with respect to ambient temperature. However, good agreement is observed
between the presently calculated values and experimental one. Figure 4.56 shows the
presently calculated thermal eos of CaO at various temperatures. Figure 4.57 shows
the quasi harmonic pdc of CaO. It is observed that at finite temperatures, the phonon
frequencies along all principal symmetry directions decreases. Figure 4.58 shows the
calculated quasi harmonic p-dos of CaO. In the calculated p-dos of CaO, the peak of
p-dos shifts towards lower frequency side. The height of p-dos is not found to be
affected much at finite temperatures. Figure 4.59 shows the presently calculated
Gibbs free energy function at various temperatures. It decreases with temperature as
expected. Figure 4.60 shows the calculated temperature dependent isothermal and
adiabatic bulk modulus along with the experimental results [38] of adiabatic bulk
modulus. The trend of variation of bulk is almost same. Both of them decrease with
temperature. The temperature coefficient of presently computed adiabatic bulk
modulus is -0.0163 GPa/K and for experimental results it is -0.02 GPa/K. Figure 4.61
shows the calculated temperature dependent Debye temperature. The Debye
temperature decrease with temperature and as we are using the classical approach, we
do not observe any quantum mechanical effect at low temperature. Figure 4.62 shows
the presently calculated specific heats at different temperatures. The specific heat at
constant pressure increases beyond the Dulong-Peltit limit, which shows the dominant
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role of anharmonic effect at high temperatures. Figure 4.63 shows the temperature
dependent thermodynamic Grüneisen parameter.
No experimental data for the sake of comparison is found for the finite
temperature thermophysical properties except equilibrium lattice constants and bulk
modulus. Quasi harmonic pdc and p-dos of CaO are calculated for the first time. The
properties calculated here form a complete set of thermodynamic properties of rock
salt structured CaO, which will be helpful to understand the dynamics behind the
finite temperature thermophysical properties of B1-CaO.
Figure 4.55. Calculated equilibrium lattice constants of CaO at various
temperatures along with the experimental results [38].
Figure 4.56. Thermal eos of B1-CaO. At 0 K (full line), 500 K (dashed line) and 1000
K (dotted line).
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Figure 4.57. Quasi harmonic pdc in B1-CaO at various temperatures. At 0 K (full
line) and at 300 K (dashed line).
Figure 4.58. Quasi harmonic p-dos at various temperatures. At 0 K (full line) and at
300 K(dashed line).
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Figure 4.59. Temperature dependent Gibbs free energy function of CaO.
Figure 4.60. Isothermal (dashed line) and adiabatic (full line) bulk modulus of B1
CaO at various temperatures along with experimental results [38].
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Figure 4.61. Temperature dependent Debye temperature of B1-CaO.
Figure 4.62. Specific heats of CaO at constant volume (full line) and at constant
pressure (dashed line).
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Figure 4.63. Calculated thermodynamic Grüneisen parameter of CaO at various
temperatures.
(2) Strontium Oxide (SrO)
Like Calcium oxide, Strontium oxide is also a alkaline earth based oxide,
having found many applications. Till date only the study of finite temperature specific
heat of SrO is studied experimentally [39]. Some theoretical studies are also reported
[40-42]. In the present work, we have adopted the Poisson’s ratio from the Ref. [11].
Figure 4.64 shows the calculated relative equilibrium lattice constants at various
temperatures. Figure 4.65 shows the thermal eos of SrO at various temperatures.
Figure 4.66 shows the quasi harmonic pdc of SrO at ambient temperature and at 500
K. Like, all other materials studied here, in SrO also, the phonon frequencies
decreases at high temperatures. This feature indicates that SrO at finite temperature
becomes mechanically soft. Figure 4.67 shows the calculated quasi harmonic p-dos of
SrO. The peak of p-dos shifts towards lower frequency side. The height of p-dos is
not found to be affected much at finite temperatures. Figure 4.68 shows the presently
calculated Gibbs free energy function at various temperatures. It decreases with
temperature. Figure 4.69 shows the calculated temperature dependent isothermal and
adiabatic bulk modulus of SrO. Figure 4.70 shows the calculated temperature
dependent Debye temperature. The Debye temperature decrease with temperature and
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as we are using the classical approach, we do not observe any quantum mechanical
effect at low temperature. The calculated Debye temperature decrease with
temperature, which is expected as the phonon frequencies also decreases and the p-
dos at high temperature moves towards lower frequency side. Figure 4.71 shows the
presently calculated specific heats at different temperatures along with the
experimental results [39]. A good agreement is observed. The specific heat at constant
pressure increases beyond the Dulong-Peltit limit, which shows the dominant role of
anharmonic effect at high temperatures. Also, it overestimates the experimental
results at high temperatures. Figure 4.63 shows the temperature dependent
thermodynamic Grüneisen parameter.
Figure 4.64. Calculated equilibrium lattice constants of SrO at various
temperatures.
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Figure 4.65. Thermal eos of B1-SrO. At 0 K (full line), 500 K (dashed line) and 1000
K (dotted line).
Figure 4.66. Quasi harmonic pdc in B1-SrO at various temperatures. At 0 K (full
line) and at 500 K (dashed line).
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Figure 4.67. Quasi harmonic p-dos of SrO at various temperatures. At 0 K (full line)
and at 500 K(dashed line).
Figure 4.68. Temperature dependent Gibbs free energy function of SrO.
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Figure 4.69. Isothermal (full line) and adiabatic (dashed line) bulk modulus of B1-
SrO at various temperatures.
Figure 4.70. Temperature dependent Debye temperature of B1-SrO.
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Figure 4.71. Specific heats of SrO at constant volume (full line) and at constant
pressure (dashed line) along with the experimental results [39].
Figure 4.72. Calculated thermodynamic Grüneisen parameter of SrO at various
temperatures.
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(3) Barium Oxide (BaO)
JANAF table [42] have noted that the data of thermodynamic properties of
alkaline earth metal oxide like BaO are suspect since the results of the calorimetric
studies, on which their evaluation is based, are ambiguous [39]. To the best of our
knowledge, no theoretical study of thermodynamic properties of BaO is performed so
far. So, we in the present work intend to report the thermodynamic properties of B1-
BaO. The value of Poisson’s ratio is taken from Ref. [12]. Figure 4.73 shows the
calculated value of equilibrium relative lattice constants at various temperatures. No
experimental data of thermal expansion in BaO is available. Figure 4.74 shows the
calculated thermal eos of BaO at various temperatures. p-V graph clearly suggest that
anharmonic effects are properly included in the present work. Figure 4.75 shows the
Gibbs free energy function as a function of temperature. It decreases with
temperature. Figure 4.76 shows the isothermal and adiabatic bulk modulus of BaO at
various temperatures. It is observed that bulk modulus decrease almost linearly with
temperature. In Figure 4.77, we have shown the temperature dependent Debye
temperature. It decreases with temperature. As we are using the classical approach to
include the ionic motion at finite temperatures, we do not observe any deep in the
temperature dependent Debye temperature. Figure 4.78 shows the temperature
dependent constant volume and constant pressure heat capacities along with the
experimental values of constant pressure specific heat [39]. It is observed that the
constant pressure specific heat in the present study is slightly overestimated compared
to the experimental data. Figure 4.79 shows the presently computed thermodynamic
Grüneisen parameter as a function of temperature. Except specific heat at constant
pressure, no experimental data are available in literature for comparison. The reported
thermal expansion, thermal eos, variation of Gibbs function, bulk modulli, Debye
temperature show proper inclusion of thermal properties in the present calculation.
Confirmation to the present work is observed when comparison is made of presently
computed specific heat with the experimental results. Thus, it is to be observed that
presently computed values form a reliable set of data finite temperature
thermophysical properties of BaO, which shall work as an important guideline for
further research in this field.
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Figure 4.73. Calculated equilibrium lattice constants of BaO at various
temperatures.
Figure 4.74. Thermal eos of B1-BaO. At 0 K (full line), 500 K (dashed line) and
1000 K (dotted line).
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Figure 4.75. Temperature dependent Gibbs free energy function of BaO.
Figure 4.76. Isothermal (full line) and adiabatic (dashed line) bulk modulus of B1-
BaO at various temperatures.
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Figure 4.77. Temperature dependent Debye temperature of B1-BaO.
Figure 4.78. Specific heats of BaO at constant volume (full line) and at constant
pressure (dashed line) with the experimental results of constants volume specific
heat [39].
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Figure 4.79. Calculated thermodynamic Grüneisen parameter of BaO at various
temperatures.
(4) Cadmium Oxide (CdO)
Cadmium oxide is a technologically important material, having found large
number of applications in the field of production of solar cells, liquid crystal displays,
electrochromic devices etc [44]. The value of Poisson’s ratio is taken from Ref. [13].
Figure 4.80 shows the calculated equilibrium lattice constants at various temperatures.
Figure 4.81 shows the calculated thermal eos of CdO at various temperatures. Again,
p-V graph clearly suggest that anharmonic effects are properly included in the present
work. Figure 4.82 shows the Gibbs free energy function as a function of temperature.
It decreases with temperature. Figure 4.83 shows the isothermal and adiabatic bulk
modulus of CdO at various temperatures. In figure 4.84, we have shown the
temperature dependent Debye temperature. It decreases with temperature. As we are
using the classical approach to include the ionic motion at finite temperatures, we do
not observe any deep in the temperature dependent Debye temperature. Figure 4.85
represents the pressure dependent Debye temperature of CdO at 0 K temperatures
along with the corresponding theoretical results of Li et al [45]. It is observed that
presently computed Debye temperature is overestimated as compared to results of Li
et al [44]. The possible reason behind such difference may be attributed to different
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theoretical approaches used. The presently computed Debye temperatures at various
pressures is fitted to 4th order polynomial and is represented by following equation,
458.09 8.4186 0.1118- 0.0016 10- )( 234-5 +++= PPPPPDθ and the results of Li et al [45]
are given by,
413.95 4.4115 0.1114- 0.0017 10- )( 234-5 +++= PPPPPDθ .
The difference between the zero pressures Debye temperature may also be attributed
to type of exchange-correlation functional used. In our work, we have used the local
spin density approximation (LSDA), while, Li et al [45] have used the generalized
gradient approximation (GGA). Figure 4.86 shows the temperature dependent
constant volume and constant pressure heat capacities. Figure 4.87 shows the
presently computed thermodynamic Grüneisen parameter as a function of
temperature. No experimental data are available in literature for comparison.
Presently calculated all thermodynamic properties show all features of proper
inclusion of thermal properties in the present calculation and will serve as a reliable
set of data of thermodynamic properties of CdO.
.
Figure 4.80. Calculated equilibrium lattice constants of CdO at various
temperatures.
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Figure 4.81. Thermal eos of B1-CdO. At 0 K (full line), 500 K (dashed line) and
1000 K (dotted line).
Figure 4.82. Temperature dependent Gibbs free energy function of CdO.
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Figure 4.83. Isothermal (full line) and adiabatic (dashed line) bulk modulus of B1-
CdO at various temperatures.
Figure 4.84. Temperature dependent Debye temperature of B1-CdO.
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Figure 4.85. Pressure dependent Debye temperature of CdO at 0 K.
Figure 4.86. Specific heats of CdO at constant volume (full line) and at constant
pressure (dashed line).
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Figure 4.87. Calculated thermodynamic Grüneisen parameter of CdO at various
temperatures.
4.4 Conclusions
In conclusion, in the present chapter 4, we have reported finite temperature
thermophysical properties of technologically important materials using plane wave
pseudopotential density functional theory as implemented in Quantum ESPRESSO
package [1] in conjunction with the quasi harmonic Debye model [2]. Following
conclusions emerge out of the work presented in this chapter.
1) Calculated thermophysical properties of all materials agree well with the
available experimental and other theoretical findings.
2) Calculated equilibrium relative lattice constants as a function of temperature
for 3C-SiC, B1-ZrC and B1-LiF agree well with the corresponding
experimental and theoretical findings. In case of SiC, computed equilibrium
lattice constant at various temperatures show a maximum of 3% deviation
compared to molecular dynamics results. On the other hand, computed,
relative equilibrium lattice constant of ZrC show a maximum of 0.3%
deviation compared to experimental results. In a similar way, in case of LiF
also, the presently calculated relative lattice constants vary by 0.3 % only from
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experimental results. Calculation of equilibrium lattice constant is a primary
test of inclusion of proper ionic motion at finite temperature, which in our
study is properly reproduced. Thus, the good agreement validates the present
calculation of thermodynamic properties. For all other materials, no
experimental or theoretical data for thermal expansion is available. Thus, we
could not compare our results. However, as they are calculated using two
strong theoretical approaches, presently calculated values will serve as a
reliable set of data for further research.
3) Further, computed thermal eos is also found in good agreement with the
available experimental results. The computation of thermal eos in all cases
reveal that the cold pressure entirely controls the finite temperature thermal
eos. The graph of eos also indicate the proper inclusion of anharmonic effects
in the present calculations.
4) We have calculated the Gibbs free energy function at various temperatures. it
decreases with temperature. As it is observed in all cases, that equilibrium
lattice constants increases with temperature (and no negative thermal
expansion is observed in any material), for the materials to reach equilibrium
at finite temperatures, corresponding free energies should decrease.
5) Calculated values of isothermal and adiabatic bulk modulus agrees well in
case of 3C-SiC and B1-LiF. The trend of variation of bulk modulus with
temperature is same as that of experimental results. Further, the temperature
coefficient of bulk modulus is also nearly same. For other materials, no
experimental data are available.
6) Calculated Debye temperature at various temperatures, agree well in case of
B1-LiF. The temperature coefficient of Debye temperature is also nearly same.
For other materials, no experimental data are available.
7) Calculated values of specific heats (at constant pressure and at constant
volume) agree well with the corresponding available experimental results, in
case of 3C-SiC, B1-LiF, B1-SrO and B1-BaO. For other materials, no
experimental data are available for comparison.
8) The calculated values of thermodynamic Grüneisen parameter at various
temperatures (expect for NaF) indicate that it increase parabolically with
temperature. Interestingly, in case of NaF, thermodynamic Grüneisen
parameter remains constant with respect to temperature.
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9) It is observed that although Si, Ge and Sn belong to same family, the
thermodynamic properties of their carbides SiC, GeC and SnC are much
different. In particular, elastic properties of SiC is affected less by temperature
as compared to GeC and SnC. It is also observed that elastic properties of ZrC
are also affected less with temperatures. Thus, among all four carbides, SiC
and ZrC are found to retain their elastic properties at high temperatures.
10) In fluorides, LiF is found to retain is elasticity up to high temperatures. In case
of LiF, the temperature coefficient of isothermal bulk modulus is -0.073
GPa/K and in case of NaF, it is -0.0306 GPa/K. thus, it is found that bulk
modulus (which is related with elastic constants C11 and C12) decreases at
high rate with temperature in case of NaF.
11) In case of CaO, the temperature coefficient of isothermal bulk modulus is -
0.0306 GPa/K, for SrO it is -0.0203 GPa/K, for BaO it is -0.0168 GPa/K and
for CdO, it is -0.057 GPa/K. thus, among all oxides, studied here, it is
observed that elastic constants of BaO should decrease at higher rate
compared to other three oxides, which indicate that BaO is much sensitive to
temperature as compared to CaO, SrO and CdO.
12) The good agreement with the presently computed values of various
thermodynamic properties of carbides, oxides and fluorides thus confirms the
present approach (i.e. DFT + quasi harmonic Debye model) in determining
various thermodynamic properties up to their normal melting.
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