The document summarizes key information about the CdGa2S4 semiconductor. It belongs to the ordered vacancy compound family, which contains direct bandgap materials less than 4 eV that can be used in optoelectronic devices. CdGa2S4 has a defect chalcopyrite structure at ambient conditions and undergoes a phase transition to a disordered rocksalt structure above 18.8 GPa. First-principles density functional theory calculations were performed to investigate the structural stability and electronic properties of both phases under varying pressures. The results show that the defect chalcopyrite phase is more stable at lower pressures and becomes metallic above the transition pressure where the structures change.
1. 1. Introduction
The cadmium thiogallate ๐ถ๐๐บ๐2๐4 is associated with the ordered vacancy compounds (OVCs)
family, which encloses the ternary semiconducting compounds ๐ด๐ผ๐ผ
๐ต2
๐ผ๐ผ๐ผ
๐4
๐๐ผ
(๐ด๐ผ๐ผ
=
๐๐, ๐ถ๐, ๐ป๐; ๐ต๐ผ๐ผ๐ผ
= ๐ด๐, ๐บ๐, ๐ผ๐; ๐ถ๐๐ผ
= ๐, ๐, ๐๐, ๐๐). This family contains a wide range of direct
bandgap materials and the forbidden energy gap is less or equal to 4 ๐๐. These compounds can
be used in photoluminescence and optoelectronic devices [1-10], i.e., laser diodes, optical fiber,
photodiodes, and solar cells. The photographic characteristic of these semiconductors is
described by electrophotographic layers and provides superior quality outputs [11]. The
๐ถ๐๐บ๐2๐4 composite can be used in a wide range of light deflectors and temperature sensors
[12-14]. Therefore, a greater focus on the importance of this crystal in optics draws attention
to the handling of its bandgap by exerting pressure. These compounds act as optically
birefringent [2] with the occupation of strong anisotropy and the absence of cubic symmetry
and are best suited for phase matching applications [15]. The electronic, optical, structural,
mechanical, and elastic properties have been investigated by the first principle DFT study of
๐ถ๐๐บ๐2๐4 crystal. The defect chalcopyrite (DC) semiconductorโs band structure is described by
Jiang and Lambrecht [16] to coordinate with normal chalcopyrite semiconductors. The
๐ถ๐๐บ๐2๐4 semiconductorโs electronic and structural properties variation have been calculated
at different pressure and temperature [17]. The vibrational properties of ๐ถ๐๐บ๐2๐4
semiconductors have been evaluated by Hecht et al. [18-19]. For ๐ถ๐๐บ๐2๐4 and ๐ถ๐๐บ๐2๐๐4
semiconductors, the PL, and absorption spectra have been observed in the range of 2.3 โ
3.8 ๐๐ and 370 โ 600 ๐๐, respectively by V.F. Zhitar [20] and N.V. Joshi [21]. The ๐ถ๐๐บ๐2๐4
thin filmโs dielectric properties and electrical conductivity have been measured by confining
the process of traditional thermal evaporation [22]. The polar phononโs dispersion is directional
for DC semiconductors and is investigated by Razzetti et al. [23-24]. The iodine is used as a
transport agent in this process. Hamide Vaezi et al. [57] have been described the optical spectra
of ๐ถ๐๐บ๐2๐4 semiconductorโs crystalline form.
The phase transition in the DC semiconductors under pressure has been tried. At high pressure,
the Raman spectroscopy, X-ray diffraction, and optical absorption process have been
accomplished on ๐ถ๐๐บ๐2๐๐4 [25], ๐๐๐บ๐2๐๐4[26] and ๐ถ๐๐บ๐2๐4 [19] semiconductors. The
Raman modes and phase transitions have been examined by Raman scattering spectroscopy
under different pressures [27-30]. Noticeably, the DC materials go through a structural phase
transition from tetragonal structure to rocksalt structure at room temperature and high pressure
[31-32]. Incidentally, the thiospinels have been demonstrated the partially controlled rocksalt
2. structure [33] under pressure. However, the ๐ถ๐๐บ๐2๐4 the structure is least studied than other
defect chalcopyrite semiconductors according to the literature review. Thus, it was considered
interesting to investigate various properties of this semiconductor under pressure. In this paper,
we have utilized generalized gradient approximation (GGA) inside the system of first-
principles density functional theory (FP-DFT) to examine both defect chalcopyrite and rocksalt
structureโs stability, electronic, elastic, and optical properties at different pressures.
2. Computational Details
The density functional theory (DFT) system [34] has been applied to crystal structure with first
principal evaluations by using Vienna Ab initio Simulation Package (VASP) [35]. This process
follows the full-potential linearized augmented plane waves (FP-LAPW) method [3]. The
generalized gradient approximation (GGA) has been used with Perdew-Burke-Ernzerhof
(PBE) parameterization [36-37] to outline electrons exchange-correlation interaction. In
this paper, the wave functions consist of valence states of ๐ถ๐(3๐, 4๐ ), ๐บ๐(3๐, 4๐ , 4๐) and
๐(3๐ , 3๐) by using pseudo-atomic OMX basis sets [38-39]. The atomโs semi-core states are
used by these basis sets for precise calculations. The Monkhorst-Pack grids [40], i.e., 6 ร 6 ร 6
and 8 ร 8 ร 8 have been used for defect chalcopyrite (DC) and disordered rocksalt (DR) phase,
respectively by Brillouin zone integration technique. The mesh cut-off for the DC and DR
phase has been set to 480 ๐๐ and 500 ๐๐, respectively. The observed structures have been
fully relaxed to their optimized configuration by the forces and stress tensor calculations in this
paper. The limited-memory Broyden-Fletcher-Goldfarb-Shanno (LBFGS) optimization
technique [41] has been applied for achieving an optimized molecular geometry. The value of
force and stress tolerance are 0.0001 ๐๐ โซ
โ and 0.009 ๐บ๐๐, respectively in the optimized
configurations. For self-consistent calculations, the total energy differences are less than
0.272 ร 10โ6
๐๐.
3. Results and Discussion
3.1 Structural Results and Properties
๐ถ๐๐บ๐2๐4 includes body-centered cubic (BCC) geometry, tetragonal structure and space group
๐ผ4 (#82). This crystal is a defect chalcopyrite (DC) semiconductor and contains seven atoms
per unit cell. The DC-phase of ๐ถ๐๐บ๐2๐4 structureโs lattice parameters are represented in Fig.
1(a) and given as [57] ๐ = 5.642 โซ and ๐ = 10.44 โซ, where ๐ = ๐ โ ๐
The Wyckoff positions of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structure is
๐ถ๐ (0,0,0), ๐บ๐1 (0,0,0.5), ๐บ๐2 (0,0.5,0.25) and ๐ (0.273,0.265,0.138). The specified atoms
occupy these positions in the traditional unit cell. The disordered rocksalt (DR) phase of
3. ๐ถ๐๐บ๐2๐4 structure [43] contains space group ๐น๐ โ 3๐ (#225), as illustrated in Fig. 1(b). At
diffusive pressure, the volume vs total energy plots has been evaluated for both (DC and DR)
phases and are represented in Fig. 2. In Table 1, the optimized lattice parameters are represented
with comparable experimental and theoretical values. For ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ ๐ถ๐๐บ๐2๐4
structures, the bulk modulus, and the energy band-gap have been calculated and are also shown
in Table 1.
Fig. 2 represents that the DC-phase is more poised than the DR-phase of ๐ถ๐๐บ๐2๐4 structure at
absolute zero temperature and zero pressure. The Gibbs free energy has been calculated for
determining the phase transition of ๐ถ๐๐บ๐2๐4 structure from DC to DR phase. The Gibbs free
energy is expressed as
๐บ = ๐ + ๐๐ โ ๐๐ (1)
In equation (1), the systemโs internal energy, work done by structure volume, and vibrational
energy are denoted as ๐, ๐๐, and ๐๐, respectively. This equation can be rewritten in terms of
enthalpy, given as
๐บ = ๐ป โ ๐๐ (2)
where enthalpy ๐ป = ๐ + ๐๐.
In this paper, the enthalpies have been calculated for optimized ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ
๐ถ๐๐บ๐2๐4 structures at 5, 10, 15, 18.8, 20, 25, and 30 ๐บ๐๐ pressures. The ๐ถ๐๐บ๐2๐4 structureโs
phase transition from DC to DR phase is achieved at 18.8 ๐บ๐๐, as represented in Fig. 3. Two
enthalpy curves intersection point describes this phase transition. Moreover, the transition
pressureโs experimental value [57] is 17 ๐บ๐๐ which is less than the calculated transition
pressure. The total difference between theoretical and experimental transition pressure is
1.8 ๐บ๐๐ due to temperature variation and taken powderโs purity. The enthalpy change turns
negative at 18.8 ๐บ๐๐ for DR structure. Consequently, the stability of the DR structure has
increased after transition pressure 18.8 ๐บ๐๐ but the DC structure is stable until phase transition
occurred.
The normalized cell volume (๐ ๐0
โ ) has been calculated through phase transition analysis from
DC to DR structure. The traditional unit cellโs volume at a certain pressure and the DC phaseโs
equivalent volume at zero pressure is denoted as ๐ and ๐0, respectively. Fig. 4 shows the
pressure vs normalized cell volume plot. As it turns out to be volume collapse (ฮ๐ ๐0
โ ) at the
transition pressure, the particular ratio is 0.586 or 58.6 %.
Fig. 5(a) represents the band structure of ๐ถ๐๐บ๐2๐4 semiconductorโs DC-phase. The DC-
phaseโs band structure is evaluated at 0 ๐บ๐๐ and the marked energy range is โ14 ๐๐ to 6 ๐๐.
4. It is found that the ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 semiconductorโs energy bandgap is 2.09 ๐๐ and is
represented in Table 1. The Fermi level is fixed to zero. The experimental value [58] of the
bandgap is quite high than the theoretical value due to temperature variation. Fig. 5(b)
illustrates the band structure of ๐ถ๐๐บ๐2๐4 structureโs DC-phase at 18.8 ๐บ๐๐. It is found that
the overlapping has occurred in valence and conduction bands due to its metallic nature.
The distinct electronic state's energy distribution can be reflected by the total density of states
(TDOS) and partial density of states (PDOS). It is well known that DOS calculations are used
for observing the structural electronic behavior of ๐ถ๐๐บ๐2๐4 semiconductorโs both phases. The
total and partial DOS of both phases of ๐ถ๐๐บ๐2๐4 the structure is illustrated in Fig. 6(a) and
6(b) at 0 ๐บ๐๐ and 18.8 ๐บ๐๐, respectively.
As reported by partial DOS in Fig. 6(a), the atomic states ๐ โ 3๐ with the combination of ๐บ๐ โ
3๐, 4๐ , and 4๐ states result from the electronic states over โ13 ๐๐ to โ11 ๐๐. The dominant
peak in energy interval of โ7.5 ๐๐ to โ7 ๐๐ arises due to ๐ถ๐ โ 4๐ atomic states. The
combination of ๐บ๐ โ 4๐ , 4๐ and ๐ โ 3๐ atomic states produce this peak. The valence and
conduction electronic states are the most significant parts of DOS. Below the fermi level, the
valence states can be splitted into three different regions. The valence bandโs lower-level states
are primarily shaped by ๐บ๐ โ 4๐ states with the ๐ โ 3๐ atomic states. The union of ๐ โ
3๐, ๐บ๐ โ 4๐, and ๐ถ๐ โ 5๐ atomic states form the intermediate region. Moreover, the upper
level of states is placed just below the fermi level and is also called the valence bandโs top
region. The chief contribution of ๐ โ 3๐ atomic states with the least combination of ๐ถ๐ โ 4๐
and ๐บ๐ โ 4๐ form upper states of the valence band. In the same way, the conduction band can
also divide into three regions. The hybridization of atomic states ๐บ๐ โ 4๐ with ๐ โ 3๐ and 3๐
states form the conduction bandโs bottom region. In the intermediate region, the peak arises
after 3 ๐๐ to 5 ๐๐ and comes from atomic states ๐บ๐ โ 4๐ with a strong contribution of ๐ โ 3๐
and ๐ถ๐ โ 5๐ states. The combination of ๐บ๐ โ 4๐ and ๐ โ 3๐ atomic states form the upper
level of conduction states.
Similarly, the atomic states ๐ โ 3๐ with the combination of ๐บ๐ โ 3๐, 4๐ , 4๐ and ๐ถ๐ โ 5๐ states
result from the electronic states over โ13 ๐๐ to โ11 ๐๐, as reported by PDOS in Fig. 6(b). the
leading peak in energy interval of โ8 ๐๐ to โ7 ๐๐ arises due to ๐ถ๐ โ 4๐ atomic states. The
combination of ๐บ๐ โ 4๐ , 4๐ and ๐ โ 3๐ atomic states produce this peak. The valence and
conduction electronic states are the most important parts of DOS and can be divided into three
regions: lower, intermediate, and upper level. This will follow the same process as described
in the above (DC-phase) paragraph. It is important to acknowledge the fact that the results
5. presented in this paper are comparable with literature results [44-45]. It is observed that the
electronic states are more responsive to high pressure by the both (DC and DR) phases DOS
comparisons due to greater angular momentum.
Figure 1: The unit cell of (a) ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and (b) ๐ท๐ โ ๐ถ๐๐บ๐2๐4. In this figure, dark green
balls represent Cd atoms, light green balls represent Ga atoms and yellow balls represent S
atoms
6. Figure 2: Total energy vs volume curves of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ ๐ถ๐๐บ๐2๐4.
Figure 3: Variation of enthalpies as a function of pressure in ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ
๐ถ๐๐บ๐2๐4.
Table 1
Lattice parameters ๐(โซ) and ๐(โซ), bulk modulus (๐ต) (in GPa) and energy gap (๐ธ๐) (in eV) of
๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ ๐ถ๐๐บ๐2๐4 phase semiconductor.
Parameters Proposed work Experimental Other theoretical
results
๐ซ๐ช โ ๐ช๐ ๐ฎ๐๐๐บ๐
a 5.642 5.56 [58], 5.536 [59] 5.553 [57]
c 10.44 10.18 [58], 10.160
[60]
10.272 [57]
7. B 47.2a
64 [57-58] 40.8 [57]
๐ธ๐ 2.093 3.23 [58] 1.96 [57]
๐ซ๐น โ ๐ช๐ ๐ฎ๐๐๐บ๐
a 5.1892 5.4355 [59]
B 159.45
๐ธ๐ 0 0 0
a
2nd
order EOS
Figure 4: Variation of the normalized volume (๐ ๐0
โ ) of ๐ถ๐๐บ๐2๐4 as a function of pressure.
3.2 Elastic Properties
The materialโs mechanical strength, hardness, brittleness, ductility, stiffness, and durability
have been described by elastic parameters. The crystallization of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4
structure occurs in ๐ผ4 the space group and placed into tetragonal shaped material group TII. In
VASP, seven elastic constants ๐ถ11, ๐ถ12, ๐ถ13, ๐ถ33, ๐ถ44, ๐ถ66 and ๐ถ16 can be calculated by using
MT elastic simulation for this group. Due to the occupation of shear elastic constant ๐ถ16 in a
slanted direction, the elastic moduli canโt be derived by these elastic constants. TI crystal can
calculate elastic moduli from six independent elastic constants. This elastic co-relation is not
possible in the TII laue group of tetragonal structure.
8. The ๐ถ16 must be zero for converting TII crystalโs seven elastic constants to TI crystalโs six
elastic constants. The rotation around the z-axis with the angle ๐๐ ,๐พ can transform these elastic
constants are is expressed as
๐๐ ,๐พ =
1
4
๐ก๐๐โ1
(
4๐ถ16
๐ถ11โ๐ถ12โ2๐ถ66
) (3)
where ๐๐ ranges from 0 to ๐ 2
โ and by employing the relation ๐๐พ = ๐๐ + ๐ 4
โ , the value of
๐๐พ can be detected. From equation (3), the value of ๐๐ is โ0.0010
at 0 ๐บ๐๐ for DC-phase of
๐ถ๐๐บ๐2๐4 structure. Using the relationship described in Ref. [46], the TII crystalโs six
independent elastic constants have been evaluated at 0 ๐บ๐๐. In Table 2, the six new elastic
constants are recorded at 0, 5, 10, 15, and 18.8 ๐บ๐๐. The calculation of elastic constants is very
useful at applied pressure for finding the mechanical properties of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structure.
The Born-Huang stability criteria [47] describes the mechanical stability at zero pressure for
tetragonal structure. According to this criterion, the conditions for elastic constants are termed
as
1) The ๐ถ11, ๐ถ44 and ๐ถ66 must be greater than zero.
2) The difference in ๐ถ11 and ๐ถ12 should be greater than zero.
3) Half of the sum of the product of ๐ถ11, ๐ถ33 and ๐ถ12, ๐ถ33 should be less than a square of
๐ถ13.
There are no experimental and theoretical elastic parameter values exist for comparing with
computed results, as per our knowledge. The Born stability conditions have been altered due
to applied pressure at a tetragonal structure. The stability conditions [47-48] for elastic
constants are termed as
1) The difference in ๐ถ11 and applied pressure (๐) must be greater than zero.
2) The difference in ๐ถ44 and ๐ should be greater than zero.
3) The half of the difference in ๐ถ11 and ๐ถ44 should be less than pressure (P).
4) The half of the product of the difference in ๐ถ33 and ๐ and summation of ๐ถ11 and ๐ถ12
must be less than the whole square of ๐ถ13 and ๐ summation.
9. Figure 5: Electronic band structure of (a) DC-phase (at 0 ๐บ๐๐) and (b) DR-phase (at
18.8 ๐บ๐๐) of ๐ถ๐๐บ๐2๐4.
10. The elastic constants ๐ถ11, ๐ถ12, ๐ถ13, ๐ถ33 and ๐ถ44 rise linearly with increasing pressure up to
18.8 ๐บ๐๐ except ๐ถ66 for ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structure. The ๐ถ66 intially rise till 5 GPa, therefore
fall up to 10 ๐บ๐๐ and then rise again with increasing pressure. The value of ๐ถ66 decreases with
pressure in the range of 5 โ 10 ๐บ๐๐ due to the change in temperature and decrease in materialโs
stiffness at subsequent pressure range. Table 2 lists the computed values of DC structureโs
elastic constants towards 20 ๐บ๐๐ pressure. It is noted that the elastic constants values fall with
the increasing pressure ranges between 18.8 โ 20 ๐บ๐๐. By the way, the Bornโs stability
criteria [47-48] is retracted by ๐ถ44 value because of the phase transition appears at 18.8 ๐บ๐๐.
Hence, the DC phase of ๐ถ๐๐บ๐2๐4 semiconductor is stable until 18.8 ๐บ๐๐ pressure and
becomes less stable after transition pressure 18.8 ๐บ๐๐, as illustrated in prior literature [49].
11. Figure 6: (a) Density of states of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 at 0 GPa. (b) The density of states of ๐ท๐ โ
๐ถ๐๐บ๐2๐4 at 18.8 ๐บ๐๐.
The ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 the structureโs calculated elastic constants are represented in Fig. 7(a)
with applied pressure. The values of ๐ถ11 and ๐ถ33 rises with increasing pressure which describes
the confinement resistance along with prominent a and c-axes. At different pressures, the DC
structure comprises lower resistance to shear than to compression because of the values of
๐ถ12, ๐ถ13 and ๐ถ66 are the half of the ๐ถ11 and ๐ถ33 values. However, the value of ๐ถ44 is 61% of
the ๐ถ11 and ๐ถ33 values. Using the relationship mentioned in Ref. [26], the elastic moduli
containing bulk modulus (๐ต), shear modulus (๐บ), Youngโs modulus (๐ธ) and Poissonโs
ratio (๐) have been calculated at 0, 5, 10, 15, and 18.8 ๐บ๐๐. The calculation of elastic moduli
has been executed by using ๐ถ๐๐บ๐2๐4 the structureโs six elastic constants and recorded in Table
2. The elastic moduli of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 the structure is represented in Fig. 7(b) and displays
the pressure dependence nature. It is noticeable that the ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structureโs bulk
modulus (๐ต) rises linearly with increasing pressure till 18.8 ๐บ๐๐. Moreover, the value of ๐บ
and ๐ธ rises linearly with increasing pressure up to 5 ๐บ๐๐, therefore falls up to 10 ๐บ๐๐ and then
rises again with increasing pressure for DC-structure. The values of ๐ต and ๐ธ reduce with
pressure in the range of 5 โ 10 ๐บ๐๐ because of the reduction in materialโs stiffness and
temperature variation at subsequent pressure range. It is noted that the calculated bulk modulus
by structureโs elastic constants is comparable with attained bulk modulus via 2nd
order energy
of states (EOS), which is recorded in Table 1. It is also discovered that the value of ๐บ is way
less than ๐ต value, which displays the lower resistance to shear deformation than compression
deformation. The materialโs stiffness is approximated by Youngโs modulus ๐ธ.
The materialโs brittleness and ductility are approximated by ๐ต ๐บ
โ ratio. This ratio is coined by
Pughโs theory [49] to play a significant role in material characterization. The material is ductile
when ๐ต ๐บ
โ ratio overtakes 1.75 otherwise possess brittle behavior. This ratio is 1.79 for ๐ท๐ถ โ
๐ถ๐๐บ๐2๐4 at 0 ๐บ๐๐, hence material possesses ductile behavior. The ๐ต ๐บ
โ the ratio rises with
increasing pressure and achieves the peak value of 3.52 at transient pressure (18.8 ๐บ๐๐), as
represented in Fig. 9. Hence the materialโs ductility has been enhanced due to the applied
pressure.
12. Table 2: Calculated elastic constants (๐ถ๐๐ ๐๐ ๐บ๐๐), bulk modulus (B in GPa), shear modulus
(๐บ in GPa), Young modulus (๐ธ in GPa), Poissonโs ratio (๐), and ๐ต ๐บ
โ ratio and Zener
anisotropy factor (๐ด) of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ ๐ถ๐๐บ๐2๐4 the structure under different
pressures.
Phase ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 ๐ท๐ โ ๐ถ๐๐บ๐2๐4
Pressure
(GPa)
0 5 10 15 18.8 20 20 25 30
๐ถ11 66.68 79.26 102.05 119.69 133.35 75.93 265.29 292.82 338.11
๐ถ12 32.92 39.49 55.49 73.94 86.45 42.24 108.27 116.44 132.28
๐ถ13 39.4 57.72 81.09 101.76 113.82 55.06
๐ถ33 61.96 80.97 103.05 134.22 147.94 83.65
๐ถ44 42.25 43.45 47.7 52.56 54.64 49.78 19.92 17.6 16.62
๐ถ66 37.43 42.29 33.83 39.14 41.77 37.01
๐ต 46.52 60.15 80.5 99.55 112.63 159.46 180.53 200.92
๐บ 26.06 25.98 25 28.76 30.45 46.29 49.1 52.57
๐ธ 65.69 67.85 67.6 78.48 83.59 126.24 134.59 144.33
๐ 0.26 0.31 0.36 0.37 0.38 0.37 0.38 0.38
๐ต ๐บ
โ 1.79 2.31 3.22 3.46 3.7 3.45 3.68 3.82
๐ด 2.22 2.13 1.45 1.71 1.78 0.43 0.427 0.38
The materialโs bonding nature is described by Poissonโs ratio ๐, which ranges from 0.26 to
0.38. The materialโs bonding is ionic when the value of ๐ confines from 0.26 to 0.5, but if ๐
is less than 0.26, it contains covalent bonding. Fig. 9 represents the change in ๐ value with
applied pressure. The ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structureโs bonding is ionic because the value of ๐ is
0.26 and this ionic bonding becomes strong with an increase in pressure. As well as, the
materialโs compressibility [50] on the dominant axis of a lattice have been approximated by
axial compressibilities ๐๐ and ๐๐, expressed as
๐๐ =
๐ถ33โ๐ถ13
๐ถ33(๐ถ11+๐ถ12)โ2๐ถ13
2 (4)
๐๐ =
๐ถ11+๐ถ12โ2๐ถ13
๐ถ33(๐ถ11+๐ถ12)โ2๐ถ13
2 (5)
13. where ๐๐ = 7.36 ร 10โ3
๐บ๐๐โ1
and ๐๐ = 6.78 ร 10โ3
๐บ๐๐โ1
for ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 at zero
pressure. The volume compressibility ๐ can be calculated by using axial compressibilities,
expressed as
๐ = โ๐โ1 ๐๐
๐๐
= 2๐๐ + ๐๐ (6)
From equation (6), the value of ๐ is 0.0215 ๐บ๐๐โ1
. The ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structureโs bulk
modulus (๐ต) is 46.51 ๐บ๐๐ considering the inverse operation of ๐. This approachโs reliability
and results precision have been validated from the fact that the calculated value of ๐ต is
comparable with 2๐๐
order Birch-Murnaghan energy of stateโs bulk modulus value.
Figure 7: Calculated elastic constants and elastic moduli of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 as a function of
pressure.
14. The specific materialโs elastic anisotropy strength is determined by Zener anisotropy factor ๐ด.
The material exhibits elastic isotropy when ๐ด = 1 otherwise elastic anisotropy. A large
anisotropic strength may likely lead to microcracks induced in the material that disable the
devices. The relationship between ๐ด and DC structureโs elastic constants [49] are represented
as
๐ด =
2๐ถ66
(๐ถ11โ๐ถ12)
(7)
The anisotropic factor from the ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 the structure was calculated at different
pressures and is shown in Table 2. The DC-phaseโs anisotropic factor falls with increasing
pressure up to 18.8 ๐บ๐๐.
The conversion from DC to DR structure for ๐ถ๐๐บ๐2๐4 semiconductor has occurred at
18.8 ๐บ๐๐. The ๐ท๐ โ ๐ถ๐๐บ๐2๐4 the structure is illustrated by three independent elastic
constants (๐ถ11, ๐ถ12 and ๐ถ44) and exhibits a cubic-shaped lattice. Fig. 8(a) represents the
calculated elastic constants at 20, 25, and 30 ๐บ๐๐ pressures and are recorded in Table 2. The
mechanical stability of steady cubic structure must satisfy the Born stability criteria [48],
illustrated as
1) The difference in ๐ถ11, ๐ถ12 and ๐ should be greater than zero.
2) The half of the difference between ๐ and ๐ถ11 should be less than ๐ถ12.
3) The difference in ๐ถ44 and ๐ should be greater than zero.
15. Figure 8: Calculated elastic constants and elastic moduli of ๐ท๐ โ ๐ถ๐๐บ๐2๐4 as a function of
pressure.
The ๐ท๐ โ ๐ถ๐๐บ๐2๐4 structureโs elastic constants ๐ถ11 and ๐ถ12 rise tediously with increasing
pressure but ๐ถ44 falls tediously with an increase in pressure. It is noted that the ๐ถ11 rises rapidly
with pressure than ๐ถ12. Hence, the DR structure contains higher resistance to compression than
to shear. The atomic bondingโs angular character is illustrated by Cauchy pressure for the cubic
structureโs elastic constants. The Cauchy pressure [51] has been determined by the difference
in ๐ถ12 and ๐ถ44. The metallic and non-metallic nature of this structure is defined by the Cauchy
pressureโs positive and negative values, respectively. It is found that the ๐ท๐ โ ๐ถ๐๐บ๐2๐4 the
structure exhibits metallic behavior due to positive values of calculated Cauchy pressure at
20, 25, and 30 ๐บ๐๐. The Cauchy pressureโs positive values increase with rising pressure and
indicate strong metallic property. The ๐ท๐ โ ๐ถ๐๐บ๐2๐4 is ductile in nature because of the
Cauchy pressureโs positive values. It also fits well with our computed electronic band structure
and DOS demonstrating its conductive character after phase transition occurs.
Using the relationship in Refs. [26], [52], the ๐ท๐ โ ๐ถ๐๐บ๐2๐4 structureโs bulk modulus (๐ต),
shear modulus (๐บ), Youngโs modulus (๐ธ) and Poissonโs ratio (๐) have been evaluated at
20, 25, and 30 ๐บ๐๐. The ๐ท๐ โ ๐ถ๐๐บ๐2๐4 structureโs elastic moduli are dependent on applied
pressures are recorded in Table 2. The value of ๐ต is more than a value of ๐บ for DR structure,
as illustrated in Fig. 8(b). Hence, the ๐ท๐ โ ๐ถ๐๐บ๐2๐4 the structure exhibits higher resistance to
compression than to shear stress. Fig. 8(b) also represents the materialโs stiffness increases with
rising pressure ranges from 20 โ 30 ๐บ๐๐.
16. Figure 9: Pressure dependence of ๐ต ๐บ
โ , ๐ and ๐ด of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 and ๐ท๐ โ ๐ถ๐๐บ๐2๐4.
For ๐ท๐ โ ๐ถ๐๐บ๐2๐4, the ๐ต ๐บ
โ the ratio rises from 3.45 at 20 ๐บ๐๐ to 3.82 at 30 ๐บ๐๐, as
illustrated in Fig. 9. It is revealed that the DR structure exhibits ductile nature at applied
pressure 20 ๐บ๐๐ and beyond.
The computed value of ๐ is 0.37 at 20 ๐บ๐๐ for the DR structure and exposes the strong ionic
bonding. The value of ๐ rises linearly with increasing pressure up to 25 ๐บ๐๐ and then displays
the constant state.
The relation between anisotropic factor ๐ด and elastic constants of DR structure [53] is
represented as
๐ด =
2๐ถ44
(๐ถ11โ๐ถ12)
(8)
For ๐ท๐ โ ๐ถ๐๐บ๐2๐4 structure, the values of ๐ด are calculated at different pressures and are
recorded in Table 2. It is found that the value of ๐ด decrease linearly with an increase in pressure
for ๐ท๐ โ ๐ถ๐๐บ๐2๐4, as shown in Fig. 9. Hence, the DR structure of ๐ถ๐๐บ๐2๐4 exhibits elastic
anisotropic nature at applied pressure ranges from 20 โ 30 ๐บ๐๐.
3.3 Optical Properties
The materialโs optical properties can be evaluated by complex dielectric function ๐(๐). The
real and imaginary parts of the dielectric function (in the x-direction) are computed by the inter-
band transitions [56] between the valence band and the conduction bands. The complex
dielectric tensors are represented as
๐๐ผ๐ฝ(๐) = ๐1 + ๐๐2 (9)
17. ๐ผ๐ ๐๐ผ๐ฝ(๐) =
โ2๐2
๐๐2๐2
โ โซ ๐๐ < ๐๐|๐๐ผ
|๐ฃ๐ >< ๐ฃ๐|๐๐ฝ
|๐๐ > ๐ฟ(๐๐๐ โ ๐๐ฃ๐ โ ๐)
๐,๐ฃ (10)
๐ ๐ ๐๐ผ๐ฝ(๐) = ๐ฟ๐ผ๐ฝ +
2
๐
๐ โซ
๐1๐ผ๐ ๐๐ผ๐ฝ(๐1)
๐12
โ๐2
๐๐1
โ
0
(11)
where P is the integralโs principal value. From equation (10), the reduced Plankโs constant,
electronโs mass, angular frequency, speed of light, and initial charge of the electron are denoted
by โ, ๐, ๐, ๐ and ๐, respectively. The ๐ฟ are represented as a partial change in parameters.
The dispersion and absorption of incident photons determine the dielectric functionโs real part
๐1(๐) and imaginary part ๐2(๐), respectively. The elements of the momentum matrix are
bounded by the occupied and unoccupied wave functions to calculate the imaginary part ๐2(๐).
Using the Kramer-Kronig relationship [54], the real part ๐1(๐) is obtained from ๐2(๐).
The imaginary part of the dielectric function ๐2(๐) is represented in Fig. 10. The fundamental
absorption edge (at 0 ๐บ๐๐) is detected at 2.08 ๐๐, which reveals the inter-band transition
among the lowermost conduction band and the uppermost valence band. The dominant states
of the uppermost valence band are ๐ โ 3๐ and ๐ถ๐ โ 5๐ . Due to the transition in ๐ โ 3๐ and
๐บ๐ โ 4๐ states, the curveโs peak achieves at 5.94 ๐๐ towards 0 ๐บ๐๐ pressure. The ๐2(๐) peaks
appear at 5.17 and 5.43 ๐๐ towards 10 ๐บ๐๐ and 18.8 ๐บ๐๐ pressures, respectively. Due to the
blue shift phenomena [55], the curve peaks tend towards greater energies with increasing
pressure ranges between 10 to 18.8 ๐บ๐๐.
Figure 10: The calculated imaginary part of the dielectric function of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4.
The photon energy falls with increasing pressure ranges between 5 to 10 ๐บ๐๐ because of the
instant variation in wavelength. This blue shift phenomena are dependent on the applied
18. pressure and also imitates other optical properties. Due to energy bandgap falls with increasing
pressure ranges from 0 ๐บ๐๐ to 18.8 ๐บ๐๐, the sharp falling edge tilt towards the higher energies.
Fig. 11 illustrates the dielectric functionโs real part. The photon energy ranges from 0 ๐๐ to
35 ๐๐ in this curve. At zero pressure, the DC structureโs static dielectric constant is found to
be 6.42 and is recorded in Table 3 including theoretical and experimental results. It is crucial
to acknowledge the fact that the results presented in this section are comparable with the
literature results.
Optical Parameters
under pressure
๐1(0) ๐(0) ๐ (0)
This
work
Literature
Values
This
work
Literature
Values
This
work
Literature
Values
0 GPa 6.42 5.86a
2.534 2.35a
, 2.67b
0.188 0.157a
5 GPa 6.83 2.613 0.199
10 GPa 7.24 2.69 0.21
15 GPa 7.63 2.762 0.219
18.8 GPa 7.88 2.807 0.198
a
Theoretical Ref. [58].
b
Experimental Ref. [60].
Table 3 also represents the calculated value of ๐1(0) at 10 ๐บ๐๐ and 18.8 ๐บ๐๐ pressures. It is
found that the ๐1(0), ๐(0) and ๐ (0) values rise with increasing pressure, also described in Ref.
[29].
Fig. 12 represents the DC structureโs refractive index ๐(๐) and is calculated at 0, 10, and
18.8 ๐บ๐๐. At 0 ๐บ๐๐, the static refractive index is found to be 2.53 and is recorded in Table 3.
The refractive index ๐(๐) is analogous of ๐1(๐) curve. The calculated result is nearer to the
experimental value [58] than the theoretical literature value [60]. At 10 ๐บ๐๐ and 18.8 ๐บ๐๐
pressures, the ๐(0) values are 2.69 and 2.81, respectively.
19. Figure 11: The calculated real part of the dielectric function of the ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 under
pressure.
Fig. 12 represents the DC structureโs refractive index ๐(๐) and is calculated at 0, 10, and
18.8 ๐บ๐๐. At 0 ๐บ๐๐, the static refractive index is found to be 2.53 and is recorded in Table 3.
The refractive index ๐(๐) is analogous of ๐1(๐) curve. The calculated result is nearer to the
experimental value than the theoretical literature value. At 10 ๐บ๐๐ and 18.8 ๐บ๐๐ pressures,
the ๐(0) values are 2.69 and 2.81, respectively.
Due to a blue shift, the peaks tend to have higher energies. The ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structure can
be used for photonic applications due to the high value of the refractive index.
The DC structureโs extinction coefficient ๐(๐) is illustrated in Fig. 13 and is calculated at
0, 10, and 18.8 ๐บ๐๐. The ๐(๐) curveโs peak achieves at 7.27 ๐๐ towards 0 ๐บ๐๐ pressure. The
absorption is dominant at this point and describes the zero value of ๐1(๐). At 10 ๐บ๐๐ and
18.8 ๐บ๐๐ pressures, the peak values of ๐(๐) are achieved at 7.28 and 7.63 ๐๐, respectively.
20. Figure 12: The calculated refractive index of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4.
Figure 13: The calculated extinction coefficient of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4.
21. Figure 14: The calculated absorption coefficient of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4.
The infiltration limit of light particles into material containing specific wavelength has been
described by absorption coefficient ๐ผ(๐) until the materialโs absorption process is initiated.
The ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structureโs absorption coefficient ๐ผ(๐) is illustrated in Fig. 14 and is
calculated at 0, 10, and 18.8 ๐บ๐๐. The photon energy ranges from 0 to 35 ๐๐ in this curve.
Due to the blue shift phenomena, the absorption curves tend towards greater energies with
increasing pressure ranges from 10 โ 18.8 ๐บ๐๐. The peak values of ๐ผ(๐) are found at
9.05 ๐๐, 8.08 ๐๐ and 9.33 ๐๐ towards 0, 10, and 18.8 ๐บ๐๐ pressures, respectively.
Fig. 15 represents the DC structureโs reflectivity ๐ (๐) in the effect of applied pressure. At
0, 10 and 18.8 ๐บ๐๐ ๐๐๐๐ ๐ ๐ข๐๐๐ , the peak values of ๐ (๐) are found at 9.5 ๐๐, 10.18 ๐๐, and
9.83 ๐๐, respectively. The reflectivity curve peaks shift towards higher energies with
increasing pressure ranges from 0 to 10 ๐บ๐๐. But, this curveโs peak falls with a further increase
in pressure because of the instant variation in blue shift and materialโs stiffness. If ๐1 tends to
zero, the energy spectrum belongs to the region of high reflectivity.
22. Figure 15: The calculated reflectivity spectrum ๐ (๐) of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4.
As illustrated in Fig. 15, the ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 structureโs incident light radiation is found to be
18.8% at zero pressure. It is important to acknowledge the fact that calculated results are closer
to theoretical literature results and are recorded in Table 3. At 10 ๐บ๐๐ and 18.8 ๐บ๐๐ pressures,
the reflection rises to 21% and falls to 19.8%, respectively due to the varied stiffness of the
material. The ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 the structure can be used as a coating agent for high-frequency
UV radiationโs shielding process.
The energy loss function ๐ฟ(๐) depicts the energy forfeit by an electron moving rapidly through
the semiconductor. The DC structureโs loss function is represented in Fig. 16. After applying
0, 10, and 18.8 ๐บ๐๐ pressures, the screening plasma frequency [61] is detected at
18.3 ๐๐, 19.55 ๐๐, and 20.18 ๐๐, respectively. The zero-crossing of ๐1(0) and concurrent
decrement of ๐ (๐) the curve has been defined by the loss functionโs peak.
23. Figure 16: The calculated loss function ๐ฟ(๐) of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4.
Figure 17: The calculate bandgaps and refractive index of ๐ท๐ถ โ ๐ถ๐๐บ๐2๐4 with pressure.
Fig. 17 demonstrates the bandgap and refractive index variation with pressure for ๐ท๐ถ โ
๐ถ๐๐บ๐2๐4 structure. The bandgap falls monotonically with an increase in pressure whereas the
refractive index rises linearly with increasing pressure. The maximum value of bandgap and
refractive index are 2.09 and 2.81, which is achieved at 0 ๐บ๐๐ and 18.8 ๐บ๐๐ pressures,
respectively. Noticeably, the bandgap is in the visible region at zero pressure and tends towards
the ultraviolet (UV) region with increasing pressure.
4. Conclusion
In the paper presented, the ๐ถ๐๐บ๐2๐4 semiconductorโs electronic, structural, elastic and optical
properties were studied using the full potential linearized augmented plane waves (FP-LAPW)
24. method as part of the GGA function. The ๐ถ๐๐บ๐2๐4 semiconductorโs phase transition has been
detected from DC to DR structure at 18.8 ๐บ๐๐ pressure. It is found that the stability of DC
structure is higher than the DR structure until 18.8 ๐บ๐๐ pressure and then vica versa after
18.8 ๐บ๐๐ pressure. At 0 ๐บ๐๐ and 18.8 ๐บ๐๐ pressures, the optimal lattice constants, bulk
moduli and energy band gaps have been determined for both DC and DR structures. Table 1
records the computed values, which are compared to the experimental and theoretical literature
values that are accessible. The computed values of lattice constants ๐ and ๐ are overestimated
by 2.5% of experimental values. Therefore, the density of states of ๐ถ๐๐บ๐2๐4 semiconductorโs
DC and DR (both) phases have been described and are contributed in band structure
calculation. Table 2 shows the computed elastic stiffness constants (๐ถ๐๐), ๐ต, ๐บ, ๐ธ, ๐, ๐ด and ๐ต ๐บ
โ
ratio for DC and DR structures, respectively for pressures of 0, 5, 10, 15 and 18.8 ๐บ๐๐ for DC
and 20, 25 and 30 ๐บ๐๐ for DR. Moreover, no comparable data is available, thus our estimates
will be used to guide future research on this semiconductor. At zero pressure, the computed
values of ๐ต ๐บ
โ and ๐ are 1.79 and 0.26, respectively and demonstrates the ductile and ionic
nature for DC structure. Further, the computed value of the ๐ต ๐บ
โ and ๐ reveal the ductile nature
and ionic behavior of ๐ท๐ โ ๐ถ๐๐บ๐2๐4 at 20 ๐บ๐๐ pressure. The optical spectra of ๐ท๐ถ โ
๐ถ๐๐บ๐2๐4 involves dielectric function ๐(๐), reflectivity ๐ (๐), absorption coefficient ๐ผ(๐),
refractive index ๐(๐), extinction coefficient ๐ (๐) and energy loss function ๐ฟ(๐), which are
computed for pressures of 0, 10 and 18.8 ๐บ๐๐. Table 3 lists the computed values of ๐1(0), ๐(0)
and ๐ (0) for pressures of 0, 10 and 18.8 ๐บ๐๐. The computed values of real dielectric function,
refractive index and reflectivity are compared with theoretical literature values and
experimental values. It is noted that the value of refractive index rises with increase in pressure
and decrease in energy band gap. The calculated values agree better with experimental values
than previous literature values, indicating the accuracy of the present computations while
awaiting experimental conformation.
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