Structural, Electronic, and Optical Properties of CsPb(Br1−xClx)3 Perovskite: First-Principles Study with PBE–GGA and mBJ–GGA Methods

The effect of halide composition on the structural, electronic, and optical properties of CsPb(Br1−xClx)3 perovskite was investigated in this study. When the chloride (Cl) content of x was increased, the unit cell volume decreased with a linear function. Theoretical X-ray diffraction analyses showed that the peak (at 2θ = 30.4°) shifts to a larger angle (at 2θ = 31.9°) when the average fraction of the incorporated Cl increased. The energy bandgap (Eg) was observed to increase with the increase in Cl concentration. For x = 0.00, 0.25, 0.33, 0.50, 0.66, 0.75, and 1.00, the Eg values calculated using the Perdew–Burke–Ernzerhof potential were between 1.53 and 1.93 eV, while those calculated using the modified Becke−Johnson generalized gradient approximation (mBJ–GGA) potential were between 2.23 and 2.90 eV. The Eg calculated using the mBJ–GGA method best matched the experimental values reported. The effective masses decreased with a concentration increase of Cl to 0.33 and then increased with a further increase in the concentration of Cl. Calculated photoabsorption coefficients show a blue shift of absorption at higher Cl content. The calculations indicate that CsPb(Br1−xClx)3 perovskite could be used in optical and optoelectronic devices by partly replacing bromide with chloride.


Introduction
Over the last decade, organic and inorganic perovskites have gained considerable attention in the field of optoelectronics, and more recently in solar cells [1][2][3][4][5][6][7][8] and light-emitting devices [9][10][11][12][13], thanks to the reduced costs [14], high quantum efficiency of photoluminescence [15], and extensively tunable emission wavelengths of these materials [16][17][18]. Recently, inorganic mixed-halide CsPb(Br 1−x Cl x ) 3 compositions were used for creating various nanophotonic components because they exhibit electroluminescence in the green [12,19] to blue [20] optical ranges. CsPbBr 3 exhibits orthorhombic symmetry at temperatures below 88 • C. When the temperature increases, structural distortion occurs and the structure of CsPbBr 3 is converted to tetragonal (88 • C < T < 130 • C), and subsequently to cubic at higher temperatures (T > 130 • C) [17,18,[21][22][23][24][25][26][27][28][29][30][31][32][33][34][35][36][37][38]. In comparison, at temperatures below 42 • C, CsPbCl 3 exhibits orthorhombic symmetry. When temperature increases, structural distortion occurs and the CsPbCl 3 structure is converted to tetragonal (42 • C < T < 47 • C), and subsequently to cubic at higher temperatures (T > 47 • C) [18,39]. The energy band gap (E g ) can be adjusted by adding The WC-GGA potential was determined by evaluating the ground state properties. These properties include the lattice constant a, bulk modulus B, and its pressure derivative B′. Structural optimization was performed by minimizing total energy with respect to cell volume, and the results of total energy versus unit-cell volume were fitted with Murnaghan's state-of-the-art equation [68]. The total energy versus volume graph is shown in Figure 2. The results of a, B, and B′ are shown in Table 1 with the corresponding theoretical and experimental data available in the literature. As shown in Table 1, the lattice constants of the CsPbBr3 and CsPbCl3 structures are in good agreement with recent theoretical and experimental results, thereby proving that our computational parameters are valid. The WC-GGA potential was determined by evaluating the ground state properties. These properties include the lattice constant a, bulk modulus B, and its pressure derivative B . Structural optimization was performed by minimizing total energy with respect to cell volume, and the results of total energy versus unit-cell volume were fitted with Murnaghan's state-of-the-art equation [68]. The total energy versus volume graph is shown in Figure 2. The results of a, B, and B are shown in Table 1 with the corresponding theoretical and experimental data available in the literature. As shown in Table 1, the lattice constants of the CsPbBr 3 and CsPbCl 3 structures are in good agreement with recent theoretical and experimental results, thereby proving that our computational parameters are valid.
Moreover, excellent agreement was observed between our obtained value of the lattice parameter for CsPbBr3 (5.8859 Å) and its experimental value of 5.85 (Å) obtained in [69]. Moreover, the value of the lattice parameter for CsPbCl3 was 5.6379 Å, which was in excellent agreement with the experimental value of 5.605 Å obtained in [70]. Theoretical X-ray diffraction (XRD) patterns were obtained using the visualization for electronic and structural analysis (VESTA 3, Ibaraki, Japan) [71] (see Figure 3). The diffraction peaks of CsPbBr3 moved toward CsPbCl3 when x changed from 0.00 to 1.00. As shown in Table 1, when the Cl content x increases from 0.00 to 1.00, the volume of the unitcell decreases in proportion x with the function of V(x) = 815.29916 -112.58513x (Å) 3 , as shown in Figure 4.  Moreover, excellent agreement was observed between our obtained value of the lattice parameter for CsPbBr 3 (5.8859 Å) and its experimental value of 5.85 (Å) obtained in [69]. Moreover, the value of the lattice parameter for CsPbCl 3 was 5.6379 Å, which was in excellent agreement with the experimental value of 5.605 Å obtained in [70]. Theoretical X-ray diffraction (XRD) patterns were obtained using the visualization for electronic and structural analysis (VESTA 3, Ibaraki, Japan) [71] (see Figure 3). The diffraction peaks of CsPbBr 3 moved toward CsPbCl 3 when x changed from 0.00 to 1.00. As shown in Table 1, when the Cl content x increases from 0.00 to 1.00, the volume of the unit-cell decreases in proportion x with the function of V(x) = 815.29916 -112.58513x (Å) 3 , as shown in Figure 4.  Moreover, excellent agreement was observed between our obtained value of the lattice parameter for CsPbBr3 (5.8859 Å) and its experimental value of 5.85 (Å) obtained in [69]. Moreover, the value of the lattice parameter for CsPbCl3 was 5.6379 Å, which was in excellent agreement with the experimental value of 5.605 Å obtained in [70]. Theoretical X-ray diffraction (XRD) patterns were obtained using the visualization for electronic and structural analysis (VESTA 3, Ibaraki, Japan) [71] (see Figure 3). The diffraction peaks of CsPbBr3 moved toward CsPbCl3 when x changed from 0.00 to 1.00. As shown in Table 1, when the Cl content x increases from 0.00 to 1.00, the volume of the unitcell decreases in proportion x with the function of V(x) = 815.29916 -112.58513x (Å) 3 , as shown in Figure 4.

Electronic Properties
First, the electronic structures for CsPb(Br1−xClx)3 were calculated by PBE-GGA and mBJ-GGA potentials without/with SOC. Figure 5 shows the calculated band structures of

Electronic Band Structure
First, the electronic structures for CsPb(Br 1−x Cl x ) 3 were calculated by PBE-GGA and mBJ-GGA potentials without/with SOC. Figure 5 shows the calculated band structures of CsPb(Br 1−x Cl x ) 3 using the mBJ-GGA potentials without/with SOC. In contrast, Figure 6 shows those using the potential of PBE-GGA without SOC. The band structures have a direct transition character at M, which can improve the photoabsorption coefficient and accelerate the rate of radiative recombination [84]. The calculated E g for CsPbBr 3 , CsPbBr 2. 75 Cl 0.25 , CsPbBr 2 Cl, CsPbBr 1.5 Cl 1.5 , CsPbBrCl 2 , CsPbBr 0. 25 Table 2. The E g calculated using mBJ-GGA were the closest to the experimental values [51][52][53][54][55].     By including the effect of SOC, the calculated E g values are smaller than the experimental by approximately 1.23 and 1.28 eV for pure CsPbBr 3 and CsPbCl 3 , respectively, and result in more reasonable band dispersions [85,86]. The SOC causes the conduction band (CB) to decrease by splitting it into a twofold degenerated state (p 1/2 ) corresponding to light electrons and a fourfold degenerate state (p 3/2 ) corresponding to heavy electrons at this point [57,87,88]. In contrast, the valance band (VB) showed no significant change in this area [57,87,88]. The correction was thus applied to the E g with the following equation [78,84,89]: , and ∆E g (B) are the E g corrections for the CsPb(Br 1−x Cl x ) 3 , CsPbBr 3 , and CsPbCl 3 compounds, respectively. Figure 7 shows the calculated E g using PBE-GGA, mBJ-GGA, mBJ-GGA + SOC, and corrected mBJ-GGA + SOC(C). The calculated E g by mBJ-GGA and mBJ-GGA + SOC(C) are in good agreement with the experimental values [53,55]. The small differences between the theoretical and experimental values are mainly attributed to the changed size for different mixed-halide [84], as depicted in the XRD patterns and the small 1 × 1 × 4 supercell models.      The optical bowing parameter (b) was calculated for determining the relationship between the E g and the Cl composition x [78,90,91] using the following equation: where b is the bowing parameter; E g (A) and E g (B) are the band gaps of pure A and B, respectively; and E g (x) is the bandgap of A, B mixed-halide perovskites with the composition x. The dependence of the obtained E g on the concentration of Cl (x) was given by fitting the nonlinear variation with the quadratic function as follows:  3 perovskite using PBE-GGA, mBJ-GGA, and mBJ-GGA + spin-orbital coupling (SOC) potentials, and mBJ-GGA + SOC(C). * Koller, Tran, and Blaha modified Becke-Johnson potential; ** Gritsenko, van Leeuwen, van Lenthe, and Baerends-Solid and Correlation; *** Quantum Espresso 6.0; **** Hybrid nonlocal exchange-correlation functional.
The influences of the dispersive nature of the conduction band (CB) and valence band (VB) on the effective masses (m e * and m h * ) are shown in Figure 8. The effective masses are related to carrier mobility, which is an essential criterion for the excellent power efficiency of photovoltaic materials [85]. m e * and m h * at the band edges are related to the band dispersions. As a result, the effective masses at the CB minimum (CBM) and VB maximum (VBM) were approximated by a parabola [85,[97][98][99]. By fitting the VB and CB edges, the effective mass (m * ) was evaluated numerically using the following equations: where m * is the effective mass of the charge carrier, i and j are the reciprocal components, ε n ( k ) is the energy dispersion function of the n th band, k represents the wave vector, and represents the reduced Planck constant. The mBJ-GGA calculation without SOC results in an accurate Eg value; however, the previous studies stated that the introduction of SOC increases band dispersion and results in more accurate effective masses with respect to DFT calculation without SOC [23,78,79,86,92,96,[100][101][102]. Therefore, we employ mBJ-GGA + SOC to evaluate the effective charge masses. The values of me * and mh * decreased significantly with the increase in Cl concentration up to 0.33 owing to the decrease of parabolic nature of the band structure [103]. The increased parabolic nature caused a drastic increase of the effective mass of carriers for high concentration of Cl [103]. The calculated effective charge masses around the M point of the Brillouin zone obtained by evaluating the second derivatives are shown in Table S8 (Supplementary Materials). The reduced masses were calculated using the following equation: The effective Bohr diameter of a Wannier-Mott exciton (a0) can be defined [99] using the following equation: where (∞) is the dielectric constant in the limit of infinite wavelength, and the exciton binding energy ( ) is given by the following: For calculating Eb, we need to know the dielectric constant of the material ε(∞) and the reduced masses (μr), which can be obtained by DFT calculation. The estimated a0 and Eb values were between 5.6 and 8.9 nm and between 41 and 72 meV, respectively, which were in good agreement with other theoretical [16,75,100,104,105] and experimental [106,107] values. A weaker Eb indicates that the charge carriers behave more like free charge carriers [99].
The dependence of the obtained a0 and Eb values on the concentration of Cl (x) was determined by fitting the nonlinear variation as Cl concentration x with the linear and quadratic functions as follows: The mBJ-GGA calculation without SOC results in an accurate E g value; however, the previous studies stated that the introduction of SOC increases band dispersion and results in more accurate effective masses with respect to DFT calculation without SOC [23,78,79,86,92,96,[100][101][102]. Therefore, we employ mBJ-GGA + SOC to evaluate the effective charge masses. The values of m e * and m h * decreased significantly with the increase in Cl concentration up to 0.33 owing to the decrease of parabolic nature of the band structure [103]. The increased parabolic nature caused a drastic increase of the effective mass of carriers for high concentration of Cl [103]. The calculated effective charge masses around the M point of the Brillouin zone obtained by evaluating the second derivatives are shown in Table S8 (Supplementary Materials). The reduced masses µ r were calculated using the following equation: The effective Bohr diameter of a Wannier-Mott exciton (a 0 ) can be defined [99] using the following equation: where ε(∞) is the dielectric constant in the limit of infinite wavelength, and the exciton binding energy (E b ) is given by the following: For calculating E b , we need to know the dielectric constant of the material ε(∞) and the reduced masses (µ r ), which can be obtained by DFT calculation. The estimated a 0 and E b values were between 5.6 and 8.9 nm and between 41 and 72 meV, respectively, which were in good agreement with other theoretical [16,75,100,104,105] and experimental [106,107] values. A weaker E b indicates that the charge carriers behave more like free charge carriers [99].
The dependence of the obtained a 0 and E b values on the concentration of Cl (x) was determined by fitting the nonlinear variation as Cl concentration x with the linear and quadratic functions as follows:

Density of States (DOS)
The total DOS (TDOS) was calculated using the mBJ-GGA potential, as shown in Figure  10. However, as the concentration (x) increased from 0.00 to 1.00, the DOS edges changed. The partial DOS (PDOS) shown in Figure 11 are based on the mBJ-GGA potential, because we are interested in the valence band (VB) and conduction band (CB) components. Previous studies have shown that inorganic cation Cs + does not contribute to VB maximum (VBM) and CB minimum (CBM), and only maintains overall load neutrality and structural stability [23,26,37,72,75,78,79,82,85,92,93,100,101,108,109]. Therefore, we observed only the states of Pb and halogen elements (Cl and Br), as shown in Figure 11. The VBM originates mainly from the p orbitals of Br and Cl, and a small number of contributions from s orbitals of Pb can also be observed. The CBM originated from the p states of Pb and halogen elements (Cl and Br). The CB structure is relatively similar for all of the compounds, and the CBM for each compound comprises mainly p orbitals of Pb and halogen elements (Cl and Br). The uppermost VB is steep, while the lowermost CB in PDOS is relatively flat.

Density of States (DOS)
The total DOS (TDOS) was calculated using the mBJ-GGA potential, as shown in Figure 10. However, as the concentration (x) increased from 0.00 to 1.00, the DOS edges changed. The partial DOS (PDOS) shown in Figure 11 are based on the mBJ-GGA potential, because we are interested in the valence band (VB) and conduction band (CB) components. Previous studies have shown that inorganic cation Cs + does not contribute to VB maximum (VBM) and CB minimum (CBM), and only maintains overall load neutrality and structural stability [23,26,37,72,75,78,79,82,85,92,93,100,101,108,109]. Therefore, we observed only the states of Pb and halogen elements (Cl and Br), as shown in Figure 11. The VBM originates mainly from the p orbitals of Br and Cl, and a small number of contributions from s orbitals of Pb can also be observed. The CBM originated from the p states of Pb and halogen elements (Cl and Br). The CB structure is relatively similar for all of the compounds, and the CBM for each compound comprises mainly p orbitals of Pb and halogen elements (Cl and Br). The uppermost VB is steep, while the lowermost CB in PDOS is relatively flat.

Density of States (DOS)
The total DOS (TDOS) was calculated using the mBJ-GGA potential, as shown in Figure  10. However, as the concentration (x) increased from 0.00 to 1.00, the DOS edges changed. The partial DOS (PDOS) shown in Figure 11 are based on the mBJ-GGA potential, because we are interested in the valence band (VB) and conduction band (CB) components. Previous studies have shown that inorganic cation Cs + does not contribute to VB maximum (VBM) and CB minimum (CBM), and only maintains overall load neutrality and structural stability [23,26,37,72,75,78,79,82,85,92,93,100,101,108,109]. Therefore, we observed only the states of Pb and halogen elements (Cl and Br), as shown in Figure 11. The VBM originates mainly from the p orbitals of Br and Cl, and a small number of contributions from s orbitals of Pb can also be observed. The CBM originated from the p states of Pb and halogen elements (Cl and Br). The CB structure is relatively similar for all of the compounds, and the CBM for each compound comprises mainly p orbitals of Pb and halogen elements (Cl and Br). The uppermost VB is steep, while the lowermost CB in PDOS is relatively flat.  For a detailed view of the band structure of CsPbBr1.5Cl1.5, PDOS was plotted on the band structure using the mBJ-GGA potential (Figure 12a). The PDOS (Figure 12b) indicated that the effects of the Cs atoms did not follow any specific rules, whereas it shows that the Eg trends are the result of the effects of Pb and Br [93]. Similar band structures of CsPbBr3 and CsPbCl3 with PDOS are shown in Figure S1 (Supplementary Materials). To support this observation, the total charge density distributions are calculated and presented in the (001) plane, as shown in Figure 13a-g, with the structures adjacent to each concentration. The nature of bonding among the atoms could be analyzed using the map of electronic charge density distribution [72,109]. According to the Pauling scale, the electro-negativity of Cs, Pb, Br, and Cl is 0.79, 2.33, 2.96, and 3.16, respectively. For the description of the bonding character, the difference of the electro-negativity (XA-XB) is crucial [110], where XA and XB are the electro-negativities of the A and B atoms, respectively. The percentage of the ionic character (IC) of the bonding can be obtained from the following equation [111]: For a detailed view of the band structure of CsPbBr 1.5 Cl 1.5 , PDOS was plotted on the band structure using the mBJ-GGA potential (Figure 12a). The PDOS (Figure 12b) indicated that the effects of the Cs atoms did not follow any specific rules, whereas it shows that the E g trends are the result of the effects of Pb and Br [93]. Similar band structures of CsPbBr 3 and CsPbCl 3 with PDOS are shown in Figure S1 (Supplementary Materials). For a detailed view of the band structure of CsPbBr1.5Cl1.5, PDOS was plotted on the band structure using the mBJ-GGA potential (Figure 12a). The PDOS (Figure 12b) indicated that the effects of the Cs atoms did not follow any specific rules, whereas it shows that the Eg trends are the result of the effects of Pb and Br [93]. Similar band structures of CsPbBr3 and CsPbCl3 with PDOS are shown in Figure S1 (Supplementary Materials). To support this observation, the total charge density distributions are calculated and presented in the (001) plane, as shown in Figure 13a-g, with the structures adjacent to each concentration. The nature of bonding among the atoms could be analyzed using the map of electronic charge density distribution [72,109]. According to the Pauling scale, the electro-negativity of Cs, Pb, Br, and Cl is 0.79, 2.33, 2.96, and 3.16, respectively. For the description of the bonding character, the difference of the electro-negativity (XA-XB) is crucial [110], where XA and XB are the electro-negativities of the A and B atoms, respectively. The percentage of the ionic character (IC) of the bonding can be obtained from the following equation [111]: To support this observation, the total charge density distributions are calculated and presented in the (001) plane, as shown in Figure 13a-g, with the structures adjacent to each concentration. The nature of bonding among the atoms could be analyzed using the map of electronic charge density distribution [72,109]. According to the Pauling scale, the electro-negativity of Cs, Pb, Br, and Cl is 0.79, 2.33, 2.96, and 3.16, respectively. For the description of the bonding character, the difference of the electro-negativity (X A -X B ) is crucial [110], where X A and X B are the electro-negativities of the A and B atoms, respectively. The percentage of the ionic character (IC) of the bonding can be obtained from the following equation [111]: Materials 2020, 13, x FOR PEER REVIEW 12 of 22 Using this equation, the obtained % IC of Cs-Br, Cs-Cl, Pb-Br, and Pb-Cl was 69.85, 75.44, 10.02, and 15.82, which indicated that the bond between Cs-Cl/Br is mostly ionic and partially covalent. In contrast, the Pb-Cl/Br bond is mostly covalent and partially ionic. Strong covalent bonds between Pb-halides have also been predicted by previous reports [72,79,110,112].

Optical Properties
The study of the optical properties of the CsPb(Br1−xClx)3 perovskite is essential because of its potential for use in photonic and optoelectronic applications. Calculations of dielectric functions with both real ε1(ω) and imaginary ε2(ω) parts, refractive index n(ω), extinction coefficient k(ω) , absorption coefficient α(ω), optical conductivity (ω), and reflectivity R(ω) were explored by mBJ-GGA potential. These optical parameters can be attracted by the knowledge of the complex dielectric function ε(ω) = ε1 (ω) + iε2 (ω). The imaginary part of the dielectric function ε2 (ω), according to the perturbation theory, is given by the following equation [113,114]: where p is the moment matrix element between the band α and β states within the crystal momentum k. ik and jk are the crystal wave functions corresponding to the conduction and valence bands with the crystal wave vector k, respectively. The real part ε (ω) of the dielectric function can be expressed as follows [114]: Using this equation, the obtained % IC of Cs-Br, Cs-Cl, Pb-Br, and Pb-Cl was 69.85, 75.44, 10.02, and 15.82, which indicated that the bond between Cs-Cl/Br is mostly ionic and partially covalent. In contrast, the Pb-Cl/Br bond is mostly covalent and partially ionic. Strong covalent bonds between Pb-halides have also been predicted by previous reports [72,79,110,112].

Optical Properties
The study of the optical properties of the CsPb(Br 1−x Cl x ) 3 perovskite is essential because of its potential for use in photonic and optoelectronic applications. Calculations of dielectric functions with both real ε 1 (ω) and imaginary ε 2 (ω) parts, refractive index n(ω), extinction coefficient k(ω), absorption coefficient α(ω), optical conductivity σ(ω), and reflectivity R(ω) were explored by mBJ-GGA potential. These optical parameters can be attracted by the knowledge of the complex dielectric function ε(ω) = ε 1 (ω) + iε 2 (ω). The imaginary part of the dielectric function ε 2 (ω), according to the perturbation theory, is given by the following equation [113,114]: where p is the moment matrix element between the band α and β states within the crystal momentum k. i k and j k are the crystal wave functions corresponding to the conduction and valence bands with the crystal wave vector k, respectively. The real part ε 1 (ω) of the dielectric function can be expressed as follows [114]: where p is the value of the principal of the integral. The absorption coefficient, optical conductivity, refractive index, extinction coefficient, and reflectance denoted by α (ω), σ (ω), n (ω), k (ω), and R (ω), respectively, are directly related to the ε 1 (ω) and ε 2 (ω) [113][114][115][116].
The calculated ε (ω) and ε (ω) are shown in Figure 14a,b. As shown in Figure 14a, the static dielectric constant ε (0) is given by the low energy limit of ε (ω). The peaks of ε (ω) shifted to higher energy as x increased from 0.00 to 1.00. The results obtained using mBJ-GGA for ε (0) at various Cl concentrations (x) are presented in Table 3 and shown in Figure 17. ε (0) decreased with an increase in the concentration of Cl, consistent with an increase in Eg. The results obey the following equation: For CsPbBr3, ε (0) was 3.82, which agrees well with the result obtained in the previous studies [23,72,105]. Figure 14b shows the behavior of ε2 (ω) for all Cl  The refractive index n (ω) and extinction coefficients k (ω) were calculated using the mBJ-GGA potential, as shown in Figure 15a,b. The spectrum of n (ω) closely resembles the spectrum of ε (ω) [117]. For CsPbBr3, the calculated n (0) value was 1.96, which agrees well with the previous theoretical and experimental values [56,72]. For CsPbCl3, n(0) was 1.798, which agrees well with the previous value [72,81]. The calculated n (0) versus the Cl concentration (x) is expressed as follows: Figure 15b shows that k(ω) depends on the concentration of Cl similar to that of ε2 (ω). The peak value of k (ω) shifted to lower energies as Cl concentration increased from 0.00 to 1.00.  For CsPbBr 3 , ε 1 (0) was 3.82, which agrees well with the result obtained in the previous studies [23,72,105]. Figure 14b shows the behavior of ε 2 (ω) for all Cl  The refractive index n (ω) and extinction coefficients k (ω) were calculated using the mBJ-GGA potential, as shown in Figure 15a,b. The spectrum of n (ω) closely resembles the spectrum of ε 1 (ω) [117]. For CsPbBr 3 , the calculated n (0) value was 1.96, which agrees well with the previous theoretical and experimental values [56,72]. For CsPbCl 3 , n(0) was 1.798, which agrees well with the previous value [72,81]. The calculated n (0) versus the Cl concentration (x) is expressed as follows: Materials 2020, 13, x FOR PEER REVIEW 14 of 22 The initial reflectivity R(ω) values were around 10.50% and 8.11% at zero frequency, which then increased to 18.62% (at 3.53 eV) and 15.24% (at 4.30 eV) for CsPbBr3(x = 0.00) and CsPbCl3 (x = 1.00), respectively, as shown in Figure 16. The maximum reflectivity peaks of 48%, 46 Figure 17 and presented in Table 3. The calculated R (0) versus Cl concentration (x) was fitted as follows:   Figure 15b shows that k(ω) depends on the concentration of Cl similar to that of ε 2 (ω). The peak value of k (ω) shifted to lower energies as Cl concentration increased from 0.00 to 1.00.
The initial reflectivity R(ω) values were around 10.50% and 8.11% at zero frequency, which then increased to 18.62% (at 3.53 eV) and 15.24% (at 4.30 eV) for CsPbBr3(x = 0.00) and CsPbCl3 (x = 1.00), respectively, as shown in Figure 16. The maximum reflectivity peaks of 48%, 46 16.10, 16.16, 16.18, and 16.29 eV, respectively, and then began to fluctuate and decrease at higher energies. The value of R (0) decreased with the increase in Cl concentration (x), as shown in Figure 17 and presented in Table 3. The calculated R (0) versus Cl concentration (x) was fitted as follows: R( )% = 10.3264 − 1.55348 − 0.54961 (20) . Figure 16. Calculated reflectivity spectra R (ω) of CsPb (Br1−xClx)3 using the mBJ-GGA potential. Figure 18a shows the absorption coefficient α (ω). With the increase in Cl concentration (x), the absorption edge shifted to higher energy. The wide absorption range from visible to ultraviolet indicates that these compounds are useful for various optical and optoelectronic applications [72]. Figure 18b shows similar features of the optical conductivity σ (ω) characteristics, and provides information on the effects of external parameters on the electronic structure [118].    Figure 18a shows the absorption coefficient α (ω). With the increase in Cl concentration (x), the absorption edge shifted to higher energy. The wide absorption range from visible to ultraviolet indicates that these compounds are useful for various optical and optoelectronic applications [72]. Figure 18b shows similar features of the optical conductivity σ (ω) characteristics, and provides information on the effects of external parameters on the electronic structure [118].

Conclusions
In this study, we investigated the influence of halide composition on the structural, electronic, and optical properties of the mixed-halide perovskites CsPb(Br 1−x Cl x ) 3 using DFT. When the Cl content x was increased from 0.00 to 1.00, a decrease in unit-cell volume was observed. Theoretical XRD analyses revealed that the peak shifts to larger angles when the concentration of Cl increases. An increase in E g was observed with an increase in the concentration of Cl. The E g values calculated using the PBE-GGA potential were between 1.53 and 1.93 eV, while those calculated using the mBJ-GGA potential were between 2.23 and 2.90 eV. The increase in E g with the increase in Cl content was due to the fact that the hybridization of Cl 3p states with Pb-s states was stronger than that with Br 4p states, which leads to a downshift of VBM and a decrease in the lattice constant. The calculated E g and exciton binding energy E b using mBJ-GGA potential best matched the previously reported experimental and theoretical values. The effective masses of electron and hole (m e * and m h *) are correlated with the energies of E g . The calculated photoabsorption coefficients display a blue shift of the absorption at a higher Cl concentration.