A. Structural properties
For all calculations, we'll focus on a comprehensive examination of the structural properties. Specifically, we'll delve into the cubic-phase perovskite binary, which belongs to space group 225. Employing a meticulous approach, we aim to compute diverse volume energies. By employing the Murnaghan equation, we'll generate an Energy-Volume (E-V) diagram. This diagram will encapsulate crucial structural parameters, including the equilibrium volume, crystal lattice characteristics, Bulk modulus, and its derivative. These findings will be visually represented in Fig-2, offering a clear depiction of our analyses.
In the cubic A2BB'X6 double perovskite structure, the bivalent metal cations B+2 and B'+2are each surrounded by 6 halogens (X) to form a BX6 octahedron. These octahedra share each halogen with two adjacent metal cations, B and B', where in the perfectly cubic system, the BX and B'X bonds align to create a BXB' angle of 180 degrees. Regarding the atomic arrangement within the cube, the A cations are situated at the cube's center, while the B' cations occupy the vertices. Meanwhile, the B anions are positioned at the midpoint of the cube's edges. This specific crystalline lattice belongs to the space group Fm-3m (number 225). The first Brillouin zone exhibits a cubic shape, illustrated in Fig 1-b. The high-symmetry points Γ and L, are respectively located in reciprocal coordinates at (0,0,0) and (1/2,1/2,1/2). The cubic unit cell comprises one molecule, and the atoms' Wyckoff positions within this cell are as follows: Cs at 8c (0.25, 0.25, 0.25), Cd at 4b (0.5, 0.5, 0.5), Pb at 4a (0, 0, 0), and I at 24e (0.23902830, 0, 0). Visual representations of the crystal structures for these compounds are depicted in Fig-1.a, b and Table 1.
Table 1: Structural properties of Cs2CdPbI6 with GGA-PBE.
Approximations
|
Atom
|
GAP
(ev)
|
RMT
|
x
|
Y
|
z
|
Mesh parameter (Å)
|
Space group Fm-3m
|
N° e-
|
GGA-PBE
|
Cs
Cd
I
Pb
|
1,23
|
2,5
2,5
2,5
2,5
|
0,25
0
0.23902830
0,5
|
0.25
0
0
0
|
0,25
0
0
0
|
12,4456
|
225
|
172
|
The ground state properties of Cs2CdPI6 are obtained by employing a fully relativistic calculation based on FP-LAPW: PBE_GGA and TB-mbj+SOC. The “all-electrons” total potential approximation is currently one of the best approaches for treating a strongly correlated system. We use the WIEN2k code for calculating all parameters and properties [10].
The common procedure used to determine structural properties near equilibrium is to evaluate the total energy of the system for different values of the lattice volume. The results obtained are then fitted to an equation of state.
In the present work, we used the Brich Murnaghan equation [15] which is given by the following expression:
The derivative of the compression modulus B’ is determined from the equation [16]:
The following Fig-2 represents the variation of energy as a function of volume with GGA-PBE of the double perovskite Cs2CdPbI6.
Fig-2 illustrates the energy values, plotted against volume, exhibit a convergence across all approximations. The results obtained are shown in Table 2. A high compressibility modulus B for Cs2CdPbI6 reveals that it is more rigid and less compressible. In general, a greater compressibility modulus indicates that the material is less compressible, and vice versa, with a smaller lattice constant. A material's ability to withstand compression is indicated by its compressibility modulus, and its derivative gives information on the amount of pressure or stress the material can withstand. The calculated structural parameters align well with each other, demonstrating the precision of the calculations conducted. Notably, as demonstrated by earlier research, our results strongly align with those of other investigations on double perovskites [17, 18].
Table 2 shows calculated lattice parameters (Å), bulk modulus (B), derivative B′, minimum total energy (Etot), and GAP (eV) using PBE-GGA.
Compound
|
a(Å)
|
V(a.u3)
|
B(GPa)
|
Bp
|
Etot(Ry)
|
GAP (eV)
|
Cs2CdPbI6
|
12.4456
|
3250.7608
|
17.2192
|
3.9552
|
-169639.247478
|
1.23
|
B. Electronic properties
The difference between the states at the valence band maximum (VBM) and conduction band minimum (CBM) determines the electronic band gap. Thus, by using the TB-mbj+SOC approximations, it has been determined that this compound is a semiconductor with an indirect gap of 1.9 eV at the L-X point in the Brillouin zone, based on the displayed band structure curves in Fig. 3.a and the coordinates of the sites stated.
The PBE-GGA calculations estimate the band gap less than the experimental data because in DFT calculations, the wave functions in the ground state are used, while as we know in reality, the excited states with higher energies are also effective in the band gap magnitude [19]. Although TB-mbj yields better outcomes than the experimental ones, as shown in several research, such as [20] Consequently, mbj+SOC is the most similar.
The Total Density of States (DOS) was calculated for the investigated compounds using the TB-mBJ potentials to examine the contributions of different elements to the valence and conduction bands in the double perovskite Cs2CdPbI6. Fig-3.b shows the total DOS for Cs2CdPbI6 and Cs, Cd, Pb, and I atoms, calculated using the TB-mBJ potentials.
The total DOS plots display zero deviation at the Fermi level with both potentials applied, confirming the semiconducting behavior deduced from the electronic band structure plot. Indium and a very small amount of cadmium are the major contributors at the top of the valence band, while the conduction band is primarily composed of Cs, I, and very little Cd orbitals.
The obtained results will be used in subsequent calculations to determine the effective masses of electrons and holes, as well as the effective conduction and valence band densities. Additionally, these results will aid in calculating the shallow uniform acceptor density.
C. Optical properties
The optical characteristics and other parameters were computed using the GGA-mbj approximation. The major optical characteristics analyzed are displayed in Fig.4-a, b, c, d, and e, together with the absorption coefficient α(ω), refractive index n(ω), optical loss factor L(ω), reflectivity R(ω), and the epsilon dielectric functions ε(ω) = ε1(ω) + iε2(ω).After the dielectric function was calculated, which is represented as ε(ω) = ε1(ω) + iε2(ω), the real ε1(ω) and imaginary components iε2(ω) of the frequency-dependent dielectric function are shown in Fig.2-a.The real component, ε1(ω), characterizes the material's polarization in response to light-matter interaction Fig.4-a. Notably, it exhibits a peak at 2.7 eV (459.204 nm) and subsequently diminishes for other energy intervals. The imaginary part of the dielectric function, iε2(ω), provides an estimation of the light absorbed by the perovskite material. We notice four clearly visible peaks recorded at 3.05eV, 7eV and 8.8eV which is equivalent to values of (406.505nm), (177.120nm), (140.89nm) of the longest waves. This indicates, or these peaks indicate, electronic transitions from the valence band to the conduction band [21]. This information offers valuable insights into the material's optical response and absorption characteristics across different energy levels in the visible spectrum.
The absorption coefficient α(ω) and the degree of light penetration into the perovskite material are depicted in Fig.4-b. The visible region's value falls between 300 nm (1.1 × 107 cm-1) and 900 nm (1 × 104 cm-1), the largest value is in the visible field at 450 nm(3,0eV), and it reaches an absorption value is about 1.3×107, as for the ultraviolet field only(9.0ev), the absorption value exceeded the threshold of 5.2×107 cm-1.
Optical loss factor L(ω) as can be seen in Fig.4-c, the value of the lost energy for the structure that we are studying (Cs2CdPbI6) is weak, especially in the visible field, which does not exceed 0.1eV. This shows the effective value of our material in the field of solar cells. The value of energy lost increases substantially in the UV field, reaching 0.78 eV at 158 nm [22]. The refractive index of light, n(ω), as it interacts with the perovskite material is displayed in Fig.4-d. Its value in the visible ranges from 0.6 at 300 nm to 0.01 at 900 nm, with a resonance peak at 387 nm and a maximum value of 0.65. In the UV field, it fluctuates between decreasing and increasing, reaching its greatest value at 133 nm.
The reflectivity R(ω) in Fig.4-e indicates the quantity of light reflected by the perovskite material. Its value in the visible area ranges from 0.01 (300 nm) to 0.09 (900 nm), there are one maximum values at 427nm, estimated at 0,202. As for the ultraviolet field, the same thing exists, there is a fluctuation of decrease and increase, and as the wavelength decreases, the reflection increases significantly.
These calculated values are consistent with various calculations previously performed on perovskite materials mentioned in [23,24], and after analyzing the results of the optical properties, the studied perovskite material (Cs2CdPbI6) it is somewhat suitable in solar cells and we will see that in the next study.
D. Elastic properties
A material's elastic characteristics are crucial in deciding how it will behave under stress and if it can regain its original size and shape after being distorted by an outside force. Understanding a material's elastic characteristics is crucial for understanding how it will behave and remain stable in a variety of natural environments. Therefore, we extracted the main constants that are known in various previous research and studies [25-27]. Table 5-a and b displays the elastic constants (ECs) that we compute using the IRelast package interfaced within Wien2k. There are four different wave velocities: transverse = 1235.81 (m/s), longitudinal = 2345.48 (m/s), average = 1381.76 (m/s), and debye temperature = 110.161 (K).
It is known that in the elastic properties, there are conditions that determine the stability of the cubic phase of materials:
C11-C12 > 0, C11 > 0, C44 > 0, and C11 + 2 C12 > zero, and also B > 0 By [28] calculating these conditions, the stability of our structure in the studied phase is revealed suggesting that these compounds are elastically stable [29-32], as we mentioned, the results are shown in Table 5(a,b).
Table 5(a) Elastic constants of cubic Cs2CdPbI6.
c11
|
c12
|
c44
|
|
28.743 (GPa)
|
7.949 (GPa)
|
4.778 (GPa)
|
|
Table 5(b): The elastic constants for Cs2CdPbI6 were calculated using additional elastic parameters such as bulk modulus, anisotropy factor, Young modulus, poison ratio, Pugh ratio (B/G), and Cauchy's pressure.
Elastic Parameters
|
Value
|
B (in GPa)
|
14.88
|
A
|
0.46
|
G (in GPa)
|
7.03
|
E (in GPa)
|
2.02
|
ʋ
|
0.29
|
Gv(in Gpa)
|
1.29
|
B/G
|
2.12
|
B/C44
|
3.11
|
C11–C12 (in GPa)
|
20.79
|
C11–C44 (in GPa)
|
23.96
|
G′
|
10.38
|
GR
|
6.10
|
E. Solar cell simulation
At this point, we will examine the outcomes of the investigated material, perovskites, in solar cells utilizing the structure illustrated in Fig.5. It is important to consider variations in the energy levels of the conduction and valence bands within heterogeneous connections. The details entered into the program are summarized in Table 6, drawing from information obtained from prior experiments and articles. In the upcoming section, we will elucidate the process of acquiring parameters for perovskites (Cs2CdPbI6).
Table 6: Physical parameters used in our simulations scaps-1d.
|
HTL-CBTS
|
Cs2CdPbI6
|
ETL-TiO2
|
FTO
|
Layer thickness( μm)
|
0.05
|
Varied
|
0.1
|
0.3
|
Dielectric constant dk
|
5.4
|
4.1
|
10.00
|
3.50
|
Band gap Eg (eV)
|
1.9
|
1.9
|
3.260
|
4.00
|
Electron affinity chi (eV)
|
3.6
|
3.9
|
4.200
|
9.00
|
Effective conduction band density (cm−3)
|
2.2E+ 1018
|
1,05E+20
|
1E+21
|
2.200E+18
|
Effective valence band density (cm−3)
|
1.8E+1019
|
1,7E+19
|
2E+20
|
1.80E+19
|
Electron mobility (cm2 V−1 s−1)
|
30
|
555.1
|
20
|
2.00E+1
|
Hole mobility (cm2 V−1 s-1)
|
10
|
89.89
|
10
|
1.00E+1
|
Shallow uniform donor density Nd (1/cm3)
|
-
|
0
|
5E+19
|
1.E+21
|
Shallow uniform acceptor density Na (1/cm3)
|
1 E+18
|
1.4E+15
|
-
|
-
|
Defect density cm-3
|
1E+15
|
Varied
|
1E+15
|
1E+15
|
References
|
[33,34]
|
/
|
[35]
|
[36]
|
E. 1. Optimising the various layers' thicknesses
Determining the optimum thickness for ETL and both the perovskite layer Cs2CdPbI6 and layer HTL is our objective at the beginning, so determining the optimal thickness for each layer gives them the greatest benefit by absorbing light to the maximum extent and transferring charges efficiently. within a range spanning between 0.1 and 1 μm, while we took the thickness of the FTO layers as 0.3μm.
As depicted in Fig-6.a and 6.b, the impact of varying the thickness of both the Hole Transport Layer (HTL) and Electron Transport Layer (ETL) was not distinctly evident. Nevertheless, the thickness of the HTL layer had a slight effect, as we recorded a four-degree increase in efficiency and current, while the voltage change was not clear. The fill factor decreased significantly, indicating that the thickness of the HTL hinders the recombination of the electron-hole pair. Thus, for the ETL and HTL layers, the ideal thickness is found to be 0.1 µm and 0.5 µm, respectively. As a result, we will proceed to examine the impact of the double perovskite thickness in the device by setting the thickness of the ETL and HTL layers at 0.1 µm and 0.5 µm, respectively.
The effects of perovskite layer thickness on device performance are shown in Figs.6-c, 6-d, and 6-e. Important characteristics are much improved when the thickness is increased from 0 µm to 1 µm, as Fig.6-c illustrates: efficiency rises from 18.1% to 32%, the fill factor increases from 52% to 81.6%, the current density reaches 28mA/cm², and the voltage is 1.4V. The J-V curve in Fig-6.d supports these results, aligning with the absorption data shown in Fig-6.e.
These improvements are attributed to the perovskite layer’s ability to effectively absorb and trap light, especially within the 380 nm to 500 nm wavelength range, beyond which the absorption rate decreases. While these findings align somewhat with the results from Fig-4.b except that here we have an absorption rate for four layers FTO/ETL/Cs2CdPbI6/HTL.
E. 2. Effect of Cs2CdPbI6 Defect States
After optimizing the thickness of the layers, we simulate the variation in defect density of the double perovskite Cs2CdPbI6 layer, as well as a defect in the density between the interface HTL/Cs2CdPbI6 we change the density defect as 108/cm3 to 1018/cm3. The PSC performance of Cs2CdPbI6 and HTL/Perovskite with variations in defect density is displayed in Fig.7-a and b, for the defect density of double perovskite, we recorded a deterioration of the photoelectric parameters after the defect density reached 1014/cm3. As for the defect density between the surfaces, the voltage and current were not affected, but the efficiency decreased, especially after a defect density of 1012/cm2. However, the fill factor increased after this value, but slightly.
E. 3. Impact of series and shunt resistances in PSC
The impact of series resistance is illustrated in Fig-8.a. The data indicates that as series resistance Rs increases, the performance of perovskite solar cells (PSC) is adversely affected. With an elevated Rs, the open-circuit voltage (Voc) of the device experiences a slight increase from 1.2503 V to 1.2506V. But the short-circuit current (Jsc) doesn't change at 27.68 mA/cm2, whereas power conversion efficiency (PCE) and fill factor (FF) drop from 70.97% to 61.79% and 24.61% to 21.40%, respectively. Notably, highly conductive fluorine-doped tin oxide (FTO) has limited contribution to Rs. Consequently, the resistance of the materials is the main factor that determines Rs. Rs greatly reduces the device's fill factor and, in some situations, also affects the open-circuit voltage (Voc) at the interface between semiconductors and metal. This increases power loss and lowers power conversion efficiency overall [33].
Fig.8-b illustrates the effect of the Resistance shunt on the device's performance specifications from 103 to 6×103 Ω.cm2, yet the RS stayed at 0.0 Ω.cm2, unchanged. We found increments in Voc, FF, and PCE values from 1.2248 V to 1.2450V, FF 25% to 85.61%, and PCE 1.11% to 18.84%, respectively, the current was not affected by this change and remained in value 27.7415 mA/cm2, Manufacturing defects mainly contribute to resistance shunt as can be seen in the curves the resistance did not effectively affect the device. Higher resistance shunts allow for higher current flow via the p/n junction by lowering its resistance [34, 35].