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Article

Mono- and Co-Doped Mn-Doped CsPbCl3 Perovskites with Enhanced Doping Efficiency and Photoluminescent Performance

by
Hao Jiang
1,
Yiting Zhao
1,
Fangchao Liu
1,
Yongqi Yan
1,
Yinuo Ma
1,
Hexin Bao
1,
Zhongchen Wu
1,2,
Wei-Yan Cong
1 and
Ying-Bo Lu
1,*
1
School of Space Science and Physics, Shandong University, Weihai 264209, China
2
Shandong Key Laboratory of Optical Astronomy and Solar-Terrestrial Environment, Institute of Space Sciences, Shandong University, Weihai 264209, China
*
Author to whom correspondence should be addressed.
Materials 2023, 16(16), 5545; https://doi.org/10.3390/ma16165545
Submission received: 29 June 2023 / Revised: 7 August 2023 / Accepted: 7 August 2023 / Published: 9 August 2023
(This article belongs to the Section Materials Physics)
Browse Figures
Versions Notes

Abstract

:
To investigate the effect of Mn and other metal dopants on the photoelectronic performance of CsPbCl3 perovskites, we conducted a series of theoretical analyses. Our findings showed that after Mn mono-doping, the CsPbCl3 lattice contracted and the bonding strength increased, resulting in a more compact structure of the metal octahedral cage. The relaxation of the metal octahedral cage, along with the Jahn–Teller effect, results in a decrease in lattice strain between the octahedra and a reduction in the energy of the entire lattice due to the deformation of the metal octahedron. These three factors work together to reduce intrinsic defects and enhance the stability and electronic properties of CsPbCl3 perovskites. The solubility of the Mn dopant is significantly increased when co-doped with Ni, Fe, and Co dopants, as it compensates for the lattice strain induced by Mn. Doping CsPbCl3 perovskites reduces the band gap due to the decreased contributions of 3d orbitals from the dopants. Our analyses have revealed that strengthening the CsPbCl3 lattice and reducing intrinsic defects can result in improved stability and PL properties. Moreover, increasing Mn solubility and decreasing the bandgap can enhance the PLQY of orange luminescence in CsPbCl3 perovskites. These findings offer valuable insights for the development of effective strategies to enhance the photoelectronic properties of these materials.

1. Introduction

In 2009, Kojima et al. were the first to successfully apply MAPbI3 (MA = CH3NH3) perovskites in the field of solar cells [1]. Since then, the power conversion efficiency (PCE) of perovskite solar cells has impressively increased within only ten years [2,3,4,5,6,7]. Due to their excellent optoelectronic performance, halide perovskites have garnered extensive attention in various optoelectronic fields, such as those examining light emitting diodes (LED) devices and detectors [8,9]. However, the photoluminescence (PL) performance and stability of perovskite materials deteriorate in environments with trace amounts of water and oxygen [10].
Various methods have been employed to enhance the performance of halide perovskites, such as altering the growth technology and modulating the device structure [6,11,12,13,14,15,16]. Doping metal impurities has been confirmed as an effective strategy to modify the physical properties of materials [17,18,19,20,21,22,23,24,25,26,27]. Moreover, doping techniques involving ions like Cu2+ and Zn2+ have been extensively studied [26,27]. Additionally, there have been significant advancements in the calculation analysis and explanation of these techniques, leading to a more detailed and comprehensive understanding. For instance, Saidaminov et al. added Cd ions to the lattice of FAPbI3 (FA = (HC(NH2)2+)) and found that this significantly reduces the intrinsic vacancies, thereby improving the stability of these mixed perovskites [28]. Similarly, Bi et al. increased the photoluminescence quantum yield (PLQY) of CsPb(Br/Cl)3 from 23% to more than 80% via Cu-doping, which is the highest recorded PLQY in mixed halide perovskites at that time [29].
Since the introduction of Mn ions into halide perovskites by Liu et al. in 2016, there has been promising progress in the application of Mn-doped perovskites in LED technology [30]. In 2018, Parobek et al. conducted a study where they prepared Mn-doped CsPbBr3 perovskites through direct thermal injection. The study found that the photoluminescence quantum yield (PLQY) of CsPbBr3 was significantly improved as a result of the Mn doping [31]. Zhou et al. discovered that the addition of Mn to CsPbCl3 and CsPb(Cl/Br3) perovskites resulted in red light emissions that could be fine-tuned by adjusting the concentration of Mn doping, thereby expanding the colour range [32]. In addition, Wu and colleagues found that Mn doping significantly improved the photoluminescence properties of Cs2AgInCl6, making it a promising material for LED applications [33].
Mn dopants have a significant impact on the luminescence of halide perovskites. However, the photoluminescence quantum yield (PLQY) of Mn-doped CsPbCl3 (Mn@CsPbCl3) is limited by a self-purification effect [34,35,36,37,38]. Xing et al. discovered that introducing Ni dopants into Mn-doped CsPbCl3 perovskites results in an increase in the solubility of the Mn dopant from 0.11% to 15.25%. This increase ultimately improves the PLQY of the Mn-generated luminescence in CsPbCl3, which is an astonishing phenomenon [39,40].
The addition of Fe and Co impurities to CsPbCl3 perovskites promotes the solubility of Mn dopants and improves the PL performance [40]. It is unclear why the second dopant has such a significant influence on the first dopant, or why Ni, Fe, and Co dopants perform similarly. Reports suggest that Ni-doping affects the band structure [40], but some PL and absorption spectra show no effect on the bandgap [41]. The internal mechanism behind Mn and Ni co-doping, as well as the other influences induced by Fe and Co dopants, remains unclear. A systematic theoretical study was conducted on the geometric and electronic structures of Mn@CsPbCl3 co-doped with Ni, Fe, and Co. The study analysed the variations of bonding interactions and crystalline structures, which are key factors that determine the band structure and physical properties of CsPbCl3 perovskites co-doped with Mn and other metal dopants. The results provide a detailed interpretation of the aforementioned factors.

2. Calculation Methods

This paragraph describes the methodology used for density functional theory (DFT) calculations in the Vienna ab initio simulation package (VASP) [41,42]. The Perdew–Burke–Ernzerhof (PBE) method with a generalized gradient approximation (GGA) function is employed to handle exchange and correlation effects between electrons [43]. Meanwhile, we use the Heyd–Scuseria–Ernzerhof hybridized function (HSE06) with the shielding parameter 0.25 to achieve more accurate electronic properties [44]. The electron wave functions are obtained using the PAW method [45] with a cut-off energy of 400 eV. The Brillouin zone [46] is integrated using a 4 × 4 × 4 Monk-horst Pack K point. The convergence criteria for the self-consistent iterative process are set to ≤10−4 eV/atoms for total energy and 0.01 eV/Å for force. The bond interactions are analysed using LOBSTER code, which considers: (1) 3p for Cl; (2) 6p for Pb; (3) 3d for Mn; (4) 3d for Ni; (5) 3d for Fe; (6) 3d for Co [47].

3. Results and Discussions

3.1. Geometric Properties

Figure 1 shows a supercell of CsPbCl3 perovskites in cubic phase with a space group of FM-3M and lattice constants of 11.47 Å. Intrinsic defects such as vacancies are commonly found in the lattice of pristine perovskites. These vacancies have a significant impact on the structural stability and optoelectronic properties of the material. Vacancies create carrier traps that impede the transport of electrons, resulting in a reduction of PLQY. In this study, we analyse the distributions of intrinsic vacancies in CsPbCl3 perovskites based on previous research. We focus solely on charge neutral defects and calculate the formation energy using the following formula:
  E f =   E d f − E i n i + ∑ i n i μ i − ∑ j n j μ j
Edf and Eini represent the total energies of the supercells with and without defects, respectively. The number of atoms removed and added during the defect formation process are expressed as ni and nj, respectively. μi and μj are the chemical potentials of elements. The chemical potentials of metal cations and chlorine atoms were calculated from bulk metal materials and gaseous chlorine, respectively. Table 1 lists the calculated formation energies of intrinsic defects, from which we can conclude that the value of Cl vacancy (VCl) is the smallest. This suggests that VCl is the most preferred intrinsic defect in CsPbCl3.
When CsPbCl3 perovskites are doped with external impurities like Mn, Ni, Fe, and Co (represented by X), it becomes difficult for X to replace Cl due to the significant difference in electronegativity between X dopants and Cl anions. Additionally, replacing univalent Cs with bivalent X ions introduces a charge imbalance into the crystal. Therefore, defects of X replacing Pb (XPb) are more likely to appear, as shown in Figure 2. For example, as shown in Table 2, when Mn dopant is introduced into the CsPbCl3 lattice to form a MnPb defect, the lattice contracts due to the smaller radius (81 pm) of Mn2+ ions compared to that (133 pm) of Pb2+ ions, which is consistent with experimental results. We conducted a detailed analysis of the bond length shrinkage after doping by calculating the data presented in Figure 3 and Table 3. Similar phenomena also occur in CsPbCl3 supercells doped with several dopants from the same family as Mn.
The replacement of Pb atoms with X dopants results in a contraction of bond lengths, as shown in Table 2, due to the smaller radii of X compared to Pb. The lattice parameters decrease from 11.47 Å to ~11.28 Å after X-doping. This contraction leads to an increase in bonding strength, making the metal octahedral cage more compact. The denser lattice structure makes it more difficult for atoms to be lost. Additionally, the Jahn–Teller effect suggests that the deformation of the metal octahedron reduces the energy of the entire lattice system. The contraction of the metal octahedral cage reduces lattice strain and stress between atoms, which in turn reduces intrinsic defect and improves the overall stability and electronic properties of CsPbCl3 perovskites. Additionally, the Jahn–Teller effect suggests that deformation of the metal octahedron can reduce the energy of the entire lattice system. Overall, these three factors contribute to a decreased likelihood of atom loss in the perovskite’s structure.
To gain a deeper understanding of this intriguing phenomenon caused by the dopant in CsPbCl3 perovskites, we assess the stability of a perovskite using the tolerance factor t, as described in the Equation (2).
t = R A + R X √ 2 ( R B + R X )
RA, RB, and RX represent the radii of composition ions in ABX3 perovskites. The radii used in this study are presented in Table 2. According to theoretical analysis, perovskites can maintain stability when the value of t falls within the range of 0.77–1.10. When t approaches one, the stability of the perovskite structure is further enhanced. By referring to Table 2 and utilizing Formula (2), the tolerance factor of CsPbCl3 is determined to be 0.87. However, when calculating t using the radius of the Mn2+ ion instead of the original Pb2+ ion, t is found to be 1.05. Similarly, the calculated t values for Ni, Fe, and Co doping are 1.07, 1.08, and 1.06, respectively. These values indicate that they are closer to one compared to the case of undoping, suggesting that the frameworks in the CsPbCl3 lattice, which consist of metal-halogen octahedra, are strengthened. Therefore, it can be inferred from this perspective that the overall structural stability of the perovskite crystal is enhanced after doping.
To analyse the variation of bond strength, a Crystal Orbital Hamiltonian Population (COHP) simulation can be used. Figure 4 provides the results of the calculation of integral projection COHP (IpCOHP), which shows that the Mn-Cl bond is stronger than the original Pb-Cl bond, resulting in a slight decrease in bond length. This explains why the CsPbCl3 perovskite lattice shrinks and the energy required for defect formation increases. Further analysis is conducted on the variation of orbital bonding induced by different dopant atoms including Fe, Co, and Ni. Table 3 and Figure S1 display the results of the IpCOHP calculation. It can be observed that the metal-chlorine bonds in the three different doping configurations are enhanced to varying degrees. Specifically, the IpCOHPs of the Ni-Cl bond, Co-Cl bond, Fe-Cl bond, and Mn-Cl bond are larger than those of Pb-Cl bond. The bonding strength follows the order of Ni-Cl bond < Co-Cl bond < Fe-Cl bond < Mn-Cl bond. This order is consistent with the defect formation energies and bond lengths, which further confirms our theoretical explanation for the metal octahedral contraction. Additionally, it was found that the peak bonding energies of Mn-Cl, Ni-Cl, Fe-Cl, and Co-Cl are significantly lower than that of Pb-Cl bond. This reduction in energy makes the perovskite systems more stable and strengthens the crystal structures.
To investigate the impact of X dopants on the pristine CsPbCl3 systems with intrinsic defects, we constructed supercells containing XPb external defects and the most common intrinsic VCl defect. The relative position between the two defects is crucial and requires careful investigation. We considered three configurations: nearest neighbouring, next nearest neighbouring, and farthest positions from the XPb defects. Figure 1a shows the positions of VCl defects in these configurations, which are indicated by dashed circles labelled as VCl-1, VCl-2, and VCl-3, and Table 2 presents the three different defects as VCl1, VCl2, and VCl3 respectively. The results of the formation energy calculations indicate that the configuration containing the nearest neighbouring XPbVCl-1 complex has the lowest formation energy, regardless of the dopant used (X = Mn, Ni, Fe, Co). This suggests that XPbVCl-1 is the most energetically favourable. Table 2 reveals that the X2+ ions have smaller radii than Pb2+ ions, resulting in shorter X-Cl bond lengths compared to the original Pb-X bond. For example, in the case of Mn-doping, the Mn-Cl bond is reduced to a length of 2.48 Å, causing high stress in the CsPbCl3 lattice. This stress leads to noticeable lattice distortion near the [MnCl6] octahedron, which is depicted in Figure 3. The elongation of the Pb-Cl bond length from 2.86 Å to 3.16 Å is caused by the neighbouring [PbCl6] octahedron sharing a joint chloride ion, which causes a strong stretch in the [MnCl6] octahedron. However, this stress can be effectively released by the nearest VCl vacancy.
Previous studies have shown that it is challenging to dope Mn to a high concentration due to its self-purification mechanism [35,38,48]. However, some reports suggest that co-doping Mn with other impurities can overcome this limitation and enhance the physical properties induced by the Mn dopant, such as the PL performances [40]. In this study, we analyse the Mn-Ni co-doping system to examine these phenomena.
To study the influence of the distance between Mn and the extra metal dopant on crystal structures and defect formation energies, we constructed three configurations for each co-doping strategy, namely co#1, co#2, and co#3, where the distance between Mn and the other metal dopant varied from near to far. Figure 5 illustrates these distributions. For Ni mono-doped and co-doped with Mn, we evaluated the solubility of the Mn dopant in CsPbCl3 perovskites by using the defect formation energies of the MnPb defect.
Table 1 shows that when Mn is mono-doped into CsPbCl3 perovskites, the formation energy of the MnPb defect is 3.96 eV. However, when Mn is co-doped with Ni dopant, the formation energy of the MnPb defect decreases significantly, indicating an improvement in the solubility of the Mn dopant in CsPbCl3 perovskites. The configuration with the Mn dopant occupying the nearest neighbouring lattice site to the extra Ni dopant consistently results in the lowest formation energy. In other words, Mn and Ni dopants tend to co-appear in pairs. Incorporating mono-doping metal dopants into CsPbCl3 perovskites can lead to lattice distortions. However, the distortions can be corrected by the nearest neighbouring metal dopants, as seen in nonlinear molecules with spatially degenerate electronic ground states. This correction reduces the energy by eliminating degeneracy and helps to relax the stress throughout the entire lattice, as illustrated in Figure 5.

3.2. Electronic Properties

To investigate the luminescence properties of CsPbCl3 perovskites, we examined the impact of external dopants on the band structures and density of states. Our analysis compared the band gap of undoped cubic CsPbCl3, which exhibited a direct band structure with a gap of 2.22 eV, to the band gap after Mn, Ni, Fe, and Co doping, as illustrated in Figure 6. Figure 7 illustrates our findings. Our analysis of the PDOS revealed that the Cl-3p orbital dominates the valence band maximum (VBM) of CsPbCl3, while the Pb-6p orbital controls the conduction band minimum (CBM). The band structures of CsPbCl3 perovskites with Mn, Ni, Fe, and Co doping are depicted in Figure 8 and Figure S2 in the Supplementary Materials. To ensure the reliability of the data, the results calculated by the HSE method are provided in Figures S5 and S6 in the Supplementary Materials. Upon comparison, it is evident that the changing trend of the energy bandgap remains consistent before and after doping. The figures illustrate that the direct band gap of CsPbCl3 perovskites remains unchanged, but the band gaps shift to 1.68 eV, 1.82 eV, 1.38 eV, and 2.16 eV, respectively, due to the introduction of impurity levels. For instance, after Mn-doping, the Mn-3d orbital significantly hybridizes with the band edges. Specifically, the Mn-3d orbital strongly hybridizes with the Pb-6p orbital near CBM, leading to a decrease in the band gap. Similarly, in Ni, Fe, and Co mono-doping CsPbCl3 systems, the strong hybridizations of Ni-3d, Fe-3d, and Co-3d with Cl-3p near CBM cause a decrease in the band gaps. The reduction of the band gap in CsPbCl3 results in a red shift in its luminescence, which can be advantageous for the production of orange light emitting diodes.
In this study, the electronic properties of MnNi@CsPbCl3 were investigated by examining the band structures and density of states of Ni, Fe, and Co co-doping with Mn. The results showed that strong interactions between Mn and Ni resulted in manifest impurity bands, which occupied the nearest neighbouring [XCl6] octahedra in CsPbCl3 perovskites. The valence band maximum (VBM) was mainly contributed by the hybridization of Mn-3d orbital, Ni-3d orbital, and Cl-3p orbital, while the conduction band minimum (CBM) was dominated by the hybridization of Mn-3d orbital and Ni-3d orbital. This led to a decrease in the band gaps, causing a red shift in the luminescence of perovskites and an enhancement of the overall electrical conductivities. Figure S3 in the Supplementary Materials and Figure 7e, f provides visual representations of the findings.
The doping efficiency and luminescence efficiency of the Mn dopant in CsPbCl3 can be improved through co-doping with Ni, Fe, and Co. The difference in radii and electronegativities between Mn and host Pb atoms leads to a self-purification effect in CsPbCl3 perovskites, which minimizes the doping concentration of Mn. However, co-doping Mn with Ni, Fe, and Co, whose outermost electronic configurations are similar to that of Mn, can effectively relax the lattice stress and distortion induced by mono-doping Mn. This eliminates intrinsic defects and trap states inside the CsPbCl3 lattices. The defect states induced by Ni, Fe, and Co dopants are at a similar level to those of Mn dopant, which means they do not create additional traps for electrons. Therefore, the doping and emission efficiency of the Mn dopant are effectively enhanced, as illustrated in Figure 8.

4. Conclusions

This study utilizes first-principles calculations to analyse the geometric and electronic structures of CsPbCl3, both mono-doped with Mn and co-doped with Mn, Ni, Fe, and Co. The study thoroughly examines the formation energies, energy bands, DOS, and COHP of various defects in the pristine, mono-doping, and co-doping CsPbCl3 systems. The results show that Mn mono-doping CsPbCl3 perovskites exhibit a contraction of bond lengths and an increase in bonding strengths, resulting in a more compact metal octahedral cage structure. This contraction reduces the lattice strain and stress between atoms in the octahedron. The Jahn–Teller effect causes deformation of the metal octahedron, which in turn reduces the energy of the entire lattice system. This, combined with the reduction of intrinsic defects and improvement of electronic properties, leads to improved stability of CsPbCl3 perovskites. When Mn is co-doped with Ni, Fe, and Co dopants, the lattice strain induced by Mn is compensated for and the solubility of the Mn dopant is significantly increased. Doping Mn into CsPbCl3 perovskites, either alone or in combination with other dopants, leads to a noticeable decrease in band gap, primarily due to the contribution of 3d orbitals of the doped atoms. Therefore, it can be concluded that strengthening the CsPbCl3 lattice and reducing intrinsic defects are beneficial for improving stability and PL properties between atoms. The increase in Mn solubility and decrease in bandgap contribute to the improvement in the orange luminescence’s PLQY. These findings aid in the understanding of the metal dopant modulation effect in halide perovskites and offer effective strategies for enhancing their photoelectronic properties.

Supplementary Materials

The following supporting information can be downloaded at: https://www.mdpi.com/article/10.3390/ma16165545/s1, Figure S1. pCOHP diagrams of (a) Ni-Cl bond, (b) Fe-Cl bond and (c)Co-Cl bond in CsPbCl3 systems. Figure S2. (a) Band structure and (b) DOS diagram of Ni-doping CsPbCl3. (c) Band structure and (d) DOS of Fe-doping CsPbCl3. (e) Band structure and f) DOS of Co-doping CsPbCl3. Figure S3. (a) Band structure and (b) DOS diagram of Mn and Fe co-doping CsPbCl3. (c) Band structure and (d) DOS diagram of Mn and Co co-doping with CsPbCl3. Figure S4. The convergency test of the CsPbCl3 systems using different Monkhorst Pack K point meshes. Figure S5. (a) Band structure and (b) DOS of pristine CsPbCl3 perovskites. (c) Band structure and (d) DOS of Mn mono-doping CsPbCl3 perovskites calculated by the HSE method. Figure S6. (a) Band structure and (b) DOS diagram of Ni-doping CsPbCl3. (c) Band structure and (d) DOS of Fe-doping CsPbCl3. (e) Band structure and f) DOS of Co-doping CsPbCl3 calculated by the HSE method.

Author Contributions

Conceptualization, H.J. and Y.-B.L.; methodology, H.J., Y.Z. and F.L.; software, H.J., Y.Y., Y.M. and H.B.; data curation, H.J., Z.W. and W.-Y.C.; writing—original draft preparation, H.J. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Natural Science Foundation of Shandong Province (No. ZR2020MA067) and the National Natural Science Foundation of China through Grant 11504202. The computations for this study were conducted at the Supercomputing Center of Shandong University (Weihai).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Data is unavailable due to privacy.

Conflicts of Interest

The authors declare no competing financial interest.

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Materials 16 05545 g001
Figure 1. (a) Geometric structure of CsPbCl3. The constituent elements, the Mn-doping position, and the VCl positions are denoted accordingly. (b) Structure plotted with metal octahedron of CsPbCl3.
Figure 1. (a) Geometric structure of CsPbCl3. The constituent elements, the Mn-doping position, and the VCl positions are denoted accordingly. (b) Structure plotted with metal octahedron of CsPbCl3.
Materials 16 05545 g001
Materials 16 05545 g002
Figure 2. Geometric structures of (a) Mn, (b) Ni, (c) Fe, and (d) Co mono-doping CsPbCl3.
Figure 2. Geometric structures of (a) Mn, (b) Ni, (c) Fe, and (d) Co mono-doping CsPbCl3.
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Materials 16 05545 g003
Figure 3. (a) Metal octahedron [PbCl6] in CsPbCl3. (b) Contraction of metal octahedron [MnCl6] and lattice distortion of [PbCl6] in Mn@CsPbCl3.
Figure 3. (a) Metal octahedron [PbCl6] in CsPbCl3. (b) Contraction of metal octahedron [MnCl6] and lattice distortion of [PbCl6] in Mn@CsPbCl3.
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Materials 16 05545 g004
Figure 4. Integral projection COHP diagrams of (a) Mn-Cl bond and (b) Pb-Cl bond in CsPbCl3 systems.
Figure 4. Integral projection COHP diagrams of (a) Mn-Cl bond and (b) Pb-Cl bond in CsPbCl3 systems.
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Materials 16 05545 g005
Figure 5. Configurations of (a) co#1, (b) co#2, and (c) co#3 for Mn and Ni co-doping CsPbCl3 perovskites.
Figure 5. Configurations of (a) co#1, (b) co#2, and (c) co#3 for Mn and Ni co-doping CsPbCl3 perovskites.
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Materials 16 05545 g006
Figure 6. Geometric structures of (a) MnNi@CsPbCl3, (b) MnFe@CsPbCl3, and (c) MnCo@CsPbCl3.
Figure 6. Geometric structures of (a) MnNi@CsPbCl3, (b) MnFe@CsPbCl3, and (c) MnCo@CsPbCl3.
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Materials 16 05545 g007
Figure 7. (a) Band structure and (b) DOS of pristine CsPbCl3 perovskites. (c) Band structure and (d) DOS of Mn mono-doping CsPbCl3 perovskites. (e) Band structure and (f) DOS diagram of Mn and Ni co-doping CsPbCl3 perovskites.
Figure 7. (a) Band structure and (b) DOS of pristine CsPbCl3 perovskites. (c) Band structure and (d) DOS of Mn mono-doping CsPbCl3 perovskites. (e) Band structure and (f) DOS diagram of Mn and Ni co-doping CsPbCl3 perovskites.
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Materials 16 05545 g008
Figure 8. Schematic diagram of Mn-induced luminescence in CsPbCl3 perovskites improved by the Ni, Fe, Co co-doping.
Figure 8. Schematic diagram of Mn-induced luminescence in CsPbCl3 perovskites improved by the Ni, Fe, Co co-doping.
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Table 1. Formation energies of various defects in CsPbCl3 systems.
Table 1. Formation energies of various defects in CsPbCl3 systems.
Doping StrategiesDefect TypeEf (eV)Doping StrategiesDefect TypeEf (eV)
Intrinsic
Defects		VCl3.15Mono-DopingMnPb3.96
VCs3.96MnPbVCl16.83
VPb3.96MnPbVCl26.86
Mono-DopingNiPbVCl14.78MnPbVCl36.85
NiPbVCl25.16Co-DopingMnNi12.56
NiPbVCl35.07MnNi22.84
CoPbVCl15.63MnNi33.34
CoPbVCl25.93MnCo13.17
CoPbVCl35.85MnCo23.36
FePbVCl16.06MnCo33.58
FePbVCl26.28MnFe13.51
FePbVCl36.19MnFe23.53
MnFe33.69
Table 2. Crystal radii (CR) and the coordination numbers (CN) of ions in doped-CsPbCl3 systems.
Table 2. Crystal radii (CR) and the coordination numbers (CN) of ions in doped-CsPbCl3 systems.
IonCs+Cl−Pb2+Mn2+Fe2+Co2+Ni2+
CN12666666
CR(pm)20218213381757977
Table 3. The bond lengths (Å) and the corresponding integral projection COHP (eV per cell) in the pristine, mono-, and co-doping CsPbCl3 systems.
Table 3. The bond lengths (Å) and the corresponding integral projection COHP (eV per cell) in the pristine, mono-, and co-doping CsPbCl3 systems.
SystemsBondsBond Lengths-IpCOHP
CsPbCl3Pb-Cl2.861.78
Ni@CsPbCl3Ni-Cl2.523.52
Co@CsPbCl3Co-Cl2.463.93
Fe@CsPbCl3Fe-Cl2.454.07
Mn@CsPbCl3Mn-Cl2.484.08
MnNi1@CsPbCl3Mn-Cl2.304.32
Ni-Cl3.424.43
MnCo1@CsPbCl3Mn-Cl2.324.15
Co-Cl3.404.82
MnFe1@CsPbCl3Mn-Cl2.354.08
Fe-Cl3.443.89
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Jiang, H.; Zhao, Y.; Liu, F.; Yan, Y.; Ma, Y.; Bao, H.; Wu, Z.; Cong, W.-Y.; Lu, Y.-B. Mono- and Co-Doped Mn-Doped CsPbCl3 Perovskites with Enhanced Doping Efficiency and Photoluminescent Performance. Materials 2023, 16, 5545. https://doi.org/10.3390/ma16165545

AMA Style

Jiang H, Zhao Y, Liu F, Yan Y, Ma Y, Bao H, Wu Z, Cong W-Y, Lu Y-B. Mono- and Co-Doped Mn-Doped CsPbCl3 Perovskites with Enhanced Doping Efficiency and Photoluminescent Performance. Materials. 2023; 16(16):5545. https://doi.org/10.3390/ma16165545

Chicago/Turabian Style

Jiang, Hao, Yiting Zhao, Fangchao Liu, Yongqi Yan, Yinuo Ma, Hexin Bao, Zhongchen Wu, Wei-Yan Cong, and Ying-Bo Lu. 2023. "Mono- and Co-Doped Mn-Doped CsPbCl3 Perovskites with Enhanced Doping Efficiency and Photoluminescent Performance" Materials 16, no. 16: 5545. https://doi.org/10.3390/ma16165545

APA Style

Jiang, H., Zhao, Y., Liu, F., Yan, Y., Ma, Y., Bao, H., Wu, Z., Cong, W.-Y., & Lu, Y.-B. (2023). Mono- and Co-Doped Mn-Doped CsPbCl3 Perovskites with Enhanced Doping Efficiency and Photoluminescent Performance. Materials, 16(16), 5545. https://doi.org/10.3390/ma16165545

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