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Search Results (828)

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Keywords = perovskite films

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40 pages, 1207 KiB  
Review
Recent Advances in Flexible Solar Cells; Materials, Fabrication, and Commercialization
by Maoz Maoz, Zohair Abbas, Syed Abdul Basit Shah and Vanni Lughi
Sustainability 2025, 17(5), 1820; https://doi.org/10.3390/su17051820 - 21 Feb 2025
Abstract
Flexibility, light weight, and mechanical robustness are the key advantages of flexible photovoltaic (PV) modules, making them highly versatile for sustainable energy solutions. Unlike traditional rigid PV modules, their flexible nature makes them incredibly versatile for harnessing energy in places where doing so [...] Read more.
Flexibility, light weight, and mechanical robustness are the key advantages of flexible photovoltaic (PV) modules, making them highly versatile for sustainable energy solutions. Unlike traditional rigid PV modules, their flexible nature makes them incredibly versatile for harnessing energy in places where doing so was once impossible. They have a wide range of applications due to their flexibility and moldability, making it possible to conform these modules to surfaces like curved rooftops and other irregular structures. In this paper, we provide a comprehensive review of all the materials used in flexible PV modules with a focus on their role in sustainability. We thoroughly discuss the active-layer materials for crystalline silicon (c-Si)-based solar cells (SC) and thin-film solar cells such as cadmium telluride (CdTe), as well as copper indium gallium diselenide (CIGS), amorphous thin-film silicon (a-Si), perovskite and organic solar cells. Various properties, such as the optical, barrier, thermal, and mechanical properties of different substrate materials, are reviewed. Transport layers and conductive electrode materials are discussed with a focus on emerging trends and contributions to sustainable PV technology. Various fabrication techniques involved in making flexible PV modules, along with advantages, disadvantages, and future trends, are highlighted in the paper. The commercialization of flexible PV is also discussed, which is a crucial milestone in advancing and adapting new technologies in the PV industry with a focus on contributing toward sustainability. Full article
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<p>Flexible roof-top photovoltaic cells.</p>
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<p>Schematics of possible cell architecture.</p>
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<p>Comparison of power-conversion efficiency for different active-layer materials for traditional and flexible PV.</p>
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<p>p-i-n (superstrate) and n-i-p (substrate) a-Si:H cell structure.</p>
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<p>OTR and WVTR of different polymers used in packaging materials of different products. Source: [<a href="#B157-sustainability-17-01820" class="html-bibr">157</a>].</p>
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15 pages, 4184 KiB  
Article
Photocatalysis of Methyl Orange (MO), Orange G (OG), Rhodamine B (RhB), Violet and Methylene Blue (MB) Under Natural Sunlight by Ba-Doped BiFeO3 Thin Films
by Abderrahmane Boughelout, Abdelmadjid Khiat and Roberto Macaluso
Materials 2025, 18(4), 887; https://doi.org/10.3390/ma18040887 - 18 Feb 2025
Abstract
We present structural, morphological, optical and photocatalytic properties of multiferroic Bi0.98Ba0.02FeO3 (BBFO2) perovskite thin films prepared by a combined sol–gel and spin-coating method. X-ray diffraction (XRD) analysis revealed that all the perovskite films consisted of the stable polycrystalline [...] Read more.
We present structural, morphological, optical and photocatalytic properties of multiferroic Bi0.98Ba0.02FeO3 (BBFO2) perovskite thin films prepared by a combined sol–gel and spin-coating method. X-ray diffraction (XRD) analysis revealed that all the perovskite films consisted of the stable polycrystalline rhombohedral phase structure (space group R3c) with a tolerance factor of 0.892. By using Rietveld refinement of diffractogram XRD data, crystallographic parameters, such as bond angle, bond length, atom position, unit cell parameters, and electron density measurements were computed. Scanning electron microscopy (SEM) allowed us to assess the homogeneous and smooth surface morphology of the films with a small degree of porosity, while chemical surface composition characterization by X-ray photoelectron spectroscopy (XPS) showed the presence of Bi, Fe, O and the doping element Ba. Absorption measurements allowed us to determine the energy band gap of the films, while photoluminescence measurements have shown the presence of oxygen vacancies, which are responsible for the enhanced photocatalytic activity of the material. Photocatalytic degradation experiments of Methylene Blue (MB), Methyl orange (MO), orange G (OG), Violet and Rhodamine B (RhB) performed on top of BBFO2 thin films under solar light showed the degradation of all pollutants in varying discoloration efficiencies, ranging from 81% (RhB) to 54% (OG), 53% (Violet), 47% (MO) and 43% (MB). Full article
(This article belongs to the Special Issue Halide Perovskite Crystal Materials and Optoelectronic Devices)
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<p>Schematic diagram of the reactor used for the photocatalytic experiments. The arrows indicate the direction of the coolant.</p>
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<p>(<b>a</b>) Measured (black), Rietveld-refined (red), and difference between measured and refined data (blue) XRD patterns using the FullProf program for a BBFO2 thin film. The vertical bars (green) indicate the angular position of the allowed Bragg reflections. (<b>b</b>) The three-dimensional schematic representation of the BBFO2 unit cell with a trigonal structure in a hexagonal setting.</p>
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<p>Two-dimensional and three-dimensional Fourier maps along (x, y, 0), (0, y, z) and (x, 0, z) planes to visualize the electron density (ED) distribution for the BBFO2 film, measured in the number of electrons per cubic Angstrom, n/Å<sup>3</sup>.</p>
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<p>SEM top view of a representative BBFO2 thin film.</p>
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<p>Deconvoluted core level XPS spectra of (<b>a</b>) Bi 4f, (<b>b</b>) O 1s, (<b>c</b>) Fe 2p and (<b>d</b>) Ba 3d of a Ba-doped BFO thin film. The black curves represent the experimental data, while the blue curves are the corresponding fittings. Red, green and cyan curves are the fitted subpeaks.</p>
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<p>BBFO2 film absorbance spectrum. The inset shows Tauc’s plot for energy band gap determination.</p>
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<p>Photoluminescence spectrum of undoped (blue curve) and Ba-doped (red curve) BFO thin films.</p>
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<p>Absorption spectra before and after the photodegradation of (<b>a</b>) OG, (<b>b</b>) Violet, (<b>c</b>) RhB, (<b>d</b>) MO and (<b>e</b>) MB solutions in the presence of BBFO2 films before and after light exposure (6 h). Each plot reports the degradation percentual with respect to the non-exposure condition.</p>
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<p>Photocatalytic degradation of MO, OG, RhB, Violet and MB.</p>
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<p>Photocatalytic mechanism diagram of MO, OG, RhB, Violet and MB in Ba-doped BFO thin films, under natural sunlight.</p>
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11 pages, 2717 KiB  
Article
Vapor-Assisted Method to Deposit Compact (CH3NH3)3Bi2I9 Thin Films for Bismuth-Based Planar Perovskite Solar Cells
by Zihao Gao, Xinjie Wang, Zhen Sun, Ping Song, Xiyuan Feng and Zhixin Jin
Micromachines 2025, 16(2), 218; https://doi.org/10.3390/mi16020218 - 14 Feb 2025
Abstract
Bismuth-based perovskite derivatives, (CH3NH3)3Bi2I9 (MBI), are promising non-toxic light-absorbing materials widely used in various photoelectric devices because of their excellent stability. However, MBI-based perovskite solar cells (PSCs) are limited by poor film quality, and [...] Read more.
Bismuth-based perovskite derivatives, (CH3NH3)3Bi2I9 (MBI), are promising non-toxic light-absorbing materials widely used in various photoelectric devices because of their excellent stability. However, MBI-based perovskite solar cells (PSCs) are limited by poor film quality, and the performance of such a device is far behind that of lead-based PSCs. In this work, the crystal structure and morphological properties of MBI films were compared across different preparation methods. The two-step vapor-assisted method can prepare continuous dense MBI films because MBI crystal nucleation is induced by the BiI3 seed layer. The MBI film grown by this method is better for the production of excellent PSCs compared to the film prepared by the solution method. The best photovoltaic device based on the MBI film could obtain a power conversion efficiency of 1.13%. An MBI device is stored in the glove box for 60 days, and the device’s performance is maintained at 99%. These results indicate that the vapor-assisted deposition of MBI films can be an effective method to improve the performance of bismuth-based planar PSCs. Full article
(This article belongs to the Special Issue Energy Conversion Materials/Devices and Their Applications)
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<p>(<b>a</b>) Preparation procedure of the MBI thin film by the SC method. (<b>b</b>) TSS method. (<b>c</b>) TSVA method.</p>
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<p>The surface morphologies of MBI films were prepared by different methods. (<b>a</b>) SC method, (<b>b</b>) TSS, (<b>c</b>) TSVA method.</p>
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<p>(<b>a</b>) XRD patterns. The “*” symbols represent the signals of the FTO substrates. (<b>b</b>) UV–visible spectra, (<b>c</b>) Tauc plot versus the light energy, (<b>d</b>) photoluminescence spectra of MBI films grown via different methods.</p>
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<p>(<b>a</b>) Configuration of the planar MBI photovoltaic device; (<b>b</b>) schematic band diagram of MBI film grown via different methods.</p>
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<p>(<b>a</b>) <span class="html-italic">J</span>-<span class="html-italic">V</span> curves of MBI devices with different growth methods. (<b>b</b>) IPCE spectra and the integrated current for the different devices. (<b>c</b>) Stability of MBI devices with different preparation methods in a glove box. (<b>d</b>) PCE box statistics of 20 photovoltaic devices prepared by different methods.</p>
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<p>(<b>a</b>) C-V curves of different devices yielded by Mott–Schottky testing; (<b>b</b>) SCLC curves for hole-only devices prepared via different methods.</p>
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9 pages, 1685 KiB  
Article
Optimal Methylammounium Chloride Additive for High-Performance Perovskite Solar Cells
by Qinghua Cao, Hui Liu, Jiangping Xing, Bing’e Li, Chuangping Liu, Fobao Xie, Xiaoli Zhang and Weiren Zhao
Nanomaterials 2025, 15(4), 292; https://doi.org/10.3390/nano15040292 - 14 Feb 2025
Abstract
Organic–inorganic lead halide perovskite solar cells (PSCs) have presented promising improvements within recent years due to the superior photophysical properties of perovskites. The efficiency of PSCs is closely related to the quality of the of the perovskite film. Additive engineering is an effective [...] Read more.
Organic–inorganic lead halide perovskite solar cells (PSCs) have presented promising improvements within recent years due to the superior photophysical properties of perovskites. The efficiency of PSCs is closely related to the quality of the of the perovskite film. Additive engineering is an effective strategy to regulate the crystallization of perovskite film. Therefore, in this work, we introduce methylammounium chloride (MACl) into a perovskite precursor as an additive to improve the crystallization of perovskite film and to suppress the formation of defects to achieve high-performance PSCs. By meticulously investigating and studying the influence of different percentages of MACl additives on perovskite film quality, we obtain that the best amount of incorporated MACl is 10%. Thanks the employment of the optimal amount of MACl, the perovskite film shows a significantly improved morphology with larger grains, a smoother surface, and suppressed defects. Finally, the target PSCs with the addition of 10% MACl present the highest PCE of 23.61%, which is much higher than the value (16.72%) of the control device. Full article
(This article belongs to the Special Issue Perovskite Nanomaterials for Photovoltaic and Optoelectronic Devices)
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<p>Statistical distribution of (<b>a</b>) PCE, (<b>b</b>) Voc, (<b>c</b>) FF, and (<b>d</b>) Jsc of PSCs with different percentages of MACl additives.</p>
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<p>SEM images of (<b>a</b>) control perovskite film and (<b>b</b>) target perovskite film; AFM images of (<b>c</b>) control perovskite film and (<b>d</b>) target perovskite film.</p>
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<p>(<b>a</b>) XRD spectra, (<b>b</b>) absorbance spectra, (<b>c</b>) Tauc plots, and (<b>d</b>) PL spectra of control and target perovskite films.</p>
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<p>(<b>a</b>) Diagram of structure of PSCs; (<b>b</b>) J-V curves of best-performing target PSCs fabricated with 10% MACl additive and control device; (<b>c</b>) dark current curves of control and target PSCs; (<b>d</b>) light intensity dependence of Voc of control and target PSCs.</p>
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27 pages, 6383 KiB  
Review
A Review of Measurement and Characterization of Film Layers of Perovskite Solar Cells by Spectroscopic Ellipsometry
by Liyuan Ma, Xipeng Xu, Changcai Cui, Tukun Li, Shan Lou, Paul J. Scott, Xiangqian Jiang and Wenhan Zeng
Nanomaterials 2025, 15(4), 282; https://doi.org/10.3390/nano15040282 - 13 Feb 2025
Abstract
This article aims to complete a review of current literature describing the measurement and characterization of photoelectric and geometric properties of perovskite solar cell (PSC) film layer materials using the spectroscopic ellipsometry (SE) measurement technique. Firstly, the influence of film quality on the [...] Read more.
This article aims to complete a review of current literature describing the measurement and characterization of photoelectric and geometric properties of perovskite solar cell (PSC) film layer materials using the spectroscopic ellipsometry (SE) measurement technique. Firstly, the influence of film quality on the performance of PSCs is combed and analyzed. Secondly, SE measurement technology is systematically introduced, including the measurement principle and data analysis. Thirdly, a detailed summary is provided regarding the characterization of the geometric and optoelectronic properties of the substrate, electron transport layer (ETL), perovskite layer, hole transport layer (HTL), and metal electrode layer using SE. The oscillator models commonly used in fitting film layer materials in PSCs are comprehensively summarized. Fourthly, the application of SE combined with various measurement techniques to assess the properties of film layer materials in PSCs is presented. Finally, the noteworthy direction of SE measurement technology in the development of PSCs is discussed. The review serves as a valuable reference for further enhancing the application of SE in PSCs, ultimately contributing to the commercialization of PSCs. Full article
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<p>Measurement and characterization of photoelectric and geometric properties for each film layer of a typical SnO<sub>2</sub>-based PSC by SE.</p>
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<p>Three common structures of PSCs.</p>
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<p>Influencing factors of power conversion efficiency of PSCs.</p>
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<p>The basic principle of SE measurement and analysis.</p>
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<p>Fitting strategies of PSC multilayer films stack structure.</p>
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<p>Characterization of SnO<sub>2</sub> films by SE. (<b>a</b>) Different substrates [<a href="#B54-nanomaterials-15-00282" class="html-bibr">54</a>]. (<b>b</b>) Different temperature [<a href="#B53-nanomaterials-15-00282" class="html-bibr">53</a>]. (<b>c</b>) Different thickness [<a href="#B51-nanomaterials-15-00282" class="html-bibr">51</a>]. (<b>d</b>) Different technology [<a href="#B52-nanomaterials-15-00282" class="html-bibr">52</a>]. (<b>e</b>) Different doping ratios [<a href="#B55-nanomaterials-15-00282" class="html-bibr">55</a>].</p>
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<p>Analysis procedure of geometric and photoelectric properties of SnO<sub>2</sub> films by SE.</p>
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<p>Perovskite materials and devices. (<b>a</b>) Element [<a href="#B16-nanomaterials-15-00282" class="html-bibr">16</a>]. (<b>b</b>) Structure [<a href="#B75-nanomaterials-15-00282" class="html-bibr">75</a>]. (<b>c</b>) Device [<a href="#B76-nanomaterials-15-00282" class="html-bibr">76</a>]. (<b>d</b>) Principle [<a href="#B77-nanomaterials-15-00282" class="html-bibr">77</a>].</p>
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<p>Preparation process of perovskite film [<a href="#B80-nanomaterials-15-00282" class="html-bibr">80</a>]. (<b>a</b>) One-step coating. (<b>b</b>) Two-step coating.</p>
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<p>Influence factors of perovskite films. (<b>a</b>) Rough layer [<a href="#B82-nanomaterials-15-00282" class="html-bibr">82</a>,<a href="#B83-nanomaterials-15-00282" class="html-bibr">83</a>]. (<b>b</b>) Ion doping [<a href="#B86-nanomaterials-15-00282" class="html-bibr">86</a>]. (<b>c</b>) Interfacial layer [<a href="#B20-nanomaterials-15-00282" class="html-bibr">20</a>]. (<b>d</b>) Void ratio [<a href="#B61-nanomaterials-15-00282" class="html-bibr">61</a>].</p>
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<p>Influence of the external environment on perovskite films [<a href="#B87-nanomaterials-15-00282" class="html-bibr">87</a>].</p>
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<p>Influence of external environment on the properties of the perovskite film characterized by SE. (<b>a</b>) Humidity [<a href="#B89-nanomaterials-15-00282" class="html-bibr">89</a>]. (<b>b</b>) Temperature [<a href="#B90-nanomaterials-15-00282" class="html-bibr">90</a>].</p>
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<p>(<b>a</b>) Optical constant of the Spiro-OMeTAD film [<a href="#B113-nanomaterials-15-00282" class="html-bibr">113</a>]. (<b>b</b>) Optical constant of PEDOT: PSS, Cu<sub>2</sub>O, and CuI films [<a href="#B114-nanomaterials-15-00282" class="html-bibr">114</a>]. (<b>c</b>) Optical constant of the NiOx film [<a href="#B115-nanomaterials-15-00282" class="html-bibr">115</a>].</p>
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<p>Assist technique in spectroscopic ellipsometry. (<b>a</b>) Scanning electron microscopy (SEM) [<a href="#B61-nanomaterials-15-00282" class="html-bibr">61</a>]. (<b>b</b>) Photoluminescence (PL) [<a href="#B46-nanomaterials-15-00282" class="html-bibr">46</a>]. (<b>c</b>) Atomic force microscopy (AFM) [<a href="#B61-nanomaterials-15-00282" class="html-bibr">61</a>]. (<b>d</b>) Ultraviolet-visible spectroscopy (UV-Vis) [<a href="#B127-nanomaterials-15-00282" class="html-bibr">127</a>].</p>
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14 pages, 7012 KiB  
Article
The Effect of A-Cation and X-Anion Substitutions on the Electronic and Structural Properties of A2ZrX6 ‘Defect’ Perovskite Materials: A Theoretical Density Functional Theory Study
by Christina Kolokytha, Nektarios N. Lathiotakis, Andreas Kaltzoglou, Ioannis D. Petsalakis and Demeter Tzeli
Materials 2025, 18(3), 726; https://doi.org/10.3390/ma18030726 - 6 Feb 2025
Abstract
In the present work, nine ‘defect’ perovskites with the chemical formula A2ZrX6 have been studied, where the A-site cations are a methylammonium cation, formamidinium cation, and trimethyl-sulfonium cation and the X-site anions are halogen, X = Cl, Br, and I. [...] Read more.
In the present work, nine ‘defect’ perovskites with the chemical formula A2ZrX6 have been studied, where the A-site cations are a methylammonium cation, formamidinium cation, and trimethyl-sulfonium cation and the X-site anions are halogen, X = Cl, Br, and I. We employ periodic DFT calculations using GGA-PBE, MBJ, HSEsol, and HSE06 functionals. All studied compounds exhibit a wide-bandgap energy that ranges from 5.22 eV to 2.11 eV, while for some cases, geometry optimization led to significant structural modification. It was found that the increase in the halogen size resulted in a decrease in the bandgap energy. The choice of the organic A-site cation affects the bandgap as well, which is minimal for the methylammonium cation. Such semiconductors with organic cations may be utilized in optoelectronic devices, given the substantial benefit of solution processability and thin film formation compared to purely inorganic analogs, such as Cs2ZrX6. Full article
(This article belongs to the Section Advanced Nanomaterials and Nanotechnology)
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<p>Calculated band structure and DOS of the (<b>a</b>) experimental crystal structure TMS<sub>2</sub>ZrCl<sub>6</sub> and (<b>b</b>) energetically optimized crystal structure TMS<sub>2</sub>ZrCl<sub>6</sub>.</p>
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<p>Calculated DOS of TMS<sub>2</sub>ZrCl<sub>6</sub> using three different functionals: (<b>a</b>) Meta-GGA functional mBJ, (<b>b</b>) screened hybrid functional HSEsol, and (<b>c</b>) screened hybrid functional HSE06.</p>
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<p>The optimized cubic crystal structures are shown for (<b>a</b>) TMS<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) TMS<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) TMS<sub>2</sub>ZrI<sub>6</sub>. The images were created using VESTA software, version 3.90.1a [<a href="#B35-materials-18-00726" class="html-bibr">35</a>]. Color assignment: yellow for S, black for carbon, white for hydrogen, grey for Zr, green for Cl, brown for Br, and violet for I.</p>
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<p>The calculated GGA-PBE band structure and DOS of (<b>a</b>) TMS<sub>2</sub>ZrBr<sub>6</sub> and (<b>b</b>) TMS<sub>2</sub>ZrI<sub>6</sub>.</p>
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<p>The calculated HSE06 DOS of (<b>a</b>) TMS<sub>2</sub>ZrBr<sub>6</sub> and (<b>b</b>) TMS<sub>2</sub>ZrI<sub>6</sub>.</p>
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<p>The optimized crystal structures of (<b>a</b>) MA<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) MA<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) MA<sub>2</sub>ZrI<sub>6</sub>. The images were created using VESTA software, version 3.90.1a. Color assignment: blue for N, black for carbon, white for hydrogen, grey for Zr, green for Cl, brown for Br, and violet for I.</p>
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<p>The calculated DOS of (<b>a</b>) MA<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) MA<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) MA<sub>2</sub>ZrI<sub>6</sub> using the GGA-PBE functional.</p>
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<p>The calculated DOS of (<b>a</b>) MA<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) MA<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) MA<sub>2</sub>ZrI<sub>6</sub> using the HSE06 functional.</p>
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<p>The optimized crystal structures are shown for (<b>a</b>) FA<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) FA<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) FA<sub>2</sub>ZrI<sub>6</sub>. The images were created using VESTA software, version 3.90.1a. Color assignment: blue for N, black for carbon, white for hydrogen, grey for Zr, green for Cl, brown for Br and violet for I.</p>
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<p>The calculated DOS of (<b>a</b>) FA<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) FA<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) FA<sub>2</sub>ZrI<sub>6</sub> using the GA-PBE functional.</p>
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<p>The calculated DOS of (<b>a</b>) FA<sub>2</sub>ZrCl<sub>6</sub>, (<b>b</b>) FA<sub>2</sub>ZrBr<sub>6</sub>, and (<b>c</b>) FA<sub>2</sub>ZrI<sub>6</sub> using the HSE06 functional.</p>
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<p>Bandgap energy as a function of the molecular weight of the A-site cation (g/mol) for the A<sub>2</sub>ZrX<sub>6</sub> crystal, calculated using the HSE06 (solid lines) and GGA-PBE (dash lines) functionals. Available experimental value is also included [<a href="#B20-materials-18-00726" class="html-bibr">20</a>]. Color assignment: blue for N, grey for carbon, white for hydrogen, yellow for S.</p>
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<p>Bandgap energy as a function of halogen electronegativity of the A<sub>2</sub>ZrX<sub>6</sub>, calculated using the HSE06 (solid lines) and GGA-PBE (dash lines) functionals. Available experimental value is also included [<a href="#B20-materials-18-00726" class="html-bibr">20</a>].</p>
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12 pages, 3506 KiB  
Article
Photoluminescence and Stability of Dion–Jacobson Tin-Based Halide Perovskites with Different Spacer Cation Chain Length
by Muhammad Umair Ali, Wen Ting Sun, Aleksandr A. Sergeev, Atta Ur Rehman, Kam Sing Wong, Aleksandra B. Djurišić and Jasminka Popović
Molecules 2025, 30(3), 703; https://doi.org/10.3390/molecules30030703 - 5 Feb 2025
Abstract
Two-dimensional tin halide perovskites are of significant interest for light emitting applications. Here, we investigate the effect of organic cation A on the stability of different Dion–Jacobson tin-based halide perovskites. The ASnBr4 materials using diammonium cation A with shorter alkyl chains are [...] Read more.
Two-dimensional tin halide perovskites are of significant interest for light emitting applications. Here, we investigate the effect of organic cation A on the stability of different Dion–Jacobson tin-based halide perovskites. The ASnBr4 materials using diammonium cation A with shorter alkyl chains are found to exhibit improved stability, exhibiting dramatic stability difference between the most stable HDASnBr4, where HDA denotes 1,6-hexanediammonium, and two materials with 8- and 10-carbon alkyl chain ammonium cations. The HDASnBr4 powders were thermally stable at 100 °C in an argon environment but exhibited decreasing photoluminescence with time in ambient air at 100 °C. The sample degradation at 100 °C is accelerated compared to room temperature, but it proceeds along similar pathways, namely phase transformation followed by perovskite decomposition. Light emission from HDASnBr4 thin films could be further enhanced by methanol vapor treatment, and warm white emission with Commission Internationale de l’Eclairage (CIE) coordinates (0.37, 0.34) could be obtained by combining HDASnBr4 with a blue-emitting polymer film, while direct mixing of blue phosphor and HDASnBr4 powder yields white emission with CIE coordinates of (0.34, 0.32). Full article
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<p>(<b>a</b>) Photoluminescence of ASnBr<sub>4</sub> as a function of time in ambient air at 100 °C for (<b>b</b>) A = HDA, (<b>c</b>) A = ODA, and (<b>d</b>) A = DDA.</p>
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<p>Le Bail refinement of (<b>a</b>) HDA-based perovskite, (<b>b</b>) ODA-based perovskite, (<b>c</b>) DDA-based perovskite. Experimental diffraction patterns are shown as black lines while the calculated patterns for are represented by blue lines. Diffraction lines corresponding to the 2D phase are marked with green vertical lines while the reflections of the 1D phase are marked with dark red vertical bars. (<b>d</b>) Structures of the 2D HDASnBr<sub>4</sub> phase and 1D HDA<sub>3</sub>SnBr<sub>8</sub>·(H<sub>2</sub>O) phase, Sn-octahedra are given in teal, bromides are shown as orange balls while carbons, nitrogens, oxygens, hydrogens are gray, light blue, red, and white balls, respectively; (<b>e</b>) enlarged part of the XRD patterns showing the most prominent diffraction lines for as-prepared HDA, ODA, and DDA samples. Diffraction lines corresponding to the 2D phase are colored in green while the reflections of the 1D phase are colored in dark red.</p>
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<p>XRD patterns of thermally treated samples with different spacers: (<b>a</b>) ODA, (<b>b</b>) DDA, (<b>c</b>) HDA; unidentified phase is denoted by *, (<b>d</b>) enlarged part of XRD pattern for HDA sample, (<b>e</b>) Le Bail refinement of diffraction lines at ~8.9°2θ. The diffraction line corresponding to the 2D phase is colored in green while the reflection of the 1D phase is colored in dark red.</p>
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<p>Thermogravimetric analysis plot of ASnBr<sub>4</sub> perovskites for different spacers A (HDA, ODA, and DDA).</p>
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<p>(<b>a</b>) PL spectra of HDASnBr<sub>4</sub> film with different blue-emitting polymer formulations. TFB10 and TFB20 denote 10 and 20 mg of TFB dissolved in 1 mL chlorobenzene, and BP@TFB indicates 10 mg of BP dissolved in TFB solution. (<b>b</b>) CIE coordinates chart for HDASnBr<sub>4</sub>+ BP@TFB corresponding to (0.37, 0.34). (<b>c</b>) PL spectrum of HDASnBr<sub>4</sub> BP mixture with a ratio 1:0.50 (inset shows the corresponding photo under UV illumination) and (<b>d</b>) corresponding CIE coordinates (0.34, 0.32).</p>
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15 pages, 3550 KiB  
Article
Enhancing Perovskite Solar Cell Stability by TCO Layer Presence Beneath MACl-Doped Perovskites
by Minkyu Song, Jinyoung Kim and Gyu Min Kim
Crystals 2025, 15(2), 152; https://doi.org/10.3390/cryst15020152 - 1 Feb 2025
Abstract
Perovskite solar cells (PSCs) have emerged as a promising photovoltaic technology, yet their stability under environmental stressors remains a critical challenge. This study examines the substrate-dependent degradation mechanisms of perovskite films and evaluates the role of methylammonium chloride (MACl) incorporation. Devices fabricated on [...] Read more.
Perovskite solar cells (PSCs) have emerged as a promising photovoltaic technology, yet their stability under environmental stressors remains a critical challenge. This study examines the substrate-dependent degradation mechanisms of perovskite films and evaluates the role of methylammonium chloride (MACl) incorporation. Devices fabricated on ITO and glass substrates exhibited markedly different stability behaviors under high-humidity conditions. ITO substrates delayed the phase transition from the black α-phase to the yellow δ-phase due to stronger substrate–film interactions and reduced defect densities, while glass substrates facilitated rapid degradation through moisture infiltration and grain boundary instability. MACl incorporation enhanced the initial crystallinity and optoelectronic properties of the perovskite films, as evidenced by superior power conversion efficiency and photon absorption. However, residual MACl under humid conditions introduced structural instability, particularly on glass substrates. To address these challenges, a fully coated ITO structure, referred to as the Island Type design, was proposed. This structure eliminates exposed glass regions, leveraging the stabilizing properties of ITO to suppress moisture infiltration and prolong device durability. The findings provide a comprehensive understanding of the interplay between substrate properties and material composition in PSC stability and highlight the potential of structural optimizations to balance efficiency and durability for commercial applications. Full article
(This article belongs to the Section Materials for Energy Applications)
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<p>(<b>a</b>) Schematic of the etched ITO device structure used in this study. (<b>b</b>) Visual evolution of the perovskite layer over time under the MACl_O condition. (<b>c</b>) Normalized performance data of MACl_X and MACl_O devices over time.</p>
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<p>(<b>a</b>) XRD patterns of perovskite films for four conditions over time. (<b>b</b>) Intensity ratio (<math display="inline"><semantics> <mrow> <msub> <mrow> <mi>I</mi> </mrow> <mrow> <mi>r</mi> </mrow> </msub> <mo>=</mo> <msub> <mrow> <mi>I</mi> </mrow> <mrow> <mi>δ</mi> </mrow> </msub> <mo>/</mo> <msub> <mrow> <mi>I</mi> </mrow> <mrow> <mi>α</mi> </mrow> </msub> </mrow> </semantics></math>) comparison between glass and ITO substrates.</p>
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<p>(<b>a</b>) PL spectra of perovskite films on glass and ITO substrates under MACl_X. (<b>b</b>) PL spectra of perovskite films on glass and ITO substrates under MACl_O. (<b>c</b>) TRPL decay curves on glass and ITO substrates under MACl_X. (<b>d</b>) TRPL decay curves on glass and ITO substrates under MACl_O.</p>
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<p>(<b>a</b>) SEM images of perovskite films on glass substrates on Day 1. (<b>b</b>) SEM images of perovskite films on ITO substrates on Day 1. (<b>c</b>) SEM images of perovskite films on glass substrates on Day 8. (<b>d</b>) SEM images of perovskite films on ITO substrates on Day 8.</p>
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<p>(<b>a</b>) Three-dimensional AFM images of perovskite films on glass substrates on Day 1. (<b>b</b>) Three-dimensional AFM images of perovskite films on ITO substrates on Day 1. (<b>c</b>) Three-dimensional AFM images of perovskite films on glass substrates on Day 8. (<b>d</b>) Three-dimensional AFM images of perovskite films on ITO substrates on Day 8. (<b>e</b>) Schematic illustration of moisture infiltration mechanisms through the surfaces of glass and ITO substrates.</p>
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<p>(<b>a</b>) J-V curves for perovskite solar cells under MACl_X and MACl_O conditions, with forward and reverse scan data. (<b>b</b>) External quantum efficiency (EQE) spectra for devices under MACl_X and MACl_O conditions. (c) The normalized performance data of perovskite solar cells under MACl_O and MACl_X conditions for both the Island Type structure and the Etched ITO structure. (<b>d</b>) Schematic diagrams of the proposed Island Type structure (<b>left</b>) and the conventional etched ITO structure (<b>right</b>).</p>
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19 pages, 14656 KiB  
Article
Research Progress on Development of PVP-Ag-Doped LaMnO3 Composites for Methyl Orange Degradation
by Adina Căta, Madalina-Gabriela Ivanovici, Paula Svera, Ioana Maria Carmen Ienașcu and Paula Sfirloaga
Metals 2025, 15(2), 151; https://doi.org/10.3390/met15020151 - 1 Feb 2025
Abstract
Water pollution caused by emerging contaminants is increasing due to rising urbanization, industrialization, and agriculture production; therefore, new materials with high efficiency for wastewater decontamination are needed. A perovskite material based on 1% Ag-doped LaMnO3 synthesized through a sol–gel technique was combined [...] Read more.
Water pollution caused by emerging contaminants is increasing due to rising urbanization, industrialization, and agriculture production; therefore, new materials with high efficiency for wastewater decontamination are needed. A perovskite material based on 1% Ag-doped LaMnO3 synthesized through a sol–gel technique was combined with PVP in a 1:10 (w/w) ratio and subjected to different temperature and microwave conditions at various time intervals. The composite materials were obtained as thin films (S1, S2) or powders (S3) and were analyzed by modern techniques. The SEM analysis showed strongly agglomerated, asymmetric formations for the S1, S2 materials; as for the S3 composite, irregularly shaped grains of perovskite were deposited on the polymer surface. Small, round formations across the surface, mainly organized as clusters with conic/square-shaped particles and observed asperity on top, were highlighted by AFM images. The XRD spectra confirmed the presence of both the perovskite and PVP phases, and the crystallite size of the materials was determined to be in the range of 33–43 nm. The structural analyses, FT-IR, and Raman spectroscopy proved the interactions between the perovskite and the polymer, which led to novel composite materials. The different methods used for the synthesis of the new materials influenced their features and behavior. Moreover, the composites were successfully tested for methyl orange (MO) elimination from an acidic aqueous solution in dark conditions, with fast and complete (>95%) MO degradation at pH = 2. Full article
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<p>Schematic representation of experimental approach for evaluation of MO degradation assisted by PVP-perovskite composites.</p>
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<p>X-ray diffractograms for samples S1, S2, and S3.</p>
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<p>The SEM images obtained for composites S1, S2, and S3.</p>
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<p>The FT-IR spectra of pure PVP and PVP–perovskite composites (S1, S2, S3).</p>
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<p>Raman spectra of pure PVP, LaMnO<sub>3</sub>:Ag, and PVP–perovskite composites (S1, S2).</p>
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<p>Two- (<b>a</b>) and three-dimensional (<b>b</b>) images of sample S1.</p>
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<p>Surface profile of selected areas of sample S1.</p>
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<p>Two- (<b>a</b>) and three-dimensional (<b>b</b>) images of sample S2.</p>
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<p>Surface profile of selected areas of sample S2.</p>
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<p>(<b>a</b>) Time-dependent degradation ratio (A/A<sub>0</sub>) illustrated at pH = 2 for reference test and for each test material (S1, S2, and S3); (<b>b</b>) representation of peak shape changes for absorbance of MO solution before pH adjustment and at pH = 2, pH = 3, and pH = 4.</p>
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<p>Degradation ratio (A/A<sub>0</sub>) vs. time calculated at (<b>a</b>) pH = 2, (<b>b</b>) pH = 3, and (<b>c</b>) pH = 4 for samples S1, S2, and S3.</p>
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<p>Degradation ratio (A/A<sub>0</sub>) vs. time calculated for (<b>a</b>) S1, (<b>b</b>) S2, and (<b>c</b>) S3 in different acidic environments (pH = 2, pH = 3, pH = 4), with inset representing the absorbance peaks of MO solution monitored over two hours at pH = 2 for (<b>a</b>) S1 composite, (<b>b</b>) S2 composite, and (<b>c</b>) S3composite.</p>
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<p>UV-VIS spectra of MO acidic solution monitored for 4 h over the course of MO degradation reaction assisted by the S3 composite; inset: in-time variation in the absorption spectra between 200 and 375 nm.</p>
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12 pages, 2055 KiB  
Article
Effect of Ammonium Salt on Conjugated Polyelectrolyte as an Interlayer for Organic–Inorganic Hybrid Perovskite Memristors
by Eun Soo Shim, Ji Hyeon Lee, Ju Wan Park, Sun Woo Kim, Su Bin Park and Jea Woong Jo
Nanomaterials 2025, 15(3), 227; https://doi.org/10.3390/nano15030227 - 30 Jan 2025
Abstract
Memristors are promising candidates for next-generation non-volatile memory devices, offering low power consumption and high-speed switching capabilities. However, conventional metal oxide-based memristors are constrained by fabrication complexity and high costs, limiting their commercial viability. Organic–inorganic hybrid perovskites (OIHPs), known for their facile solution [...] Read more.
Memristors are promising candidates for next-generation non-volatile memory devices, offering low power consumption and high-speed switching capabilities. However, conventional metal oxide-based memristors are constrained by fabrication complexity and high costs, limiting their commercial viability. Organic–inorganic hybrid perovskites (OIHPs), known for their facile solution processability and unique ionic–electronic conductivity, provide an attractive alternative. This study presents a conjugated polyelectrolyte (CPE), PhNa-1T, as an interlayer for OIHP memristors to enhance the high-resistance state (HRS) performance. A post-treatment process using n-octylammonium bromide (OABr) was further applied to optimize the interlayer properties. Devices treated with PhNa-1T/OABr achieved a significantly improved ON/OFF ratio of 2150, compared to 197 for untreated devices. Systematic characterization revealed that OABr treatment improved film morphology, reduced crystallite strain, and optimized energy level alignment, thereby reinforcing the Schottky barrier and minimizing current leakage. These findings highlight the potential of tailored interlayer engineering to improve OIHP-based memristor performance, offering promising prospects for applications in non-volatile memory technologies. Full article
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<p>(<b>a</b>) Chemical structure of PhNa−1T and OABr. (<b>b</b>) UV−Vis absorbance spectra of PhNa−1T and PhNa−1T/OABr. (<b>c</b>) XPS plots of S 2p for PhNa−1T films before and after OABr treatment (dotted points are raw data, and blue lines are total fitted data, yellow lines are S 2<span class="html-italic">p</span><sub>1/2</sub> for SO<sub>3</sub><sup>−</sup>, red lines are S 2<span class="html-italic">p</span><sub>3/2</sub> for SO<sub>3</sub><sup>−</sup>, peach lines are S 2<span class="html-italic">p</span><sub>1/2</sub> for S, and green lines are S 2<span class="html-italic">p</span><sub>3/2</sub> for S). (<b>d</b>) Memristic <span class="html-italic">I−V</span> curve of PhNa−1T interlayer with OIHP (inset image: device architecture).</p>
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<p>(<b>a</b>) Schematic device configuration of the OHP memristor used in this study. (<b>b</b>) Current–voltage measurement of the memristors with PhNa−1T and PhNa−1T/OABr interlayers. (<b>c</b>) Endurance and (<b>d</b>) retention testing results for OIHP memristors depending on interlayers (Resistance range at HRS were shaded with color for retention tests).</p>
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<p>(<b>a</b>) AFM images and (<b>b</b>) XRD patterns for the PbBr<sub>2</sub> films on PhNa−1T and PhNa−1T/OABr. (<b>c</b>) AFM images and (<b>d</b>) microstrain analysis for the OIHP films on PhNa−1T and PhNa−1T/OABr (AFM images were taken with dimensions of 4 μm × 4 μm).</p>
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<p>(<b>a</b>) UPS spectra for PhNa−1T and PhNa−1T/OABr films. (<b>b</b>) Schematic diagram for energy level alignments occurred for PhNa−1T and PhNa−1T/OABr.</p>
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18 pages, 1876 KiB  
Review
A Review of Perovskite-Based Solar Cells over the Last Decade: The Evolution of the Hole Transport Layer and the Use of WO3 as an Electron Transport Layer
by Albán Ávila-López, Julio César Cruz, Jesús Adrián Díaz-Real, Karla García-Uitz, Daniel Cante-Góngora and German Rodríguez-May
Coatings 2025, 15(2), 132; https://doi.org/10.3390/coatings15020132 - 23 Jan 2025
Viewed by 539
Abstract
Perovskite solar cells are part of the third generation of solar cells, a technology that holds the potential to reduce the use of fossil fuels in energy production. Some factors, such as stability and toxicity, jeopardize the scaling process towards commercialization and access [...] Read more.
Perovskite solar cells are part of the third generation of solar cells, a technology that holds the potential to reduce the use of fossil fuels in energy production. Some factors, such as stability and toxicity, jeopardize the scaling process towards commercialization and access to worldwide markets. This work comprises a review over the last decade on PSC advances and progress in the most highly cited databases. A marked trend was found in replacing Pb for Sn from the absorbing perovskite materials, as well as finding the transport layers that will help in the stability and the efficiency of the solar cell. WO3 is presented as a viable element for the formation of the electron transport layer. Spiro-OMeTAD is the most used compound for the hole transport layer, but other viable substitutes were also found. Lastly, the Cs2SnI6 double perovskite was identified as one of the most stable perovskites that emerged in these 10 years. The efficiency and stability of Sn-based solar cells is still very low when compared to their Pb-based counterparts, driving the current research in material science to enhance their performance. Full article
(This article belongs to the Special Issue Perovskite Films as Functional Coatings: Synthesis and Applications)
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<p>Detail of (<b>a</b>) crystal structure of a perovskite [<a href="#B14-coatings-15-00132" class="html-bibr">14</a>,<a href="#B15-coatings-15-00132" class="html-bibr">15</a>], reproduced with permission of Gražulis et al. [<a href="#B15-coatings-15-00132" class="html-bibr">15</a>] and (<b>b</b>) extended network structure of an ABX<sub>3</sub> perovskite [<a href="#B2-coatings-15-00132" class="html-bibr">2</a>] Reproduced with permission of Noman et al. [<a href="#B2-coatings-15-00132" class="html-bibr">2</a>].</p>
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<p>Several schematic configurations of PSCs including: (<b>a</b>) regular mesoscopic, (<b>b</b>) regular planar, (<b>c</b>) inverted planar, and (<b>d</b>) inverted mesoscopic configurations [<a href="#B30-coatings-15-00132" class="html-bibr">30</a>]. Figure reproduced with permission of Sharif et al. [<a href="#B30-coatings-15-00132" class="html-bibr">30</a>].</p>
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<p><span class="html-italic">(</span><b>a</b>) Schematic of the working principle of a PSC. (<b>b</b>) Energy level diagram of an n-i-p type device configuration. Adapted with permission from Hole and electron transport materials: A review on recent progress in organic charge transport materials for efficient, stable, and scalable perovskite solar cells. Krishna et al. [<a href="#B45-coatings-15-00132" class="html-bibr">45</a>].</p>
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<p>Energy levels for various ETMs and perovskite absorbers. Data taken from [<a href="#B2-coatings-15-00132" class="html-bibr">2</a>,<a href="#B21-coatings-15-00132" class="html-bibr">21</a>,<a href="#B48-coatings-15-00132" class="html-bibr">48</a>,<a href="#B54-coatings-15-00132" class="html-bibr">54</a>,<a href="#B55-coatings-15-00132" class="html-bibr">55</a>].</p>
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<p>Best performing Sn-based PSC with Spiro-OMeTAD as an HTL from 2014 to 2023. Data taken from [<a href="#B87-coatings-15-00132" class="html-bibr">87</a>,<a href="#B97-coatings-15-00132" class="html-bibr">97</a>,<a href="#B98-coatings-15-00132" class="html-bibr">98</a>,<a href="#B99-coatings-15-00132" class="html-bibr">99</a>,<a href="#B100-coatings-15-00132" class="html-bibr">100</a>,<a href="#B101-coatings-15-00132" class="html-bibr">101</a>,<a href="#B102-coatings-15-00132" class="html-bibr">102</a>,<a href="#B103-coatings-15-00132" class="html-bibr">103</a>,<a href="#B104-coatings-15-00132" class="html-bibr">104</a>,<a href="#B105-coatings-15-00132" class="html-bibr">105</a>,<a href="#B106-coatings-15-00132" class="html-bibr">106</a>].</p>
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<p>Cs<sub>2</sub>SnI<sub>6</sub> crystal structure [<a href="#B121-coatings-15-00132" class="html-bibr">121</a>]. Figure adapted from Stoumpos et al. [<a href="#B121-coatings-15-00132" class="html-bibr">121</a>].</p>
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25 pages, 7109 KiB  
Review
Research Progress on Quantum Dot-Embedded Polymer Films and Plates for LCD Backlight Display
by Bin Xu, Jiankang Zhou, Chengran Zhang, Yunfu Chang and Zhengtao Deng
Polymers 2025, 17(2), 233; https://doi.org/10.3390/polym17020233 - 17 Jan 2025
Viewed by 471
Abstract
Abstract: Quantum dot–polymer composites have the advantages of high luminescent quantum yield (PLQY), narrow emission half-peak full width (FWHM), and tunable emission spectra, and have broad application prospects in display and lighting fields. Research on quantum dots embedded in polymer films and plates [...] Read more.
Abstract: Quantum dot–polymer composites have the advantages of high luminescent quantum yield (PLQY), narrow emission half-peak full width (FWHM), and tunable emission spectra, and have broad application prospects in display and lighting fields. Research on quantum dots embedded in polymer films and plates has made great progress in both synthesis technology and optical properties. However, due to the shortcomings of quantum dots, such as cadmium selenide (CdSe), indium phosphide (InP), lead halide perovskite (LHP), poor water, oxygen, and light stability, and incapacity for large-scale synthesis, their practical application is still restricted. Various polymers, such as methyl methacrylate (PMMA), polyethylene terephthalate (PET), polystyrene (PS), polyvinylidene fluoride (PVDF), polypropylene (PP), etc., are widely used in packaging quantum dot materials because of their high plasticity, simple curing, high chemical stability, and good compatibility with quantum dot materials. This paper focuses on the application and development of quantum dot–polymer materials in the field of backlight displays, summarizes and expounds the synthesis strategies, advantages, and disadvantages of different quantum dot–polymer materials, provides inspiration for the optimization of quantum dot–polymer materials, and promotes their application in the field of wide-color-gamut backlight display. Full article
(This article belongs to the Special Issue Polymers/Their Hybrid Materials for Optoelectronic Applications)
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<p>(<b>a</b>) Photoluminescent liquid crystal display structure schematic diagram. Reprinted with permission from ref. [<a href="#B1-polymers-17-00233" class="html-bibr">1</a>]. Copyright 2020 Springer Nature. (<b>b</b>) Gamut in CIE chromaticity diagram. Reprinted with permission from ref. [<a href="#B4-polymers-17-00233" class="html-bibr">4</a>]. Copyright 2023 Wiley. (<b>c</b>) Current problems and challenges faced by quantum dot materials.</p>
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<p>Group II–VI quantum dots. (<b>a</b>) PL spectra for CdSe/CdS core–shell nanocrystals with different core size and different shell thickness. (<b>b</b>) Photograph of solutions of CdSe/CdS core–shell nanocrystals with different core size and different shell thickness under normal indoor light without UV irradiation. Reprinted with permission from ref. [<a href="#B60-polymers-17-00233" class="html-bibr">60</a>]. Copyright 2005 Wiley. (<b>c</b>) Photographs under ambient room light (<b>top</b>) and UV light (<b>bottom</b>) showing effect of CdCl<sub>2</sub> treatment at increasing CdCl<sub>2</sub> concentrations on QD PL. Reprinted with permission from ref. [<a href="#B68-polymers-17-00233" class="html-bibr">68</a>]. Copyright 2018 American Chemical Society. (<b>d</b>) Cu:Mn-ZnSe-doped QD samples with different amounts of Cu precursors. Reprinted with permission from ref. [<a href="#B64-polymers-17-00233" class="html-bibr">64</a>]. Copyright 2011 Wiley. (<b>e</b>) Solutions of CQWs after different CE reaction times (10 to 60 min) under 365 nm UV light. (<b>f</b>) Normalized absorption and PL spectra of CdZnSe CQWs with respect to the CE reaction time. Reprinted with permission from ref. [<a href="#B66-polymers-17-00233" class="html-bibr">66</a>]. Copyright 2024 Wiley.</p>
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<p>Group III–V quantum dots. (<b>a</b>) The synthesis strategy of InP/Zn(Se,S)/ZnS featuring a core–shell–shell structure and the attainment of multiple emission colors through the adjustment of the composition of the inner shell. (<b>b</b>) Absorbance and emission spectra of InP/ZnSe/ZnS QDs. Reprinted with permission from ref. [<a href="#B80-polymers-17-00233" class="html-bibr">80</a>]. Copyright 2022 American Chemical Society. (<b>c</b>) Absorption spectra of alloyed In<sub>1−x</sub>GaxP cores and the large range of emission colors produced by core−shell In<sub>1−x</sub>GaxP/ZnS samples with varying gallium. (<b>d</b>) In<sub>1−x</sub>GaxP/ZnS emission spectra. Reprinted with permission from ref. [<a href="#B87-polymers-17-00233" class="html-bibr">87</a>]. Copyright 2023 American Chemical Society.</p>
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<p>Perovskite quantum dots (<b>a</b>) FAPbX<sub>3</sub> nanocrystals dispersed in toluene under UV irradiation (λpeak = 365 nm) and PL emission spectra of FAPbX<sub>3</sub> nanocrystals. (<b>b</b>) Corresponding color gamut of FAPbX<sub>3</sub> nanocrystals displayed on the CIE diagram. Reprinted with permission from ref. [<a href="#B93-polymers-17-00233" class="html-bibr">93</a>]. Copyright 2017 American Chemical Society. (<b>c</b>) Scheme of synthesized aqueous-based CsPbBr<sub>3</sub>/CsPb<sub>2</sub>Br<sub>5</sub> PQDs using vacancy inhibitors of PEG, forming a defect-free surface in water (OA refers to oleic acid, and OAm represents oleylamine). Reprinted with permission from ref. [<a href="#B91-polymers-17-00233" class="html-bibr">91</a>]. Copyright 2023 Wiley.</p>
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<p>(<b>a</b>) Schematic diagram of functions by encapsulation illustrated by CsPbX<sub>3</sub> QDs. Reprinted with permission from ref. [<a href="#B20-polymers-17-00233" class="html-bibr">20</a>]. Copyright 2019 Wiley. (<b>b</b>) Radar map of the advantages and disadvantages of three methods of combining QDs with polymers.</p>
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<p>(<b>a</b>) Flowchart of the dual-solvent assisted reprecipitation (DSAR) technique. (<b>b</b>) Photoluminescence spectra (the inset shows photoluminescence quantum yield). (<b>c</b>) Blue light stability test. (<b>d</b>) The 60 °C/90%RH stability test. (<b>e</b>) Color gamut of the fabricated devices using the Cs-DSAR and CsFA-DSAR PQDs. Reprinted with permission from ref. [<a href="#B38-polymers-17-00233" class="html-bibr">38</a>]. Copyright 2023 Elsevier.</p>
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<p>(<b>a</b>) Schematic illustration of the in situ fabrication of MAPbBr<sub>3</sub> NCs-embedded PVDF composite films. (<b>b</b>) Optical images under a UV lamp (365 nm) of color-tunable MAPbX<sub>3</sub>–PVDF composite films with different halogen constitutions on glass substrates. (<b>c</b>) Emission spectrum of the white LED using green emissive MAPbBr<sub>3</sub>–PVDF composite films and red emissive phosphor. (<b>d</b>) The color coordinate (star) and the white triangle (white line) of obtained white LED in CIE 1931 diagram. Reprinted with permission from ref. [<a href="#B32-polymers-17-00233" class="html-bibr">32</a>]. Copyright 2016 Wiley.</p>
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<p>(<b>a</b>) Schematic diagrams of the preparation procedure for yellow PQDF via melt extruding-rolling method. Photographs of the as-prepared PP-encapsulated CsPbX<sub>3</sub>@glass composite particles and the corresponding green and yellow PQDFs. (<b>b</b>) Photograph of yellow monolithic PQDF-based backlit unit and luminescent image of the backlit unit at an operating voltage of 12 V. (<b>c</b>) Schematic structure of an LCD prototype using yellow PQDF as a light converter. (<b>d</b>) Comparison of the display performance of a YAG-based LCD and PQDF-based LCD. (<b>e</b>) Color gamut of PQDF-based LCD (blue solid triangle), NSTC 1953 standard (black dashed triangle), and YAG-based commercial LCD (black solid triangle). Reprinted with permission from ref. [<a href="#B37-polymers-17-00233" class="html-bibr">37</a>]. Copyright 2024 Wiley.</p>
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<p>(<b>a</b>) Schematic structures of the growth of green and red QDs. (<b>b</b>) Light intensity spectra (solid line) and brightness (hatched area) of QD-LED (blue) and phosphor-LED (gray). Inset: color triangles of QD-LED (white) and phosphor-LED (yellow) compared to NTSC1931 (black). (<b>c</b>) Display image of a 46-inch LCD TV panel and a quarter of the white QD-LED backlights (inset). Reprinted with permission from ref. [<a href="#B43-polymers-17-00233" class="html-bibr">43</a>]. Copyright 2010 Wiley. (<b>d</b>) Schematic of syntheses of the ZnS modified green and red QRs. (<b>e</b>) The spectrum of the fabricated QRWLED consists of three emission band peaks at 450, 527, and 624 nm. (<b>f</b>) Schematic of a QRs on-chip backlight with dual-brightness-enhancement film (DBEF) design for displays. Reprinted with permission from ref. [<a href="#B44-polymers-17-00233" class="html-bibr">44</a>]. Copyright 2021 Wiley.</p>
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23 pages, 3584 KiB  
Review
Recent Advances of Colossal Magnetoresistance in Versatile La-Ca-Mn-O Material-Based Films
by Navjyoti Boora, Rafiq Ahmad, Shafaque Rahman, Nguyen Quoc Dung, Akil Ahmad, Mohammed B. Alshammari and Byeong-Il Lee
Magnetochemistry 2025, 11(1), 5; https://doi.org/10.3390/magnetochemistry11010005 - 16 Jan 2025
Viewed by 528
Abstract
Hole-doped manganese oxides exhibit a gigantic negative magnetoresistance, referred to as colossal magnetoresistance (CMR), owing to the interplay between double-exchange (DE) ferromagnetic metal and charge-ordered antiferromagnetic insulator/semiconductor phases. Magnetoresistive manganites display a sharp resistivity drop at the metal–insulator transition temperature (TMI). [...] Read more.
Hole-doped manganese oxides exhibit a gigantic negative magnetoresistance, referred to as colossal magnetoresistance (CMR), owing to the interplay between double-exchange (DE) ferromagnetic metal and charge-ordered antiferromagnetic insulator/semiconductor phases. Magnetoresistive manganites display a sharp resistivity drop at the metal–insulator transition temperature (TMI). CMR effects in perovskite manganites, specifically La0.67Ca0.33MnO3 (La-Ca-Mn-O or LCMO), have been extensively investigated. This review paper provides a comprehensive introduction to the crystallographic structure, as well as the electronic and magnetic properties, of LCMO films. Furthermore, we delve into a detailed discussion of the effects of epitaxial strain induced by different substrates on LCMO films. Additionally, we review the early findings and diverse applications of LCMO thin films. Finally, we outline potential challenges and prospects for achieving superior LCMO film properties. Full article
(This article belongs to the Special Issue Magnetic Materials, Thin Films and Nanostructures—2nd Edition)
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<p>A schematic of the cubic perovskite structure.</p>
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<p>Orbitals and energy levels of Mn<sup>4+</sup> and Mn<sup>3+</sup>.</p>
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<p>The crystal-field splitting of the 5-fold degenerate, split into lower t<sub>2g</sub> and higher eg levels.</p>
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<p>A schematic of the Zener pair.</p>
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<p>Schematic showing DE mechanism.</p>
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<p>Shows the maximum ferromagnetic transition around x = 0.33. Adapted from [<a href="#B21-magnetochemistry-11-00005" class="html-bibr">21</a>], copyright 2024, Elsevier.</p>
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<p>(<b>a</b>) A cross-sectional SEM image of the La<sub>0.8</sub>Ca<sub>0.2</sub>MnO<sub>3</sub>/LaAlO<sub>3</sub> film; (<b>b</b>) MR at an applied field of 1.5 T; (<b>c</b>) TCR values along the a–b plane and in the c direction [adapted from [<a href="#B88-magnetochemistry-11-00005" class="html-bibr">88</a>], copyright 2015, Elsevier]; (<b>d</b>) a TEM image; (<b>e</b>) the XRD of LCMO/MgO film; and (<b>f</b>) magnetization vs. temperature for LCMO film (inset shows the T<sub>C</sub> value) [adapted from [<a href="#B89-magnetochemistry-11-00005" class="html-bibr">89</a>], copyright 2020, Elsevier].</p>
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8 pages, 810 KiB  
Article
Getting to the Heart of the Matter: Control over the Photolysis of PbI2 Through Partial Lead Substitution
by Marina I. Ustinova, Gennadii V. Shilov, Pavel A. Troshin, Sergey M. Aldoshin and Lyubov A. Frolova
Inorganics 2025, 13(1), 13; https://doi.org/10.3390/inorganics13010013 - 6 Jan 2025
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Abstract
A crucial problem of the photoinduced degradation of perovskite semiconductors based on complex lead halides has been addressed here by suppressing PbI2 photolysis to metallic lead. The systematic screening of >30 modifying cations introduced as substituents for 5% of Pb2+ in [...] Read more.
A crucial problem of the photoinduced degradation of perovskite semiconductors based on complex lead halides has been addressed here by suppressing PbI2 photolysis to metallic lead. The systematic screening of >30 modifying cations introduced as substituents for 5% of Pb2+ in the PbI2 composition has revealed their tremendous effects on the rate of material degradation under light exposure. Thus, the most successful stabilizing cations could maintain a high absorbance of the Pb0.95M0.1/nI2 films and block Pb0 formation after 400 h of continuous illumination, when the non-modified PbI2 films completely decomposed to Pb0 and I2. The obtained results present a promising solution for the problem of metallic lead formation in the active layer of perovskite solar cells during their operation, which can pave the way for the development of a new generation of highly efficient and stable perovskite photovoltaics. Full article
(This article belongs to the Special Issue New Semiconductor Materials for Energy Conversion)
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<p>The evolution of the UV-Vis absorption spectra of PbI<sub>2</sub> (<b>a</b>) and Pb<sub>0.95</sub>Fe<sub>0.05</sub>I<sub>2</sub> (<b>b</b>) films upon white light exposure. The survey of the aging behavior of different Pb<sub>0.95</sub>M<sub>0.1/n</sub>I<sub>2</sub> films in terms of their normalized absorbance after 400 h of light exposure (<b>c</b>) and relative phase composition according to the XRD data (<b>d</b>).</p>
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<p>The photochemical aging dynamics of the selected Pb<sub>0.95</sub>M<sub>0.1/n</sub>I<sub>2</sub> films represented by the evolution of the normalized film absorbance as a function of the aging time (<b>a</b>). The dependencies corresponding to the first (<b>b</b>), second (<b>c</b>), and third (<b>d</b>)-order reaction kinetics are plotted in the corresponding linear coordinates.</p>
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12 pages, 3658 KiB  
Article
Buried Interface Smoothing Boosts the Mechanical Durability and Efficiency of Flexible Perovskite Solar Cells
by Erxin Zhao, Yongshuai Gong, Yixin Dong, Wanlei Dai, Chou Liu, Tinghuan Yang, Nan Wu, Ye Yang, Zheng Zhang, Chenqing Tian, Buyi Yan, Dongxue Liu, Lu Zhang and Tianqi Niu
Energies 2025, 18(1), 174; https://doi.org/10.3390/en18010174 - 3 Jan 2025
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Abstract
Flexible perovskite solar cells (F-PSCs) have the advantages of high power-per-weight, solution processability, and bending durability and have emerged as a competitive photovoltaic technology for various applications. As the core electron transport layer (ETL) in n-i-p-type device configurations, the solution-processed SnO2 generally [...] Read more.
Flexible perovskite solar cells (F-PSCs) have the advantages of high power-per-weight, solution processability, and bending durability and have emerged as a competitive photovoltaic technology for various applications. As the core electron transport layer (ETL) in n-i-p-type device configurations, the solution-processed SnO2 generally suffers from serious defect stacking on films, compromising the charge transport properties and the performance of resulting devices. Herein, we proposed a media-filling strategy to optimize the contact quality at the buried interface by introducing Al2O3 nanoparticles on the SnO2 surface. Rather than forming a compact insulating layer, the Al2O3 can fill the grain boundaries of SnO2 and smooth the substrate surface. Optimized interfacial contact under careful concentration control can rationally minimize the contact area of the perovskite with the surface imperfections of SnO2 to mitigate trap-assisted charge recombination. Furthermore, the reduced surface roughness of SnO2 facilitates the uniform deposition and oriented growth of upper perovskite film. As a result, the target F-PSCs achieved an impressive efficiency of 23.83% and retained 80% of the initial performance after 5000 bending cycles at a radius of four mm. Full article
(This article belongs to the Section A2: Solar Energy and Photovoltaic Systems)
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<p>(<b>a</b>,<b>d</b>) AFM topography of pristine SnO<sub>2</sub> and SnO<sub>2</sub>/Al<sub>2</sub>O<sub>3</sub> films. (<b>b</b>,<b>e</b>) SEM images of buried interface of perovskite films deposited on SnO<sub>2</sub> and SnO<sub>2</sub>/Al<sub>2</sub>O<sub>3</sub>. Schematic illustration showing crystal stacking modes of perovskite on the (<b>c</b>) SnO<sub>2</sub> and (<b>f</b>) SnO<sub>2</sub>/Al<sub>2</sub>O<sub>3</sub> substrates.</p>
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<p>(<b>a</b>) XRD patterns, (<b>b</b>) optical transmittance spectra, (<b>c</b>) electron mobility, and (<b>d</b>) conductivity tests of the SnO<sub>2</sub> films with and without Al<sub>2</sub>O<sub>3</sub> decoration.</p>
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<p>(<b>a</b>,<b>b</b>) AFM topography of (<b>a</b>) control and (<b>b</b>) target perovskite films, showing the average root-mean-square roughness (Ra). (<b>c</b>,<b>d</b>) Top-view SEM images of control and target films. (<b>e</b>,<b>f</b>) Statistical diagram of grain-size distribution of perovskite films. (<b>g</b>) XRD patterns of perovskite films. (<b>h</b>) Peak intensity and FWHM of the (100) plane of perovskite. (<b>i</b>) UV-vis absorption spectra.</p>
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<p>(<b>a</b>) Steady-state PL spectra, (<b>b</b>) PL lifetime in mapping images, (<b>c</b>) TRPL spectra for control and target perovskite films, dark <span class="html-italic">I</span>-<span class="html-italic">V</span> measurement of the electron-only device for (<b>d</b>) the control and (<b>e</b>) the target cases. (<b>f</b>) Mott–Schottky curves, (<b>g</b>) EIS measurement, (<b>h</b>) dark <span class="html-italic">J</span>-<span class="html-italic">V</span> characteristics of control and target devices.</p>
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<p>(<b>a</b>) <span class="html-italic">J</span>-<span class="html-italic">V</span> curves of the best-performing devices at different Al<sub>2</sub>O<sub>3</sub> concentrations, (<b>b</b>) EQE curves and the corresponding integrated current density of the control and target devices. Statistical charts of (<b>c</b>) <span class="html-italic">V</span><sub>OC</sub>, (<b>d</b>) <span class="html-italic">FF</span>, (<b>e</b>) PCE, and (<b>f</b>) <span class="html-italic">J</span><sub>SC</sub> (20 devices for each condition), (<b>g</b>) the environmental stability, (<b>h</b>) bending cycle stability for control and target F-PSCs.</p>
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