Register Login 切换中文 中国高分子学术平台
RESEARCH ARTICLE | Updated:2024-08-06
    • Simplified p-i-n Perovskite Solar Cells with a Multifunctional Polyfullerene Electron Transporter

    • Wang Fei-Fei

      ,  

      Liu Tian-Xiao

      ,  

      Cui Ze-Wei

      ,  

      Wang Ling-Yuan

      ,  

      Dou Yun-Jie

      ,  

      Shi Xiao-Yu

      ,  

      Luo Si-Wei

      ,  

      Hu Xiao-Dong

      ,  

      Ren Zhi-Jun

      ,  

      Liu Yang-Yang

      ,  

      Zhao Yu

      ,  

      Chen Shang-Shang

      ,  
    • Chinese Journal of Polymer Science   Vol. 42, Issue 8, Pages: 1060-1066(2024)
    • DOI:10.1007/s10118-024-3156-y    

      CLC:
    • Published:01 August 2024

      Published Online:26 June 2024

      Received:12 March 2024

      Revised:24 April 2024

      Accepted:04 May 2024

    Scan for full text

  • Cite this article

    PDF

  • Fei-Fei Wang, Tian-Xiao Liu, Ze-Wei Cui, et al. Simplified p-i-n Perovskite Solar Cells with a Multifunctional Polyfullerene Electron Transporter. [J]. Chinese Journal of Polymer Science 42(8):1060-1066(2024) DOI: 10.1007/s10118-024-3156-y.

  •  
  •  
    Sections

    Abstract

    In prevailing p-i-n perovskite solar cells (PSCs), solution-processible fullerene molecules are widely used as electron-transporting layers (ETLs) but they typically suffer from poor uniformity and undesirable stability issues. Additionally, a separate bathocuproine (BCP) layer is needed to block hole transfer, increasing fabrication complexity and cost. Here, we address these limitations by developing a novel polymeric ETL (named PFBCP) synthesized by polymerizing C60 with BCP. This innovative material achieves both efficient electron transport and hole blocking, while its excellent uniformity minimizes interface recombination and enhances stability. Consequently, our blade-coated PSCs utilizing PFBCP achieve a high power conversion efficiency exceeding 22% and retain 91% of initial efficiency after 1200 h of light exposure. This development not only paves the way for commercially viable PSCs but also opens avenues for future ETL design to realize even more efficient and stable PSCs.

    transl

    Keywords

    Polyfullerene; Perovskite solar cells; Electron transporter; Stability

    transl

    INTRODUCTION

    Inverted or p-i-n perovskite solar cells (PSCs) are more promising for commercialization due to their low cost, low-temperature processibility, better stability, and compatibility with silicon photovoltaics for tandem cells compared with their n-i-p counterparts.[

    1−7] In a typical p-i-n PSC, hole-transporting layers (HTLs) like poly(3,4-ethylenedioxythiophene)-poly(styrenesulfonate) (PEDOT:PSS), poly[bis(4-phenyl)(2,4,6-trimethylphenyl)amine] (PTAA), or carbozole-based self-assembled monolayers are first deposited on the top of indium tin oxide (ITO) glass substrates.[8] After the fabrication of perovskite films on the top of HTLs, electron-transporting layers (ETLs) like C60 or PCBM are deposited via thermal evaporation or solution methods to extract electrons.[9−11] However, different from n-i-p structured PSCs in which a perovskite film is sandwiched between an ETL and an HTL prior to the deposition of metal electrodes, a separate bathocuproine (BCP) layer is an indispensable component to improve the fill factors (FFs) of p-i-n PSCs because the highest occupied molecular orbital (HOMO) levels of conventional fullerene ETLs are not deep enough to block hole transfers.[1,12] In this case, the involvement of another hole-blocking layer, on the one hand, complicates the fabrication procedures and increases the production cost; on the other hand, it was found that the crystallization of BCP molecules at elevated temperatures causes the burn-in loss and the degradation of the PSCs.[13] Therefore, it is essential to develop low-cost and high-performance ETLs that can be fabricated with a simple procedure and address the aforementioned issues of current fullerene/BCP ETLs.
    transl

    In 2022, our group reported the first polyfullerene-type ETL for p-i-n PSCs that exhibits not only excellent electron-transporting capacities but also good stability, and realizes high-performance p-i-n PSCs and perovskite mini-modules.[

    14] Most importantly, the polymerization between fullerene monomers and various linkers enables us to facilely functionalize the resultant polyfullerenes without tedious purification of conventional molecular fullerene derivatives. In this work, we develop a new polyfullerene-type ETL by polymerizing BCP units with C60 moieties (Fig. 1 and Scheme 1). The resultant polyfullerene ETL (named PFBCP) not only efficiently extracts electrons generated in perovskite films, but also effectively blocks hole transfer to cathode electrodes. As a result, the p-i-n PSCs based on a single PFBCP ETL realized an impressive power conversion efficiency (PCE) of 22.3%, outperforming the cells based on PCBM/BCP double layers. Meanwhile, the polymeric PFBCP ETL exhibits reduced aggregation and improved uniformity compared to conventional fullerene molecules, which significantly improves cell operational stability. The PSCs based on PFBCP can retain 91% of the initial PCE after 1200 h of light soaking. Our work reports the first polyfullerene ETL that can both transport electrons and block holes, which simplifies the fabrication procedures and facilitates the commercialization of perovskite photovoltaics.
    transl

    fig

    Fig 1  Schematic illustration of simplified PSC structure by replacing conventional PCBM/BCP with a new polyfullerene ETL named PFBCP.

    icon Download:  Full-size image | High-res image | Low-res image

    EXPERIMENTAL

    Materials

    PTAA (average Mn 7×103−1×104), BCP, lead iodide (PbI2, 99.999% trace metals), dimethyl sulfoxide (DMSO), L-α-phosphatidylcholine (LP), benzylhydrazine hydrochloride, 2-methoxyethanol (2-ME), and toluene were purchased from Sigma-Aldrich and used without further purification. C60 and PCBM were purchased from Nanjing Zhiyan Inc. Methylammonium iodide (MAI), formamidinium iodide (FAI), 4-fluoro-phenyethylammonium iodide (p-F-PEAI) and n-dodecylammonium iodide were purchased from GreatCell Solar. All chemicals without any notes were commercially available and used without further purification.

    transl

    Synthesis of PFBCP

    fig

    Fig 1  Synthetic route to PFBCP.

    icon Download:  Full-size image | High-res image | Low-res image

    Compound 3

    In a 100 mL round bottom flask, compound 1 (2.87 g, 3 equiv.), compound 2 (0.5 g, 1 equiv.), K2CO3 (1.25 g, 5 equiv.), and tetrakis(triphenylphosphine)palladium(0) (208 mg, 10 mol %) were added into THF:H2O (10 mL:2 mL, 5:1), and the mixture was heated at 80 °C for 24 h under nitrogen. After completion of the reaction, the resulting suspension was cooled to room temperature, and extracted in brine and DCM. The organic fraction was evaporated under reduced pressure. The residue was directly purified by silica gel chromatography (DCM:MeOH=50:1, V:V), and the product is a colorless viscous liquid, giving the final compound 3 with 60% (1.0 g) yield. 1H-NMR (400 MHz, CDCl3, δ, ppm): 7.77 (s, 1H), 7.49–7.41 (m, 2H), 7.08 (ddd, J=7.5, 3.5, 1.5 Hz, 1H), 7.00 (d, J=1.6 Hz, 1H), 4.80 (d, J=5.5 Hz, 2H), 3.94 (dd, J=8.7, 5.3 Hz, 2H), 2.99 (d, J=7.4 Hz, 3H), 1.86–1.78 (m, 1H), 1.49–1.21 (m, 35H), 0.91–0.83 (m, 6H). 13C-NMR (101 MHz, CDCl3, δ, ppm): 159.31, 158.78, 157.11, 148.48, 145.96, 138.97, 129.34, 128.49, 124.70, 124.31, 123.87, 122.99, 121.81, 120.86, 112.25, 70.97, 61.98, 53.42, 50.87, 38.08, 31.90, 31.87, 31.58, 29.99, 29.67, 29.61, 29.55, 29.33, 26.92, 25.97, 25.78, 22.68, 14.10. MALDI-TOF-MS (SA matrix) m/z: [M]+ calcd. for C64H105N2O4 1013.80; found 1013.80.

    transl

    Compound 4

    In a 100 mL round bottom flask, compound 3 (500 mg, 1 equiv.) and DCM (3 mL) were added, then 33% HBr·AcOH (495 mg, 2.5 equiv.) was added dropwise at 0 °C. After 30-min stirring, the color changed to a pale yellow. Monitoring with TLC (2% MeOH/DCM) showed a complete disappearance of the starting materials. The reaction mixture was diluted with DCM (50 mL), and the organic layer was washed with H2O (3 × 15 mL) and saturated brine (15 mL). The organic layer was dried over anhydrous MgSO4, and the solvent was removed under reduced pressure to give compound 4 as a yellow oil (225 mg, 40%). 1H-NMR (400 MHz, CDCl3, δ, ppm): 7.78 (s, 1H), 7.51–7.43 (m, 2H), 7.09–7.03 (m, 1H), 6.99 (dd, J=4.3, 1.6 Hz, 1H), 4.74 (s, 0H), 4.64 (s, 1H), 3.94 (d, J=5.2 Hz, 1H), 3.00 (s, 2H), 1.84 (h, J=5.9 Hz, 1H), 1.57–1.20 (m, 32H), 0.86 (td, J = 6.9, 2.1 Hz, 5H). 13C-NMR (101 MHz, CDCl3, δ, ppm): 158.86, 157.20, 157.10, 148.22, 145.95, 140.20, 130.77, 130.42, 126.36, 124.58, 123.82, 123.01, 121.69, 112.76, 112.67, 70.99, 64.88, 53.42, 41.36, 38.14, 38.11, 31.91, 31.89, 31.48, 30.01, 29.69, 29.63, 29.58, 29.34, 28.50, 26.95, 26.93, 26.02, 22.68, 14.11. MALDI-TOF-MS (SA matrix) m/z: [M]+ calcd. for C68H103Br2N2O4 1139.64; found 1139.64.

    transl

    PFBCP

    Extra dry 1,2-dichlorobenzene (15 mL), C60 (50 mg, 1 equiv.), CuBr (20 mg, 2 equiv.) and 2,2’-bipyridine (43 mg, 4 equiv.) were added into a flame-dried, N2-flushed flask and stirred at room temperature for 2 h. On confirmation of the solvation of C60, compound 4 (79 mg, 1 equiv.) was added and the mixture was stirred at 120 °C for 24 h. After cooling to room temperature, the 1,2-dichlorobenzene solvent was removed under vacuum distillation. The solid deposit was dissolved in a minimum of 1,2-dichlorobenzene, precipitated by addition to methanol, and recovered by filtration in a cellulose tube ready for Soxhlet extraction with acetone (2 days) and n-hexane (2 days). The polymer was dried under reduced pressure to a brown powder (47 mg, yield 40%). The molecular weight of PFBCP was determined with an Agilent GPC instrument with THF as the eluent (Mn: 2.8×104).

    transl

    Device Fabrication

    Patterned ITO glass substrates (1.5 cm × 1.5 cm) were first cleaned by ultrasonication with soap, deionized water and isopropyl alcohol, and then UV-ozone treated for 15 min before use. All perovskite solar devices were prepared by blade-coating at room temperature inside a fume hood with a relative humidity of 40%±10%. The PTAA solution at a concentration of 3.3 mg·mL−1 dissolved in toluene was blade-coated onto ITO glass substrates at a speed of 20 mm·s−1. The gap between blade-coater and ITO substrates was 150 μm. 1.35 mol/L MA0.7FA0.3PbI3 precursor solution was prepared by dissolving corresponding organic halide salts and lead iodide into 2-ME in a N2-filled glovebox with an O2 level <10 ppm. 0.83 mg·mL−1 n-dodecylammonium iodide, 0.27 mg·mL−1 LP, 0.14 vol% MAH2PO2, 1.40 mg ml−1 p-F-PEAI, 0.15 mg·mL−1 benzylhydrazine hydrochloride, 2.8 vol% DMSO were added as additives before blade-coating. Subsequently, the precursor solution was blade-coated onto the PTAA-covered ITO glass substrates with a gap of 250 μm at a movement speed of 20 mm·s−1. The air knife worked at 20 psi during blade-coating. After that, the perovskite films were annealed at 120 °C for 10 min in air. The filtered PCBM or PFBCP ETL solutions (20 mg·mL−1 in 1,2-dichlorobenzene) were coated onto perovskite layers at a speed of 20 mm·s−1. The optimal thickness of ETLs is around 30 nm. For PCBM-based PSCs, a thin layer of BCP (5 nm) was evaporated on the top of PCBM (0.1 Å·s−1). The solar cells were completed by thermally evaporating 100 nm copper (1 Å·s−1).

    transl

    Characterization

    1H-NMR and 13C-NMR spectra were obtained on a 400 MHz Bruker AVANCE III-400 spectrometer. High-resolution mass spectrometry (HRMS) was done on a Bruker Daltonics MALDI TOF UltrafleXtreme. Thermogravimetric analysis (TGA) was conducted using a Netzsch STA449F3 thermogravimetric-differential scanning calorimetric thermal synchronous analyzer. The sample was heated from 30 °C to 600 °C at a heating rate of 10 °C·min−1 under a nitrogen atmosphere. UV-Vis absorption spectra were obtained with a Shanghai Metash UV-8000 spectrometer. Cyclic voltammetry was carried out on a ZAHNER IM6EX electrochemical workstation with a three-electrode configuration, using Ag/AgCl as the reference electrode, a Pt plate as the counter electrode, and a glassy carbon as the working electrode. The ETL solutions were drop-cast onto the electrodes to form thin films. 0.1 mol·L−1 tetrabutylammonium hexafluorophosphate in anhydrous acetonitrile was used as the supporting electrolyte. Potentials were referenced to the ferrocenium/ferrocene couple by using ferrocene as external standards in acetonitrile solutions. The scan rate is 0.1 V·s−1. Both steady-state PL and TRPL spectra were acquired on a HORIBA FL-3 fluorescence spectrophotometer at room temperature. The excitation wavelengths were 480 nm and 405 nm for PL and TRPL measurements, respectively. The TRPL curves were fitted with a bi-exponential formula:

    transl

    y=y0+A1exp((xx0)/t1)+A2exp((xx0)/t2)(t2>t1)math 1

    where the t1 values of the two systems were found to be comparable (Table S1 in the electronic supplementary information, ESI), and here we used t2 to represent the lifetime of the films.

    transl

    Atomic force microscopy (AFM) images were scanned from a Bruker Icon Atomic Force Microscope. Scanning electron microscopy (SEM) images were taken on TESCAN MIRA3 LMH operating at 5.0 kV. The J-V characteristics of solar cells were performed using an LED solar simulator (BG-LED3A-100S, Class AAA Solar Simulator) and the power of the simulated light was calibrated to 100 mW·cm−2 by a silicon reference cell (Newport 91150V). A metal mask with an aperture (6.8 mm2) aligned with the device area was used for measurements. All devices were measured using a Keithley 2400 source meter with a backward scan rate of 0.1 V·s−1 in air at room temperature, and the delay time was 10 ms. There was no preconditioning before measurement. The PSCs were encapsulated with cover glass sealed by an epoxy encapsulant on the back. After curing, the stability of encapsulated cells was monitored with a 91 PVKSOLAR MSCLT-1 automatic maximum power point (MPP) tracker. After connecting the PSCs to the MPP tracker, the cells kept working at MPP conditions under simulated AM 1.5G one sun illumination (100 mW·cm−2) in air (relative humidity: 40%±10%). The stabilized PCEs were recorded every 5 s. No fan or cooler was used to control the cell temperature, and the temperature of the cells was measured to be about 40 °C.

    transl

    The electron mobilities were measured using the space-charge-limited-current (SCLC) method, employing a device architecture of glass/ITO/ZnO/ETL/PDINN/Ag. The mobilities were obtained by taking current-voltage curves and fitting the results to a space charge limited form, where the SCLC is described by:

    transl

    J=9ϵ0ϵrμ(VapplVbiVs)8L3math 2

    where ε0 is the permittivity of free space, εr is the relative permittivity of the material (assumed to be 3), μ is the electron mobility, Vappl is the applied voltage, Vbi is the built-in voltage (0.7 V), Vs is the voltage drop from the substrate’s series resistance (Vs = IR, R is measured to be 10.8 Ω) and L is the thickness of the film. By linearly fitting J1/2 with Vappl-VbiVs, the mobilities were extracted from the slope and L:

    transl

    μ=Slope28L39ϵ0ϵrmath 3

    tDOS spectra were obtained with an Agilent E4980A precision LC meter. The energetic profile of tDOS was derived from the angular frequency dependent capacitance using the equation:

    transl

    NT(Eω)=1qkBTωdCdωVbiWmath 4

    where C is capacitance, ω is the angular frequency, q is the elementary charge, kB is the Boltzmann’s constant and T is the temperature. Vbi and W are the built-in potential and depletion width, respectively, which were extracted from the Mott-Schottky analysis. The applied angular frequency ω defines an energetic demarcation,

    transl

    Eω=kTln(ω0ω)math 5

    where ω0 is the attempt-to-escape angular frequency (ω0 = 2πν0, ν0=1×109 Hz). The trap states below the energy demarcation can capture or emit charges with the give ω and contribute to the capacitance.

    transl

    RESULTS AND DISCUSSION

    PFBCP exhibits good solubility in common organic solvents like chlorobenzene and 1,2-dichlorobenzene, making it suitable for solution processing as the ETL of p-i-n PSCs. PFBCP also shows good thermal stability with a decomposition temperature (5% mass loss) of over 360 oC (Fig. S1 in ESI). The UV-Vis absorption spectra of PFBCP and PCBM thin films are depicted in Fig. 2(a). PFBCP film shows an absorption maxima at 340 nm, which is the typical absorption peak of fullerene derivatives.[

    15] Compared to PCBM film, PFBCP shows a broader and red-shifted absorption profile, and the optical band gap (Eg) of PFBCP was estimated to be 2.36 eV from the onset in the film spectra. Cyclic voltammetry (CV) was employed to investigate the energy levels of PFBCP. As shown in Fig. 2(b). The lowest unoccupied molecular orbital (LUMO)/HOMO levels of PFBCP were estimated to be −3.62 eV/−5.98 eV. Electron mobility is one of the figure-of-merits for an ETL, and electron mobilities of both PCBM and PFBCP were investigated by using the SCLC method. As shown in Fig. S2 (in ESI), PFBCP possesses a comparable electron mobility of 4.1×10−4 cm2·V−1·s−1 to that of PCBM (2.9×10−4 cm2·V−1·s−1). These results verify that the fullerene polymerization strategy has no detrimental effects on the electron mobility of the resulting polyfullerene. Subsequently, we employed steady-state photoluminescence (PL) and time-resolved photoluminescence (TRPL) spectroscopy to characterize the fluorescence quenching efficiency and lifetime change after the deposition of the ETL on perovskite films.[16] As shown in Fig. 2(c), when excited at 480 nm, the PL of perovskite thin film undergoes significant quenching upon the deposition of the ETLs, and PFBCP-coated perovskite exhibited a higher PL quenching efficiency of 96.2% than that based on PCBM (80.3%). The higher quenching efficiency indicates a more effective electron transport from perovskite to PFBCP.[17] In addition, the bare perovskite film exhibits a PL decay time of approximately 793 ns (Fig. 2d, Fig. S3 and Table S1 in ESI), and it rapidly decayed to 336 and 131 ns when coated with PCBM and PFBCP, respectively. These observations confirm the effectiveness of PFBCP in extracting electrons generated in perovskite films, demonstrating the great potential of PFBCP as an ETL in p-i-n PSCs.
    transl

    fig

    Fig 2  (a) UV-Vis absorption spectra of PCBM and PFBCP thin films; (b) CV curve of PFBCP film; (c) Steady-state PL and (d) TRPL curves of the bare, PCBM- and PFBCP-coated perovskite films.

    icon Download:  Full-size image | High-res image | Low-res image

    Perovskite film surface morphology was investigated using AFM and SEM before and after the deposition of ETLs. AFM height image (Fig. 3a) revealed that bare perovskite film showed a root mean square (RMS) roughness of 7.43 nm. PCBM deposition (Fig. 3b) decreased film uniformity and increased roughness to 11.8 nm. Conversely, PFBCP deposition (Fig. 3c) led to a significantly smoother film (RMS roughness of 5.45 nm) with improved uniformity. Consistent with the AFM results, SEM images (Figs. 3d−3f) showed a smoother top surface and the absence of aggregation or pinholes for the PFBCP-coated film. These findings suggest a more conformal coating of PFBCP on the perovskite surface, potentially enhancing electron transport and inhibiting reactions between the perovskite and metal electrode.[

    11]
    transl

    fig

    Fig 3  AFM height (first row) and top-view SEM (second row) images of (a, d) bare, (b, e) PCBM-, and (c, f) PFBCP-coated perovskite films.

    icon Download:  Full-size image | High-res image | Low-res image

    We evaluated the photovoltaic performance of PFBCP as an ETL in inverted planar PSCs. The PSCs employed a glass/indium tin oxide (ITO)/PTAA/MA0.7FA0.3PbI3/ETL/copper (Cu) architecture, with both perovskite layers and the HTL/ETL deposited via blade-coating under ambient conditions.[

    7,18,19] The PFBCP-based PSC achieved an impressive PCE of 22.3%, exceeding the control device (PCE of 20.1%) based on PCBM (solution-processed)/BCP (thermally evaporated) (Fig. 4a). The average PCEs for PCBM and PFBCP cells were 18.8%±0.8% and 21.8%±0.3%, respectively (Fig. S4 and Table S2 in ESI). This PCE improvement stemmed from several factors in the PFBCP device: a higher open-circuit voltage (VOC) of 1.15 V (compared to 1.10 V for the control cell), a slightly higher short-circuit current density (JSC) of 25.5 mA·cm−2 (versus 24.9 mA·cm−2), and an improved FF of 0.759 (versus 0.731). The enhanced VOC likely results from reduced recombination and more efficient charge collection due to PFBCP's conformal film formation on the perovskite. Furthermore, the EQE spectra (Fig. 4b) confirm more efficient photon-to-current conversion across the 400−750 nm range for the PFBCP device, with a higher integrated photocurrent of 24.0 mA·cm−2, which aligns with the PL results indicating superior electron extraction by PFBCP. The improved FF of PFBCP-based cells confirms that the BCP moieties in PFBCP can block the hole transfer and facilitate the charge extraction before recombination.
    transl

    fig

    Fig 4  (a) J-V characteristic curves, (b) EQE plots, (c) tDOS spectra, and (d) long-term stability testing results (MPP condition under simulated AM 1.5G illumination of 100 mW·cm−2) of the PSCs based on PCBM/BCP and PFBCP.

    icon Download:  Full-size image | High-res image | Low-res image

    Thermal admittance spectroscopy (TAS) technique was then leveraged to investigate the trap density of states (tDOS) of the p-i-n PSCs.[

    20] The tDOS spectra in Fig. 4(c) confirmed a significantly reduced trap density of states (tDOS) within the trap depth of 0.10−0.20 eV for the PFBCP-based PSC compared to PCBM devices. This lower trap density explains the improved VOC observed in the PFBCP cell. Furthermore, the encapsulated PFBCP device under simulated AM 1.5G illumination (100 mW·cm−2) and air exposure (40±10% RH, 40 °C) demonstrated superior stability. As shown in Fig. 4(d), the PFBCP device retained 91% of its initial PCE after 1200 h of MPP tracking, while the PCBM device degraded below 80% after 500 h. This enhanced stability likely stems from the more conformal film formation and polymer chain entanglement of PFBCP, which effectively hinders reactions between the perovskite and metal electrodes and suppresses fullerene aggregation.[14] Based on the device characterization results above, it can be well concluded that the single PFBCP ETL delivers exceptional photovoltaic performance within a simplified p-i-n PSC architecture.
    transl

    CONCLUSIONS

    We report a new multifunctional ETL for p-i-n PSCs that simplifies device structure and enhances device performance. This ETL, named PFBCP, is solution-processible and combines efficient electron extraction with effective hole blocking in a single layer. Compared to conventional PCBM ETL, PFBCP offers superior film uniformity and coverage, leading to reduced recombination and lower trap density. Consequently, PSCs fabricated using blade-coating with PFBCP achieved a remarkable PCE of 22.3%, exceeding PCBM-based devices. Moreover, these PSCs retained an impressive 91% of their initial PCE after 1200 h of light soaking. This work presents a novel strategy for achieving high-performance PSCs with a simplified structure, paving the way for lower-cost manufacturing of perovskite solar technology.

    transl

    References

    1

    Jeng, J. Y.; Chiang, Y. F.; Lee, M. H.; Peng, S. R.; Guo, T. F.; Chen, P.; Wen, T. C. CH3NH3PbI3perovskite/fullerene planar-heterojunction hybrid solar cells.Adv. Mater.2013,25, 3727−3732.. [Baidu Scholar] 

    2

    Zhu, R. Inverted devices are catching up.Nat. Energy2020,5, 123−124.. [Baidu Scholar] 

    3

    Liu, T.; Chen, K.; Hu, Q.; Zhu, R.; Gong, Q. Inverted perovskite solar cells: progresses and perspectives.Adv. Energy Mater.2016,6, 1600457.. [Baidu Scholar] 

    4

    Zhu, P.; Chen, C.; Dai, J.; Zhang, Y.; Mao, R.; Chen, S.; Huang, J.; Zhu, J. Toward the commercialization of perovskite solar modules.Adv. Mater. 2024 , 2307357.. [Baidu Scholar] 

    5

    Li, Z.; Sun, X.; Zheng, X.; Li, B.; Gao, D.; Zhang, S.; Wu, X.; Li, S.; Gong, J.; Luther, J. M.; Li, Z. A.; Zhu, Z. Stabilized hole-selective layer for high-performance inverted p-i-n perovskite solar cells.Science2023,382, 284−289.. [Baidu Scholar] 

    6

    Bu, T.; Li, J.; Li, H.; Tian, C.; Su, J.; Tong, G.; Ono, L. K.; Wang, C.; Lin, Z.; Chai, N.; Zhang, X.-L.; Chang, J.; Lu, J.; Zhong, J.; Huang, W.; Qi, Y.; Cheng, Y. B.; Huang, F. Lead halide-templated crystallization of methylamine-free perovskite for efficient photovoltaic modules.Science2021,372, 1327−1332.. [Baidu Scholar] 

    7

    Chen, S.; Dai, X.; Xu, S.; Jiao, H.; Zhao, L.; Huang, J. Stabilizing perovskite-substrate interfaces for high-performance perovskite modules.Science2021,373, 902−907.. [Baidu Scholar] 

    8

    Duan, Y.; Chen, Y.; Wu, Y.; Liu, Z.; Liu, S.; Peng, Q. A comprehensive review of organic hole-transporting materials for highly efficient and stable inverted perovskite solar cells.Adv. Funct. Mater. 2024 , 2315604.. [Baidu Scholar] 

    9

    Zahran, R.; Hawash, Z. Fullerene-based inverted perovskite solar cell: a key to achieve promising, stable, and efficient photovoltaics.Adv. Mater. Interfaces2022,9, 2201438.. [Baidu Scholar] 

    10

    Jia, L.; Chen, M.; Yang, S. Functionalization of fullerene materials toward applications in perovskite solar cells.Mater. Chem. Front.2020,4, 2256−2282.. [Baidu Scholar] 

    11

    Fang, Y.; Bi, C.; Wang, D.; Huang, J. The functions of fullerenes in hybrid perovskite solar cells.ACS Energy Lett.2017,2, 782−794.. [Baidu Scholar] 

    12

    Chen, C.; Zhang, S.; Wu, S.; Zhang, W.; Zhu, H.; Xiong, Z.; Zhang, Y.; Chen, W. Effect of BCP buffer layer on eliminating charge accumulation for high performance of inverted perovskite solar cells.RSC Adv.2017,7, 35819−35826.. [Baidu Scholar] 

    13

    Deng, Y.; Xu, S.; Chen, S.; Xiao, X.; Zhao, J.; Huang, J. Defect compensation in formamidinium-caesium perovskites for highly efficient solar mini-modules with improved photostability.Nat. Energy2021,6, 633−641.. [Baidu Scholar] 

    14

    Yin, J.; Shi, X.; Wang, L.; Yan, H.; Chen, S. High-performance inverted perovskite solar devices enabled by a polyfullerene electron transporting material.Angew. Chem. Int. Ed.2022,61, e202210610.. [Baidu Scholar] 

    15

    Qaiser, D.; Khan, M. S.; Singh, R. D.; Khan, Z. H. Comparative study of optical parameters of fullerene C60film at different temperatures.Optics Commun.2010,283, 3437−3440.. [Baidu Scholar] 

    16

    Campanari, V.; Martelli, F.; Agresti, A.; Pescetelli, S.; Nia, N. Y.; Di Giacomo, F.; Catone, D.; O'Keeffe, P.; Turchini, S.; Yang, B.; Suo, J.; Hagfeldt, A.; Di Carlo, A. Reevaluation of photoluminescence intensity as an indicator of efficiency in perovskite solar cells.Solar RRL2022,6, 2200049.. [Baidu Scholar] 

    17

    Zhu, Z.; Chueh, C. C.; Lin, F.; Jen, A. K. Y. Enhanced ambient stability of efficient perovskite solar cells by employing a modified fullerene cathode interlayer.Adv. Sci.2016,3, 1600027.. [Baidu Scholar] 

    18

    Chen, S.; Xiao, X.; Gu, H.; Huang, J. Iodine reduction for reproducible and high-performance perovskite solarcells and modules.Sci. Adv.2021,7, eabe8130.. [Baidu Scholar] 

    19

    Ren, Z.; Cui, Z.; Shi, X.; Wang, L.; Dou, Y.; Wang, F.; Lin, H.; Yan, H.; Chen, S. Poly(carbazole phosphonic acid) as a versatile hole-transporting material for p-i-n perovskite solar cells and modules.Joule2023,7, 2894−2904.. [Baidu Scholar] 

    20

    Shao, Y.; Xiao, Z.; Bi, C.; Yuan, Y.; Huang, J. Origin and elimination of photocurrent hysteresis by fullerene passivation in CH3NH3PbI3planar heterojunction solar cells.Nat. Commun.2014,5, 5784−5790.. [Baidu Scholar] 

    0

    Views

    85

    Downloads

    0

    CSCD

    Alert me when the article has been cited
    Submit
    Tools
    Download
    Export Citation
    Share
    Add to favorites
    Add to my album

    Related Articles

    Inkjet-Printed Organic Solar Cells and Perovskite Solar Cells: Progress, Challenges, and Prospect
    UV-triggered Polymerization of Polyelectrolyte Composite Coating with Pore Formation and Lubricant Infusion
    Solution-processed Molybdenum Oxide Hole Transport Layer Stabilizes Organic Solar Cells

    Related Author

    Xing-Ze Chen
    Qun Luo
    Chang-Qi Ma
    Jia-Qi Hu
    Wei-Pin Huang
    Jing Wang
    Ke-Feng Ren
    Jian Ji

    Related Institution

    Lab & Printable Electronics Research Center, Suzhou Institute of Nano-Tech and Nano-Bionics, Chinese Academy of Sciences, Suzhou
    School of Nano-Tech and Nano-Bionics, University of Science and Technology of China
    MOE Key Laboratory of Macromolecular Synthesis and Functionalization, International Research Center for X Polymers, Department of Polymer Science and Engineering, Zhejiang University
    School of Chemistry, Beihang University
    CAS Key Laboratory of Nanosystem and Hierarchical Fabrication, National Center for Nanoscience and Technology
    0