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Progress in Chemistry 2020, Vol. 32 Issue (1): 119-132 DOI: 10.7536/PC190603 Previous Articles   Next Articles

Interface Passivation Strategy: Improving the Stability of Perovskite Solar Cells

Lei Wang1,2, Qin Zhou1,2, Yuqiong Huang1,2, Bao Zhang1,**(), Yaqing Feng1,2   

  1. 1. School of Chemical Engineering and Technology, Tianjin University, Tianjin 300350, China
    2. Collaborative Innovation Center of Chemical Science and Engineering, Tianjin 300072, China
  • Received: Online: Published:
  • Contact: Bao Zhang
  • About author:
    ** E-mail:
  • Supported by:
    National Key R&D Program of China(2016YFE0114900); National Natural Science Foundation of China(21761132007)
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In recent years, the emerging organic and inorganic hybrid perovskite solar cells have made rapid progress. In just ten years, its photoelectric conversion efficiency has rapidly developed from 3.8% to the current certified efficiency of 25.2%, which is regarded as one of the most potential solar cells. Although perovskite solar cells have high photoelectric conversion efficiency comparable to polysilicon thin film cells, the long-term stability of the cells remains a major challenge hindering their commercialization. There are many defects on the surface and grain boundary of perovskite. Interface passivation is an important and effective strategy to improve the stability of perovskite solar cells. Two-dimensional perovskite materials are organic amine and inorganic layer alternate layered perovskite, with bulky organic ammonium cations. Compared with the traditional three-dimensional perovskite materials, the stability for the environment is good, with the flexible and adjustable structure. The 3D perovskite’s surface is modified by a two-dimensional perovskite to passivate defects, ensuring the stability and at the same time improving the efficiency of perovskite solar cells. In addition, suitable passivation agent molecules can also passivate defects effectively. This paper reviews the unstable factors of perovskite solar cells, summarizes the research progress in interface passivation of perovskite solar cell, points out the great potential of two-dimensional perovskite materials’ development and the principle of finding suitable passivation agent molecules, which is expected to provide useful guidance for obtaining high-performance perovskite solar cells and realizing commercialization.

Key words: perovskite solar cell, stability, interface passivation
Fig. 1 (a) Illustration of the 3D hybrid perovskite structure ABX3, showing the corner-sharing [BX6]4- octahedra (A is an organic cation, B is a metal cation and X is a halide); (b) Upon exposure to moisture, UV light or heat, 3D perovskites decompose into either the precursor materials or a 0D hydrated phase; (c) Illustration showing the degradation processes initiated by infiltration of O2 through the grains in a 3D perovskite[23] (Reproduced with permission from ref 23)
Fig. 2 Typical structures of the 2D layered hybrid organic-inorganic perovskite for n=1 with double (a) and single (b) intercalated organic molecule layer[52] (Reproduced with permission from ref 52)
Fig. 3 Illustration showing that 2D perovskites is used as dopant to passivate the crystal grain boundaries of 3D perovskites[24] (Reproduced with permission from ref 24)
Fig. 4 Schematic figure of (a) the perovskite film treated by BA to form a 2D/3D stacking structure and (b,c) 2D/3D molecular junctions on the surface and at grain boundaries of 3D perovskite films induced by BA and BAI treatments, respectively; SEM images of (d) MAPbI3 films, (e) BA-treated MAPbI3 films, and (f) BAI-treated MAPbI3 films[57] (Reproduced with permission from ref 57)
Fig. 5 (a) Schematic of the MP passivation treatment method with FAI and iBAI; (b) Stability test: PCEs monitored in 75% RH condition over a period of 38 d; (c) Distribution of PCE, VOC, JSC, and FF of devices with various passivation compositions[59] (Reproduced with permission from ref 59)
Fig. 6 Schematic of the surface of perovskite with (a) PEAI modification wherein the PEA+ ion seemed to stand vertically and (b) ODAI modification wherein the ODA2+ ion seemed to lie horizontally (color: atom, red: I, gray: Pb, blue: H, yellow: C and brown: N); (c) Device performance as a function of storage time in an ambient environment with a humidity of about 20%~40% under the dark condition, and the inset shows the final photographs of control (left) and ODAI-modified (right) devices[60] (Reproduced with permission from ref 60)
Fig. 7 (a) Molecular structure of the molecules with hygroscopic molecules, (b) Molecular structure of the molecules with Lewis base functional groups[62,64] (Figure a is reproduced with permission from ref 62, Figure b is reproduced with permission from ref 64)
Fig. 8 Images of unmodified FAPbI3, A-FAPbI3, BA-FAPbI3, and PA-FAPbI3 films after different durations (fresh, 3 d, 4 months) of exposure under (50 ± 5)% RH air[65] (Reproduced with permission from ref 65)
Fig. 9 UV-vis absorption spectra of aged MAPbI3 films with and without surface passivation with OA in a dark and humid environment; (a) The absorption spectra of MAPbI3 before and after 1 week of aging; (b) The absorption spectra of MAPbI3 film with OA before and after 1 and 4 weeks of aging, Insets show photographic images of the corresponding samples[68] (Reproduced with permission from ref 68)
Fig. 10 The structure of planar heterojunction devices[69] (Reproduced with permission from ref 69)
Fig. 11 Schematic illustration of defect passivation and water repellence induced by BAA incorporation[70] (Reproduced with permission from ref 70)
Fig. 12 (a) Schematic representation of AVA passivation at lattice termination of MAPbI3, schematic representation of enhanced stability resulting from AVA passivation of surface defect sites of MAPbI3: in the absence of AVA (b), oxygen can access iodide vacancies at grain boundaries, resulting under irradiation in superoxide mediated photodegradation; in the presence of AVA (c), AVA binds to these iodide vacancies, inhibiting this degradation[71] (Reproduced with permission from ref 71)
Fig. 13 The potential surface defect sites in perovskite[72] (Reproduced with permission from ref 72)
Fig. 14 (a) Photographs of the pristine and passivated perovskite films before and after high humidity aging; (b) XRD patterns of freshly prepared and aged perovskite films. (c) Stability test of the reference and 2-MP passivated devices stored in ambient air with a relative humidity of 60%~70% at room temperature[77] (Reproduced with permission from ref 77)
Table 1 Summary of defect passivation for PSCs: passivator, structure, perovskite materials, passivation functional group, passivation type (two-dimensional passivation)/targeted defect (molecular passivation) and photovoltaic parameters without (C) and with (P) passivation (A: average; PVK: perovskite)
Passivator Structure Perovskite Passivation
functional
group		 Passivation
type/
Targeted
defects		 Jsc[mA/
cm2]
(C/P)		 Voc[V]
(C/P)		 FF
(C/P)		 PCE
[%]
(C/P)		 ref
PEAI MAPbI3 Ammonium 2D 23.58/22.69 1.104/1.146 0.7685/0.7632 20.0/19.84 56
BA/BAI MAPbI3 Amine/Ammonium 2D 22.20/22.49、22.59 1.08/1.11, 1.09 0.74/0.78, 0.77 17.75/19.56、18.85 57
ZnPc MAPbI3 Ammonium 2D 22.93/23.23 1.08/1.09 0.76/0.77 18.83/19.56 58
ODAI FAPbI3 Ammonium 2D 24.81/24.90 1.04/1.13 0.78/0.75 20.23/21.18 60
FPEAI Cs0.1(FA0.83
MA0.17)0.9
Pb(I0.83Br0.17)3		 Ammonium 2D 22.04/22.80 1.090/1.126 0.80/0.80 19.22/20.54 61
BA FAPbI3 Amine Undercoor-
dinated Pb2+ or the iodide ions		 22.7/23.6 1.01/1.12 0.70/0.73 15.7/19.2 65
PVP MAPbI3 N donor
(pyridine
group)		 Undercoordinated Pb2+ 20.1/22.0 0.90/1.05 0.64/0.66 11.6/15.1 66
PEO MAPbI3 O donor Undercoordinated Pb2+ 19.823/20.850 1.055/1.105 0.750/0.754 15.552/17.194 67
OA MAPbI3 Carboxyl group Surface Pb2+
and/or CH3NH3+		 24.4/23.5 0.86/0.93 36.0/41.7 7.62/9.11 68
Passivator Structure Perovskite Passivation
functional
group		 Passivation
type/
Targeted
defects		 Jsc[mA/
cm2]
(C/P)		 Voc[V]
(C/P)		 FF
(C/P)		 PCE
[%]
(C/P)		 ref
PCDTBT CH3NH3 PbIxCl3-x S, N donor Undercoordinated Pb2+ 20.87/21.71 0.91/0.94 0.69/0.77 13.19/15.76 69
BAA Cs/FA/MA PVK
MAPbI3		 Amine Undercoordinated Pb2+ 23.4/23.4
22.0/22.5		 1.06/1.16
1.08/1.18		 0.684/0.794
0.772/0.817		 17.0/21.5
18.3/21.7		 70
PBDB-T (CsPbI3)0.04
(FAPbI3)0.82
(MAPbBr3)0.14		 O donor Undercoordinated Pb2+ 21.73/22.39 1.075/1.113 0.740/0.778 17.28/19.38 72
AQ310 (FAPbI3)0.85
(MAPbBr3)0.15		 Carboxyl group Undercoordinated Pb2+ 21.76/21.80 1.11/1.15 0.780/0.784 18.84(17.98 A)/19.66(19.43 A) 73
LL MAPbI3 Bipolarity Anionic defects 21.35/24.09 1.00/1.02 0.728/0.741 15.55/18.20 74
FAL Cs0.05(MA0.17
FA0.83)0.95
Pb(I0.83Br0.17)3		 Amine The sites of
MA/FA vacancies		 22.56/23.33 1.02/1.33 0.743/0.777 17.08/20.48 75
2-MP MAPbI3 N donor (pyridine
ring) and S donor		 Undercoordinated Pb2+ 22.56/22.61 1.09/1.16 0.7464/0.7744 18.35/20.28 77
HS MAPbI3 the-COO-/-SO3- anionic and Na+
cationic groups		 Undersaturated Pb2+ and I- in
MAPbI3 and Ti4+ in TiO2		 21.29/23.34 1.090/1.114 0.7407/0.7731 17.20/20.10 78
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