Full Text

Turn on search term navigation

1. Introduction

Alternative renewable energy sources are considered reliable options for long-term usage due to the limited availability of traditional energy resources (i.e., coal, oil, and gas). Since solar energy is abundant and free (i.e., it comes from a natural source), it is referred to as clean and green energy. Also, solar energy can help reduce air pollution and global warming caused by greenhouse gas emissions if low-cost manufacturing is achieved [1]. This notion of utilizing solar energy further led to the development of photovoltaic technology, resulting in three generations. The first generation of photovoltaic technology was silicon wafer-based solar cells. However, they were not commercially successful due to their high cost. In contrast, second generation solar cells offered a low cost, but compromised in efficiency. Hence, the third generation was developed to be cost-effective and efficient. In this context, perovskite solar cells are considered advanced level third generation photovoltaic technology that could offer low-cost processing with ease of manufacturing and equally high efficiency when compared to their traditional counterparts [2]. This is why the research community has paid attention to perovskite solar cells in the last decade.

“Perovskite” is the name of the mineral CaTiO₃ discovered in the Ural Mountains of Russia; it is named after the Russian nobleman and mineralogist, Lev Perovski. Nevertheless, this term is being used for all compounds, with the general formula ABX₃, with the same crystal structure as CaTiO₃ or derived from this structure. These materials consist of two cations. Cation A is 12-fold coordinated by anion X, and cation B is 6-fold, where X can be either oxygen or a halide. In terms of perovskite solar cells, the most commonly used A-site cations are MA/[CH₃NH₃]⁺, FA/[H₂NCHNH₂]⁺, Rb⁺, Cs⁺, B site cations are Pb²⁺, Sn²⁺, Ge²⁺_. While the X site is halogen atoms, I⁻, Cl⁻, Br⁻ [3]. Among many different perovskite absorber layers, methyl ammonium lead iodide (MAPbI₃) is the most prominently studied hybrid organic–inorganic perovskite for perovskite solar cell application. MAPbI₃ offers several unique properties and advantages to be applicable in perovskite solar cells (PSC). It has a suitable bandgap~1.6 eV, a high absorption coefficient (the absorption coefficient of MAPbI₃ lies in the range of 10⁴–10⁵ cm⁻¹, which is more than one order of magnitude larger than that of silicon for the visible light spectrum). The high absorption coefficient of MAPbI₃ allows it to absorb in the low light region. Moreover, a high absorption coefficient allows light to be absorbed by a thin film (generally in the range of 0.3–0.6 μm) of the perovskite layer, while crystalline silicon-based solar cells are usually made thicker ~300 μm. This, in turn, reduces the quantity of required material, thereby reducing the cost. Besides, MAPbI₃ can be easily solution-processed to produce efficient solar cells, which further lowers manufacturing costs. Moreover, MAPbI₃ can result in high open-circuit voltages (V_oc), low V_oc loss/deficit, and low exciton binding energy: 2–70 meV, resulting in better charge transport with decent charge carrier motilities of 2–66 cm² V⁻¹ s⁻¹, long diffusion lengths of charge carriers ~1 um. Because of these properties, scientists and researchers have recommended the fabrication of perovskite solar cells using MAPbI₃ as the active layer [4,5,6]. Nevertheless, long-term operational stability has been a significant factor that acts as a blockade for the commercialization of PSCs. In comparison, the traditionally made silicon-based solar cells remain operational for up to 20–25 years. On the contrary, perovskite solar cells are stable for a few hundred hours to a maximum of one year [4]. Thus, PSCs face serious stability issues compared to already available PV technology in the market. These stability issues involve both extrinsic and intrinsic challenges to overcome.

The perovskite-based active layer is susceptible to external factors, such as water, air, and moisture [7,8,9]. Reports have shown that, upon exposure to these external factors, PSC degrades and loses its operational stability [10]. It was found that, in the presence of water, MAPbI₃ crystal structure forms hydrates/complex with H₂O (Equation (1)), and deforms the perovskite structure, destroying optoelectronic properties, resulting in loss of photovoltaic performance [7,11,12].

4CH₃NH₃PbI₃ + H₂O ↔ 4CH₃NH₃PbI₃·H₂O ↔ (CH₃NH₃)4PbI₆·2H₂O + 3PbI₂ + 2H₂O(1)

Moreover, it was demonstrated that exposure of CH₃NH₃PbI₃ photoactive layers to light and oxygen results in the formation of superoxide (O₂⁻) species. This reactive O₂⁻ species can deprotonate the methyl ammonium cation (CH₃NH₃⁺), leading to the formation of PbI₂, water, methylamine and iodine [13,14,15], as shown in Equation (2).

4CH₃NH₃PbI₃ + O₂⁻ → 4CH₃NH₂ + 2I₂ + 2H₂O + 4PbI₂ (2)

Furthermore, when MAPbI₃ is exposed to moisture, methyl-ammonium cation degrades and results in PbI₂, I₂ and water formation (Equations (3)–(6)) [4], and the solar cell is destabilized.

CH₃NH₃PbI₃(s) → CH₃NH₃I (aq) + PbI₂ (s) (3)

CH₃NH₃I (aq) → CH₃NH₂ (aq) + HI (aq) (4)

4HI (aq) + O₂ (g) → 2I₂ (s) + 2H₂O (5)

2HI (aq) → H₂ (g) + I₂ (g) (6)

Nevertheless, the impact of these external factors can still be minimized by encapsulating the active layer. However, it may affect performance and the cost. Ironically, MAPbI₃ is intrinsically unstable as well. It means that, in the presence of light and heat, MAPbI₃ tends to decompose. Sadly, these conditions are unavoidable for the operation of a solar cell.

When the temperature exceeds 85 °C in the dark, MAPbI₃ forms ammonia or some other volatile species, and PbI₂ (Equation (7)) [12,16].

CH₃NH₃PbI₃ → PbI₂ + CH₃I + NH₃ (7)

Whereas, in the presence of light and temperature, PbI₂ intermediate forms and further decomposes, resulting in the formation of metallic lead and molecular iodine. At the same time, volatile species/by-product may rise from CH₃NH₃I. In the presence of light and heat, the identified degradation pathways are presented in Equations (8) and (9) [2,17,18,19,20,21,22,23]:

CH₃NH₃PbI₃ → [PbI₂] + volatile species (rising from CH₃NH₃I) (8)

PbI₂ → Pb²⁺ + 2I⁻ → Pb⁺ + I⁰ + I⁻ → (1/2)Pb⁰ + (1/2)PbI₂ + (1/2)I₂ (9)

Thus, these Pb and iodine sites create defect sites/trap states, resulting in instability of the CH₃NH₃PbI₃ active layer and CH₃NH₃PbI₃-based perovskite solar cell devices overall. These defect sites are often reported to be within the grains, at grain boundaries or at the surface of the CH₃NH₃PbI₃ perovskite layer. Moreover, these trap states can also alter the energy level alignment and destroy charge transfer properties in CH₃NH₃PbI₃ solar cell devices. Additionally, non-radiative recombination becomes more prominent in such a scenario, a clear indication of deterioration of device performance. Therefore, it is crucial/important to chemically passivate these defect sites to achieve longer stability of the CH₃NH₃PbI₃ layer [14]. To achieve the aforementioned, additive engineering has been widely applied. Although, the passivation can also be achieved by physically passivating the defects with the help of encapsulating layer [24,25,26,27].

In this review, however, we will focus only on the additive approach. To accomplish this, we have analyzed/scrutinized additives used in the CH₃NH₃PbI₃ photoactive layer. Further, the role of the additive and mechanism of the additive interaction with CH₃NH₃PbI₃ has also been discussed. Their impact on film morphology, charge transport properties, and impact on stability has been intensively described. It should be noted that, here, we discussed only those additives that are added in the CH₃NH₃PbI₃ layer. In addition, scrutiny of the physical passivation layers/encapsulation approach that may result in the same is beyond the scope of this review, as we mainly focused only on the aspect of additive engineering. Further, we aim to discuss those additives that do not alter/destroy the perovskite structure of CH₃NH₃PbI₃, i.e., do not result in mixed cation or mixed halide perovskite. The additives are mainly classified as organic additives and inorganic salt additives. Furthermore, organic additives are analyzed based on the functional group associated with the N/O/S donor atom. At the same time, the inorganic salt additives are further classified as per the group name in the periodic table, i.e., alkali metals, transition metals, other metals, and non-metals. This review aims to analyze the research progress/advancement in the context of additives employed to improve the performance and stability of the CH₃NH₃PbI₃ photoactive light-absorbing layer. This can further help design additives, ultimately resolving stability challenges to commercialize the CH₃NH₃PbI₃-based perovskite solar cell.

2. Organic Additives

Organic additives are the most common types of additives used in perovskite solar cells. These organic additives can be further categorized based on N donor, O donor, and S donor atoms. These electron donor atoms can bind/coordinate with the Pb²⁺ species, resulting in adduct formation, passivating the grain boundaries and, thus, improving efficiency and stability. Subsequently, based on the electron-donating atoms, additives can be further subcategorized as amines, nitriles belonging to the N donor atom, amides, acids, acetates, alcohol, esters, and ethers, belonging to oxygen donor atoms and sulfides, thiocyanates belonging to the S donor atom [28].

2.1. N Donor Atom-Based Additives

2.1.1. Amine Additives

Following the notion of amine-based additives, the non-stoichiometric use of methylammonium iodide as an amine additive was advised in the early phases of developing perovskite solar cells. It was established that adding excess MAI reduces trap density, increases PL lifetime, and further increases PCE regardless of fabrication methods [29,30,31]. Likewise, some other organic amine derivatives, such as benzylammonium iodide (BAI) and phenethylammonium iodide (PEAI), have also been investigated as additives and were found to improve light harvesting properties and exciton lifetime with reduced charge recombination [32,33]. Moreover, it was discovered that, if hydrophobic cations containing amine additives are employed, such as hexylamine hydrochloride (1-HH), 1,6-diaminohexane dihydrochloride (1,6-DD) and phenylhydrazinium iodide (PHAI), it may even work as a protection for the MAPbI₃ film against moisture, improving the stability in ambient conditions [34,35]. Later, it was found that, if instead of an iodide, a chloride-based counterpart (i.e. MACl instead of MAI) was used as an additive, perovskite films became more crystalline, with increased grain size and homogenous, smooth morphology, which further resulted in grain boundary passivation, resulting in better performance. Unfortunately, the addition of MACl was reported to form mixed halide perovskite CH₃NH₃PbI_3−xCl_x [36,37,38]. Although there were opposite reports about mixed halide formation. It was shown that when other halide ions, i.e., X = Br/Cl, are used with a minimum concentration in MAPbI₃ precursor, it does not affect MAPbI₃ characteristics, and the final perovskite remains crystalline MAPbI₃ phase-only instead of mixed halide perovskite. This is because a low concentration of halide ions can quickly evaporate as the films are annealed during the fabrication process. Some of the examples of such additives are amphiphilic hexadecyl trimethyl ammonium bromide(CTMAB), ethyl ammonium chloride (EACl), 1,3-diaminoguanidine monohydrochloride (DAGCl), benzamidine hydrochloride (BMCl), acetamidine hydrochloride (AcHc), methoxyammonium chloride (MeOCl), 2, 2, 2-trifluoroethylamine hydrochloride (TFEACl), benzenamine hydrochloride(BACl), 3-chloropropylamine Hydrochloride (3-CPACl), diethylamine hydrochloride (DEACl) [39,40,41,42,43,44,45].

Furthermore, nitrogen-containing heterocyclic amines play a great role in improving stability [46]. For instance, the introduction of 4,4′-bipyridine in MAPbI₃ demonstrated complex formation with PbI₂, thus improving intrinsic stability against illumination [47]. Additionally, it has been shown that the presence of N atoms prevents the loss of volatile species from the perovskite film and acts in a similar way as polymeric passivation coating. Further, such a passivation effect was visible, morphologically (in the SEM cross-section images and energy dispersive X-ray analysis), when PVC was added in MAPbI₃ [48]. Later, scientists designed pyridine derivatives with units containing different multifunctional groups. One such additive is (C₆₀-PyP), which contains C₆₀ units that are hydrophobic in nature and pyridine units, which chelates Pb²⁺ by donating the lone electron pair on the N atom. It is known that uncoordinated Pb²⁺ ions are considered trap states at grain boundaries and can block charge extraction [49]. Thus, grain boundaries are passivated by assisting coordination interactions with the Pb²⁺ ion of MAPbI₃ and PyP unit that further improved short circuit current density J_sc and eliminated ion migration. While the hydrophobic C₆₀ unit does not let moisture directly affect the film [49]. Similar results were noticeable when pyridine-2-carboxylic lead salt (PbPyA₂) and polyvinylpyrrolidone (PVP) additives were employed in MAPbI₃ precursor [36,50]. Additionally, solvent additives with heterocyclic nitrogen-containing units also demonstrated similar results. In an investigation, Zhang and co-workers demonstrated that NMP as a solvent additive (when added in DMF) resulted in a high quality of perovskite film due to the Lewis acid–base reaction with Pb atom. The study revealed that intermediates obtained with different PbI₂/NMP ratios are of the same kind, because of which, the solar cell performance and stability do not depend on the NMP ratio in the precursor [51]. Following the idea of the Lewis acid–base interaction, KIM and co-workers explored pyrrolidone-based solvent additives and compared with commonly used DMF-based precursor [52]. For pyrrolidone-based solvent additives, different N-substituents: N-methyl-2-pyrrolidone (NMP), N-ethyl-2-pyrrolidone (NEP), N-cyclohexyl-2-pyrrolidone (CHP), and N-octyl-2-pyrrolidone (NOP) was employed. During the in situ crystal growth, it was observed that solvent additive containing pyrrolidone structure with higher boiling point results in lower vapor pressure over pristine DMF-based precursor. Thus, it resulted in a further improvement in the morphology of perovskite film since the N substituent becomes bulkier with a higher boiling point (the boiling points of NMP, NEP, CHP, and NOP are 154 °C, 202 °C, 204 °C, 286 °C, 303 °C). Furthermore, it was discovered that the strength of coordination of solvent component influenced intermediate formation with PbI₂, which, in turn, was influenced by the boiling point of the solvent. This was based on the evidence when the intermediate phase vanished with the CHP solvent additive, whereas pure DMF solvent without pyrrolidone-based solvent additives showed DMF: PbI₂ solvate formation. Therefore, it was suggested that the bulkier additive solvent suppress DMF: PbI₂ solvate formation, which shows lack of stability when used without any cosolvent [52]. Some other derivatives, such as DMI, 1-(4-ethenylbenzyl)-3-(3,3,4,4,5,5,6,6,7,7,8,8,8-tridecafluorooctylimidazolium iodide (ETI), 1-methyl-3- propylimidazolium bromide (MPIB), 1-butyl-3- tetrafluoroborate (BMIMBF4) are other examples that result in improved PCE and ambient stability due to hydrophobicity of N atoms with a ring-like structure [53,54,55]. Figure 1 below shows the chemical structures of additives based on amine derivatives.

2.1.2. Cyano/Nitrile Additives

Subsequently, it was observed that the cyano group-containing N atom could be equally effective to passivate grain boundaries [56]. Triazine-graphdiyne (Tra-GD) is a graphene-like material that consists of pyridine-like nitrogen in the highly conjugated framework. It was suggested that balanced charge distribution in the C=N bond in the triazine ring promotes stronger interaction with Pb²⁺, resulting in very tight contact between these two materials. This, in turn, did not allow the ion migration on the surface and successfully passivated grain boundaries [56]. Similarly, graphitic carbon nitride addition also resulted in good morphology due to highly compact bonding between Pb²⁺ and N of C=N that further endorsed to achieve power conversion efficiencies (PCEs) up to 21.1% (aperture 0.16 cm²) and 19.5% (aperture 1.0 cm²), featuring an open-circuit voltage of 1.16 V (corresponding to a slight voltage loss of 0.39 V), and improved operational device stability (~90% initial efficiency retained after constant one sun illumination for 500 h) [57,58]. Further, Zhou and co-workers demonstrated that, by employing 1,8-Diazabicyclo[5.4.0]undec-7-ene (DBU), the formation of I⁻ can also be suppressed due to adduct formation with PbI₂ [59]. Moreover, another solvent additive, acetonitrile (ACN), also showed improvement in morphology due to adduct formation with PbI₂ when added in a DMF-based precursor. This further proved to increase PCE from 15.04% to 19.7%, which remained stable without encapsulation for 160 h, with the PCE remaining ~60% of the initial value when exposed to the white light [60]. The chemical structures of the mentioned nitrile-based additives are illustrated in Figure 2.

Further, at a glance, the summary of additives that improve stability is presented in Figure 3. In Figure 3, “Extrinsic” represents results reported by conducting stability tests in air, moisture, or in ambient conditions, whereas “Intrinsic” represents results reported by conducting stability tests in inert, inside glovebox (nitrogen or argon filled), or vacuum. All subsequent figures depicting stability time versus additive will use these terms and represent the aforementioned. Here, the stability time refers to the time for which the active layer with additives was reported to be operational/functional in corresponding references. Additional details of additive influence on power conversion efficiency (PCE) and stability are described in Table 1, displaying the additives based on the N donor atom for the MAPbI₃ active layer.

2.2. O Donor Atom-Based Additives

Similar to N donor, O donor and S donor can also act as Lewis bases due to lone pair of electrons available to co-ordinate with Pb defect site. Additives containing O atom as the Lewis base may consist of various functional groups, such as carbonyls, carboxyl, carboxylates, ester, ethers, and alcohols [28].

2.2.1. Carbonyl and Amide Additives

One such systematically investigated additive is urea. Urea is an eco-friendly compound consisting of a carbonyl group known to interact with PbI₂ [65]. It has been illustrated that PbI₂ and urea forms an intermediate PbI₂.O=C(NH₂)₂ when added to the PbI₂ precursor solution in the double-step spin coating process. The oxygen atoms act as a Lewis base. Whereas Pb²⁺ acts as Lewis acid, resulting in the formation of Lewis acid–base adduct. This adduct formation further results in large, flat grains [66,67]. Similar results were observed for the single-step spin coating process, resulting in grain boundary passivation, improved crystalline film, and suppressed non-radiative recombination losses, further improving the efficiency of solar cells [67,68,69]. Moreover, it was shown that incorporating amides in MAPbI₃ reduces the Fermi level by interacting I⁻ defect vacancy, reducing the trap sites, and increasing the work function of MAPbI₃ perovskite. At the same time, the carbonyl group transfers electrons to perovskite, reducing the Fermi level, which in turn helps to achieve better charge transport properties [70]. Recently, a variant of urea, biuret incorporation in MAPbI₃ precursor attributed the intermediate formation with PbI₂ to the electron delocalization in the N–C=O–N system in the presence of carbonyl group and explained this is why the peak shift for C=O vibration is noticed in FTIR spectra (from 1722 to 1713 cm⁻¹ in case of biuret-modified MAPbI₃ film) [71], resulting in higher PCE over urea incorporated devices [72]. Some other additives, such as benzoquinone (BQ), triazine perylene diimide (TPDI), 3,4-dihydroxybenzhydrazide (DOBD), containing the carbonyl group have shown similar properties [73,74,75,76]. Similarly, it was also shown that, if a hydrophobic ring is attached within the additive framework in combination with the carbonyl group (Isatin-Cl additive), it also acts as a shield against humidity in ambient conditions, helping to maintain the PCE nearly to 95% of the initial state [77]. Moreover, the usage of the carbonyl group can also be expanded to improve the flexibility of flexible, printable solar cells (FPSC). Polycaprolactone (PCL) additive in MAPbI₃ has shown desirable improvement in PCE as well as mechanical strength. This improvement in mechanical stability was ascribed to a two-fold increase in grain size (from 200 to 400 nm) and homogenous grain distribution, leading to improved mechanical stability that maintained PCE more than 90% of the initial state after 300 bending cycles for the radius from 20 to 4 mm and stability under illumination for 350 h [78].

2.2.2. Sulfonyl Additives

Furthermore, carbonyl-based additives are often compared with the sulfonyl-based group, where the O atom is connected to different species, (i.e., S atom instead of C atom). Fang and co-workers have done one such study in which the strength of Pb coordination of the sulfonyl group containing additive was compared with the carbonyl-based additive. For this purpose, two novel fused ring non-fullerene acceptor materials IDIS-Th and IDIC-Th were introduced into MAPbI₃. IDIC-Th had the Lewis base functional group carbonyl (C=O), and IDIS-Th had a sulfonyl group (O=S=O). Since the sulfonyl group (O=S=O) is a stronger electron-withdrawing group compared with carbonyl (C=O); the sulfonyl group was predicted to have a stronger interaction with Pb ions than carbonyl (C=O) because the two sulfur-oxygen double bonds can chelate Pb²⁺ with stronger interaction. Moreover, it was noticed that replacing carbonyl with the sulfonyl group could effectively downshift the lowest unoccupied molecular orbital (LUMO) level of IDIS-Th, which indicated the sulfonyl group is a stronger electron-withdrawing group. Thus, the interaction with Pb would reduce the defect traps density. Further, to confirm the defect passivation effect of IDIC-Th and IDIS-Th, the trap densities (n_trap) in bulk MAPbI₃ films were calculated and found to be 8.85 × 10¹⁵ cm⁻³ and 4.20 × 10¹⁵ cm⁻³, respectively. Undoubtedly, the sulfonyl group reduced the defect states. This further reflected improvements in the contact angles of the film (the hydrophobicity of the films). The improvement in hydrophobicity indicated that the additive molecules at the GBs and surface could inhibit the raid of moisture to MAPbI₃ films. However, both IDIC-Th and IDIS-Th are known for their hydrophobic nature. Nevertheless, these changes reflect improvement in hydrophobic nature. Moreover, the influence of the two molecules on photovoltaic performance was also examined. The PSC with IDIS-Th molecule showed significant improvement in PCE and reached up to 20.01%. Additionally, due to the strong passivation effect of IDIS-Th, PSC with IDIS-Th demonstrated superior stability over PSC with IDIC-Th in ambient conditions, under solar radiation and in the dark at high temperature [79]. Likewise, a comparison of solvent additives hexamethylphosphoric triamide (HMPA) and dimethyl sulfoxide (DMSO) was made, which was further compared to solvent additive NMethyl-2-pyrrolidone (NMP). Here, Lewis basicity, donor number (D_N), and the boiling point of solvents were utilized as comparison parameters to correlate the role of solvents in regulating morphology. This investigation, conducted by Cao and Wei, and co-workers, highlighted that the larger the donor number, the stronger is the Lewis basicity of the solvent additive. The donor number of DMF, NMethyl-2-pyrrolidone (NMP), dimethyl sulfoxide (DMSO), and hexamethylphosphoric triamide (HMPA) are 26.6, 27.3, 29.8, and 38.8, respectively. Therefore, it was suggested that Pb-O bond strength would increase with an increase in the donor number of the additive [80,81]. Hence, NMP, DMSO, and HMPA were expected to form stronger intermediates over pure DMF. In addition, it is also observed that the strong Lewis base additives exhibit higher boiling points. (The boiling points of the DMF, NMP, DMSO, and HMPA are 152, 202, 189, 235 °C, respectively) [82,83]. This, in turn, reduces the evaporation rate of the solvent during the spin-coating process, resulting in a good film morphology. As a result, DMSO followed by NMP cosolvents displayed excellent PCE of 14.66% and 16.17% over pristine (DMF) (12.25%). No residue of PbI₂ remained and complete conversion into perovskite resulted in less resistance [84]. Further, other solvent additives based on O donor atoms, such as tetramethylene sulfone (TMS) [85] and tetrahydrothiophene oxide (THTO), also utilized a similar mechanism of forming the Pb–O bond and improved performance and stability [86]. The chemical structures and influence of amides/carbonyl/sulfonyl group-based additives onto the stability of the MAPbI₃ layer are presented in Figure 4 and Figure 5, respectively, with a glance summary shown in Table 2.

2.2.3. Carboxylic/Acid Additives

Acid additives have also been incorporated in the MAPbI₃ precursor. The most commonly reported acid additive is 5-amino valeric acid (5-AVA). Dauskardt and co-workers showed that the introduction of 5-AVA into MAPbI₃ precursor could be helpful to increase the mechanical robustness of the perovskite film. To test the mechanical reliability, the double cantilever beam method was used, and the cohesion energy (Gc) was calculated from the critical load at which the film created cracks. It was observed that the incorporation of 5% concentration of 5-AVA into MAPbI₃ precursor increased cohesion energy (Gc) from 0.61 ± 0.27 J/m² (pristine) to 6.04 ± 2.04 J/m² (with AVA additive) almost 12-fold. This improvement in Gc with 5-AVA was attributed to enhanced interaction forces due to the longer alkyl chains present in the 5-AVA [87]. Additionally, a further increase in plasticity and crack deflection around the additive-containing perovskite grain boundaries was observed. Later, the elastic moduli of MAPbI₃ perovskite films with 5-AVA showed a slight decrease in the elastic modulus from 20.5 GPa (pristine) to 18.9 GPa (5-AVA) (using the nanoindentation method). This decrease in stiffness of the planar perovskite structure made it more mechanically robust and less brittle. Moreover, it was confirmed that adding 5 AVA in MAPbI₃ precursor does not change MAPbI₃ lattice parameters [87]. Simultaneously, another study done by Durrant and the group reported enhanced photostability of MAPbI₃ solar cells due to surface defect passivation in screen printed, HTM free, carbon electrode-based PSC consisting of 5 AVA in MAPbI₃. They found a 40-fold increase in device lifetime measured under full sun illumination in ambient air (RH ± 15%). Further, it was proposed that AVA is located at grain boundaries and, thus, able to passivate surface defect sites, resulting in enhanced resistivity to oxygen-induced degradation [88]. The impressive improvement in the stability due to the AVA additive is attributed to the interaction of halides with –COOH and NH₃⁺ group, through hydrogen bonding ((O–H----I) and (N–H----I)), and further verified in the large area cell with an area of 0.25 cm², which demonstrated the efficiency of 6.6% with a decent shelf life of 75 days, maintaining more than 90% of initial efficiency [89]. Later, using polyacrylic acid (PAA), Cao and workers demonstrated that acid additives could be useful for large area (1 cm²) films using the doctor blade method. Using the carboxyl functional groups of PAA, iodide ion vacancies at the perovskite crystal surface could be cross-linked. Thus, the interaction of the PAA molecule with MAPbI₃ passivates defects and improves PCE and stability [90]. In addition, it was demonstrated that bifacial passivation could also be obtained by the interaction of a functional group of –COOH, combined with –C, –S (of thioctic acid (TA)). Lewis acid–base reaction between under-coordinated Pb²⁺ and S atom in MAPbI₃ can passivate one side, and at the same time, TiO₂ can interact with COOH through hydrogen bonding, resulting in double-sided passivation [91]. Likewise, various studies reported that if multiple –COOH groups are attached with hydrophobic phenyl ring—it can chelate with Pb²⁺ atom and act as a shield against moisture and humidity under ambient conditions, maintaining the overall crystallinity of film. Terephthalic acid (TPA) and trimesic acid (TMA) are examples. The proposed mechanism of stability in such a case is given as follows: negatively charged groups (–COO⁻) strongly attract Pb²⁺ ions in the precursor solution via electrostatic interactions. At the same time, the hydrogen atom from carboxylic acid can bond covalently with halide anion in solution due to the strong electronegativity of halide ions. Thus, it overall suppresses the loss of iodine molecules and, in turn, slows down the decomposition of MAPbI₃ light absorbing layer. Simultaneously, benzene ring with rigidity and π–π bond effect does not allow interacting with water and protects against thermal stress and UV-illumination in ambient conditions [92,93]. Similar effects were observed when 3,3’,5,5’-azobenzene-tetracarboxylic acid (H₄abtc) containing two benzene rings connected via azo bonding is introduced in PbI₂ precursor in optimum amounts (2 mass %). The purpose of using the azo group was to reduce the stiffness of the perovskite film [94]. However, due to the hydrophobic nature of the attached cation in the acid-containing additive, most of them increase ambient stability (see Figure 6 for chemical structures of acid-containing additives and Figure 7 for associated stability). Further details of acid–based additives in MAPbI₃ are provided in Table 3 below.

2.2.4. Carboxylate/Acetate Additives

In a similar fashion, the acetates in the form of additives also show improvement in crystallinity and grain size, passivating the grain boundaries. One of the examples is formamidine acetate salt (FAAc). It was reported that FAAc controlled the film morphology and improved fill-factor over 80%, which in turn improved PCE to 16.59%. The improved photovoltaic parameter was further associated with the incorporation of FAAc that eliminated the defect and trap density in the MAPbI₃ film and, thus, improved the charge transport efficiency and reduced the hysteresis [98]. On the contrary, methyl ammonium acetate (MAAc) resulted in lower crystallinity and a smaller grain size ~200 nm [99]. However, it was suggested to use MAAC together with thiosemicarbazide (TSC) salt in the precursor to overcome lower crystallinity. This combination of additives (10–15% MAAc (molar ratio) and a tiny amount of TSC (3–5% molar ratio)) gave a certified PCE of 19.19% for an aperture area of 1.025 cm², and the high-performing devices were able to sustain over 80% of the initial PCE after 500 h of thermal ageing at 85 °C [100]. Moreover, acetate additives were reported to be used as complementary to halogens. For instance, ammonium acetate (NH₄Ac) was found to produce full film coverage with higher crystallinity. It was speculated that NH₄Ac resulted in the formation of methylamine acetate salt by forming NH₄PbI₃ as an intermediate phase with a volatile by-product NH₃ resulting in a higher nucleation density of grains and full coverage of the surface. This, in turn, resulted in a higher efficiency of 13.9% in carbon-based solar cells (FTO/TiO₂/perovskite/Carbon), and 17.02% in the two-step spin coating in FTO/TiO₂/CH₃NH₃PbI₃/spiro-OMeTAD/Au configuration [101,102]. Further, the influence of NH₄Ac addition was compared with NaAc and ZnAc₂. Sadly, the incorporation of sodium acetate (NaAc) into MAPbI₃ precursor reported no improvement in photovoltaic performance. However, the PCEs were comparable. While compared to Zinc-acetate (ZnAc₂) additive, devices with ZnAc₂ demonstrated improved fill factor and short circuit current density over reference cells, resulting in improved PCE from 11.1% to 12.30%. Furthermore, against the speculation that Zn²⁺ might partially replace Pb²⁺, due to the smaller ionic radius, the small quantity of ZnAc₂ (MAI/PbI₂/ZnAc₂ (1:1−x:x, x = 7% as of molar ratio)) was reported to assimilate well within the MAPbI₃ framework, and maintained ~89% of initial PCE after 1900 h when stored in Rh=40%, dark. However, NH₄Ac incorporated devices exhibited ~96% PCE of the initial stage after 1900 h with the same conditions [101,102]. Later, lead acetate (PbAc₂) was employed as an additive, demonstrating excellent PCE improvement from 17.25% to 19.07%. It was further demonstrated that incorporation of PbAc₂ in precursor creates an intermediate phase by forming hydrogen bonding due to interaction with MA⁺ and O from acetate. Thus, this hydrogen bonding acts as a cross-linking agent for the intermediate phase, which later improves the intrinsic stability of devices that maintain almost 95% of the initial PCE for 20 days [103]. A similar mechanism was utilized in another study where the addition of barium acetate (BaAc₂) was explored in MAPbI₃ perovskite with a lower concentration (0–2 mg/mL), which suppressed ion migration and improved thermal stability. The devices could sustain ~90% PCE of the initial stage after exposure to thermal stress at 90 °C in the dark in inert conditions without any encapsulation up to 400 h [104]. Thus, by employing acetate-based additives (Figure 8), improved stability can be obtained both in ambient and inert conditions (Figure 9). Further, the acetate-based additives are summarized in Table 4.

2.2.5. Ester- and Ether-Based Additives

Interestingly, phenyl-C61-butyric acid methyl ester (PCBM), which is commonly employed as a charge transport layer in organic–inorganic hybrid solar cells, was also examined as an additive in the perovskite layer to achieve hole transport material (HTM) free fully printable MPSC (mesoporous perovskite solar cell). It was shown that, when the concentration of PCBM increased from 0 to 0.25 mg/mL, the PCE significantly improved from 8.58% to 12.36%, achieving a PCE enhancement of more than 44%. This enhancement of PCE was further ascribed to increased J_sc from 14.56 mA cm⁻² to 20.26 mA cm⁻² due to higher photogenerated charge separation, and suppressed the charge recombination process. Later, it was illustrated that the PCBM-perovskite intermediate phase was facilitated due to the formation of an intermediate adduct with PbI₂ and carbonyl groups in PCBM [105]. Afterwards, Hu et al. compared PCBM incorporation with only the C₆₀ unit and C₆₀-taurine unit in a single-step spinning coating method in p-i-n configuration. It was reported that C₆₀ (16.59%), PCBM (15.94%), C₆₀-Ta (16.59%) all improved PCE over pristine (14.87%), which was consistent with the previously published report. Further, it was found that the addition of C₆₀ and its derivatives decreased the trap densities and exhibited higher stability when exposed to ambient conditions RH = 25–50% without encapsulation [106].

Moreover, investigations have shown that ethers can help passivate grain boundaries on the perovskite surface. Poly (propylene glycol) bis (2-aminopropyl ether) (PEA) and Jeffamine are some of the examples that showed interaction with Pb ions due to the lone pair of the electron on the oxygen-containing ether part of the additives. Simultaneously, the MA⁺ cation from perovskite forms hydrogen bonding with the counter ion of the additive. Thus, the polymer works as a cross-linking agent that decreases trap densities and hysteresis, improving the device performance and stability. Moreover, the cross-linking properties can also improve the ductility of the perovskite film while stretching when fabricated on a flexible substrate (such as D2000, a Jeffamine variation) [107,108]. Furthermore, using the mechanism above, ethyl cellulose (EC), a low cost, environmentally friendly, thermally stable, and water-insoluble compound, also demonstrated chemical passivation of defect traps. Thus, because of the passivation effect of EC additive, the MAPbI₃ crystal structure remained stable against moisture and air, maintaining 80% of PCE when exposed unencapsulated to ambient air at RH = 45% in the dark for 30 days [109]. Later on, tetra-orthosilicate (TEOS) additive in MAPbI₃ was also reported to lower the cost of processing by making the fabrication process feasible in the air instead of the glove box, which was found valid for both single and double step spin-coating methods. This achievement is due to the fact that, when TEOS is introduced to MAPbI₃ in air, SiO₂ precipitates, acting as a passivation for the perovskite surface and shielding it from moisture and air. This improved the overall stability in ambient conditions [110,111,112]. Further, cyclic ether compound THF (tetrahydrofuran) also reported improving stability in ambient air, which the pioneer of the PSCs, the Miyasaka group, investigated. The study demonstrated that THF and PbI₂ in DMF interact and form a complex, resulting in dense, homogenous, and pinhole-free film due to complex formation between the Pb and O donor from THF, because of the Lewis acid nature of Pb and Lewis basicity of THF. This, in turn, avoids a direct interaction of PbI₂ with water, improving T80 (T80 is the time at which PCE is degraded to 80% of initial PCE) for 20 days in the ambient environment, with 50% RH, when devices were exposed unencapsulated [113]. Similarly, the liquid additive diethyl ether was also found to influence the crystallization process, resulting in large grains, leading to improved photocurrent properties and performance [114]. The chemical structures (Figure 10) and an overview illustrating the influence of ester and ether-based additives on the stability of MAPbI₃-based solar cells is shown in Figure 11, respectively. Further, a table describing ester and ether containing additives and their role in the MAPbI₃ layer is presented in Table 5.

2.2.6. Hydroxyl/Alcohol

The Hydroxyl group can also play a vital part in interacting with perovskite through hydrogen bonding, further resulting in improved crystallinity and performance. For example, enhanced PCE and stability was observed when dibutyl hydroxyl toluene (BHT) additive containing a phenol group was mixed in MAPbI₃ precursor [115]. Furthermore, methanol and isopropanol showed larger grain size, reduced grain boundaries, lessened defect density, and demonstrated efficient charge carrier extraction at the interfaces, leading to improved PCE stability in ambient conditions without encapsulation. Similarly, improvement in PCE was also noticed due to other hydroxyl-based additives, such as 2-methoxy ethanol (ME), 2-ethoxyethanol (EE), and 2-propoxy ethanol (PE) and n butanol [116,117,118]. The chemical structures of the discussed additives are shown in Figure 12. The influence of some of the alcohol additives on the stability of MAPbI₃ perovskite is displayed in Figure 13. Further, a summary of alcohol-based additives, their influence on the PCE, and their role with the perovskite framework is described in Table 6.

2.2.7. Oxygen-Based Multifunctional Group Containing Additives

Other than these additives, other oxygen atom-based additives with multiple functional groups, consisting of C=O, COOH, and OH, were also employed in the MAPbI₃ precursor. One of the examples is reduced graphene oxide (rGO), which was used to achieve fast electron transport rates toward anode, including the growth of large, uniform, smooth, and crystalline perovskite film, resulting in a massive improvement in device performance from 13.6% to 20% [120]. Another example includes poly (amic acid) (PAA) and polyimide (PI) additive. However, the PAA and PI additives also consisted of the N atom, other than C=O, COOH and the OH functional group. The O atoms in PAA and PI form hydrogen bonds with H atoms in CH₃NH₃⁺. The lone pair of electrons of N atoms interact with Pb ions, which stabilized the PVSK framework. Furthermore, these interactions improved the optoelectronic properties of the perovskite layer. As a result, an increment in the grain size was observed when 0.0497 mg/mL PAA-derived perovskite was employed, illustrating the Lewis acid−base interaction between C=O and Pb²⁺ that controls the crystallization process and defect passivation of PVSK. Moreover, both PAA and PI are hydrophobic and highly heat-resistant polymers and further contribute to the stability of PSC when operated in a humid and high-temperature environment [121]. The chemical structure of these additives and their influence on stability are shown in Figure 14 and Figure 15, respectively. Table 7 presents the detailed description of these additives.

2.3. S Donor Atom-Based Additives

2.3.1. Sulfide and Organosulfur Additives

Further, sulfur-based donor atoms have also improved crystallinity and device performance [28]. For instance, Yang and co-workers used dimethyl sulfide (DS) additive in MAPbI₃ precursor solution (based on DMSO precursor) and demonstrated a record high PCE of ~18.4% for a flexible perovskite solar cell. In addition, the formation of a stable intermediate complex between PbI₂ and DS molecule was observed, which further enhanced stability. The enhancement of stability due to DS solvent additive was ascribed to the smaller electronegativity of the sulfur atom (2.5) in the DS molecule compared to an oxygen atom (3.5) in the DMSO molecule, which allowed sulfur molecules to provide electrons to empty 5d Pb orbitals, ultimately resulting in a hexa-coordinated complex formation. Therefore, with better crystallization and stable intermediate formation, 86% of initial PCE remained for 60 days when unencapsulated devices were exposed to moisture RH~35% in the dark at room temperature [122]. Thiourea is another example of such an organosulfur compound, the addition of which, into the photoactive layer, results in improved performance and stability due to intermediate formation because of the Lewis acid–base reaction. However, the addition of thiourea in the active layer is often compared to the similar compound urea, where the O atom from the carbonyl group (in urea) is replaced with the S atom for thiourea. (i.e., the carbon atom is connected to different species—C=O for urea and C=S for thiourea). Both thiourea and urea were found to show similar effects of increasing grain size, crystallinity, grain boundary passivation, and coordination with PbI₂ in the MAPbI₃ framework [123]. Moreover, many other organosulfur derivatives were reported to form an adduct with PbI₂ as the Pb atom acts as the Lewis acid. One such example is a volatile Lewis base, thioacetamide (CH₃CSNH₂), abbreviated as TAA [124]. Another example is 2-pyridylthiourea, which has an S donor from thiourea, with a better ability to coordinate with PbI₂, and an N donor from pyridine, which can co-ordinate with PbI₂ as a Lewis acid base and regulate the co-ordination strength with PbI₂. This further resulted in an improvement in crystallinity, which in turn resulted in better light-harvesting ability, charge transport, the reduction of defect and recombination loss, leading to PCE of 18.2%. In addition, this allowed retaining the stability of PSC more than 90% when exposed to ambient conditions, at room temperature or at higher temperature in the dark [125]. Recently, Zhang and his co-workers combined thiourea with water and iodine (ITU) ions to reduce iodine defect vacancy produced during the film fabrication process. Afterwards, the grain size was found increased with ITU (3.4 um) compared to when thiourea was added (800–2000 nm), reducing the defects at grain boundaries. Moreover, PSCs with ITU additives displayed a higher V_oc, longer decay time, and longer carrier lifetime, with a lower charge recombination rate. Thus, overall, the addition of ITU resulted in improvement in PCE from 17.75% to 20.3%. In addition, the trap densities of the perovskite film significantly reduced as the ITU additive was incorporated into PSC, allowing PSC to stabilize and maintain ~80 of initial PCE after 100 h of exposure to 1.5 AMG solar irradiation and 30 days in the ambient atmosphere [126].

2.3.2. Thiocyanates

Thiocyanates (SCN⁻ containing anions) additives are another subcategory for S atom-based additives. It should be noted that thiocyanates are also considered pseudo halides. However, the role of thiocyanates in the perovskite film is very controversial. For example, Yanfa Yan et al. demonstrated that a small amount (5%) of Pb(SCN)₂ addition in the precursor can significantly increase the grain size and crystalline quality of perovskite thin films using a one-step solution process method. This increased the average PCE from 15.57 to 17.80%. It was proposed that SCN⁻ anions do not incorporate in the perovskite film. SCN⁻ react with CH₃NH₃⁺ and form volatile products HSCN and CH₃NH₂. This allows excess Pb²⁺ and I⁻ to form PbI₂ at grain boundaries that sources passivation effect [127]. On the contrary, Kim et al. demonstrated that Pb(SCN)₂ in CH₃NH₃PbI₃ partially substitutes I anions and forms CH₃NH₃Pb(SCN)_xI_3−x at lower temperatures. This phenomena was observed as not dependent on the concentration of Pb(SCN)₂. However, similar reports of enhancement of crystal size were found. Thus, it was concluded that the influence of processing temperature could affect the purity of the final perovskite film when Pb(SCN)₂ additive is used with MAPbI₃ [128]. Whereas, the addition of potassium thiocyanate (KSCN) also reported to form volatile products HSCN and CH₃NH₂, consistent with earlier mentioned results, with no traces of SCN⁻ found in the final perovskite film [127]. In the case of the KSCN additive, however, the residue was KI instead of PbI₂. Nevertheless, the authors illustrated that the final product upon KSCN incorporation was MAPbI₃, not KPbI₃, due to the smaller radius of the K cation. In addition, KI residue improves the crystal quality of perovskite film, resulting in enhancement of charge transport, reduced carrier recombination, and eliminating hysteresis [129].

Conversely, when NH₄SCN was incorporated in MAPbI₃, it was reported to form an unstable intermediate phase NH₄PbI_3−xSCN_x due to lower formation enthalpy (△Hf) of the NH₄PbI₃ over MAPbI₃, which later resulted in CH₃NH₃PbI_3−xSCN_x a mixed halide perovskite after annealing of the films [130]. Therefore, when methylammonium thiocyanate (MASCN) was introduced as an additive to the precursor, a rapid vacuum-based drying approach was used to extract volatile intermediate product, so that MAPbI₃ was formed as the final product with no traces of SCN⁻. The film fabricated, using this fabrication technique, was reported to gain grain size of more than one micrometer with uniform surface morphology, resulting in high crystallinity and significantly large carrier lifetimes (τ1 = 931.94 ± 89.43 ns; τ2 = 320.41 ± 43.69 ns), improving the ambient stability up to 1000 h [131]. However, when a larger cation guanidinium (Gu) was directly added in MAPbI₃ as GuSCN, GuPbI₃ was formed as an intermediate phase present with the MAPbI₃ phase. It was contradictory to the earlier belief and reports, which showed that Gu single-handedly could not form three-dimensional perovskite materials due to a larger ionic size (278 pm) over MA cation (217 pm). As a result, improved crystallinity, grain size, and reduced trap density were noticed further, resulting in improved PCE (from 15.57% to 16.70%) that maintained stability ~90% of the initial value after being stored for 15 days without encapsulation [132]. On the other hand, when guanidinium isothiocyanate was added in the PbI₂ precursor, with the dual step fabrication method; mixed cation perovskite was formed (GU)_x(MA)_(1−x)PbI₃ [133]. Nevertheless, most S donor atom-based additives (Figure 16) were found to influence ambient stability, as displayed in Figure 17. At a glance, a summary of additives containing S atom and their role in the MAPbI₃ framework are presented in Table 8.

2.4. Alkane Additives

Alkane-based additives are another class of additives that was briefly investigated within the MAPbI₃ framework. Additives such as poly(vinylidene fluoride-co-hexafluoropropylene) (PVDF-HFP) have shown interaction with MA cation via hydrogen bonding with fluorine atoms in the additive. Such an additive is quite useful for indoor photovoltaic applications, as the additive is reported to control the nucleation and growth rate on a very thin (~150 nm) active layer of MAPbI₃ through a one-step solution processing method. Thinner light absorber perovskite is usually full of voids, results in a low fill factor, and lower internal quantum efficiency due to poor perovskite film quality. However, increasing the thickness is not suitable to obtain semi-transparent films [134]. As a solution to this problem, a poly(vinylidene fluoride-co-hexafluoropropylene) (PVDF-HFP) additive illustrated less rough morphology when a ~150 nm thick perovskite layer was obtained. In addition, it was found that perovskite solar cells with PVDF-HFP in the active layer have a higher charge transfer rate and lower carrier recombination rate [135]. Similar observations were seen when another derivative of PVDF polyvinylidene fluoride-trifluoroethylene polymer P(VDF-TrFE) was employed in a two-step fabrication process instead [136]. Other than these additives, some other haloalkane additives, such as diiodomethane (CH₂I₂) and diiodooctane (C₈H₁₆I₂), were also reported to reduce the trap states, resulting in improved morphology and enhanced PCE [137,138]. The chemical structures of alkane additives are shown in Figure 18. Further, Table 9 summarizes their role in the MAPbI₃ framework.

2.5. Quantum Dot-Based Additives

Recently, a new area of additive engineering has emerged, based on quantum dots containing different functional groups introduced in the precursor. This allows the functional group to chelate under coordinated Pb vacancy or iodine defect sites at the surface of the perovskite layer (Figure 19). At the same time, a quantum dot improves the crystallinity of film due to the quantum confinement effect and reduces non-radiative recombination centers; thus, passivating defects at grain boundaries [139,140,141,142,143,144]. In some cases, quantum dots can even promote charge transfer from the oxide surface to the perovskite layer, further reducing the charge trap density, boosting fill factor as high as 84% and efficiency as 21.04% [143,145]. The influence of incorporation of QDs onto the stability is shown in Figure 20. A summary of such additives based on quantum dots (QDs) is presented in Table 10.

3. Inorganic Additives

Inorganic salts can be further explained as per the category in the periodic table, i.e., based on alkali metals, alkaline earth metals, transition metals, other metals, and other non-metals. These additives may exist in the form of inorganic halide salts or inorganic acids [146].

3.1. Alkali Metals Additives

Hydro halides are at the top, as hydrogen is the first element in group one of the periodic table. Soe et al. studied the incorporation of hydrohalic acids (HX, X=I, Br, Cl) in MAPbI₃ precursor prepared using DMF. It was found that HX incorporation in the perovskite layer alters the bandgap and unit cell parameters. The HI addition compressed bandgap, whereas HBr widens the bandgap at high concentrations (20–25 vol%). Further, these changes were found correlated with the types of defects present in polycrystalline perovskite thin films combined with the structural strain induced in very small crystallites. Thus, it was concluded that these acids could influence crystallization rate, surface coverage, and improve morphology. However, HCl incorporation showed no influence on bandgap [147,148]. The same was verified by Yan and co-workers who investigated HI (hydroiodic acid) as an iodine quencher in MAPbI₃ precursor solution (prepared with isopropyl alcohol (IPA)), that further lead to chemically passivate grain boundaries and increase in PCE from 16.13% (pristine) to 18.21% (with HI additive) [149]. Likewise, alkali metals, such as Li, Na, and K, combined with halogen counterparts, have been inspected as additives for the MAPbI₃ light absorber layer. Grätzel and Friend co-workers demonstrated the influence of NaI (sodium iodide) on the optical, excitonic, and electrical properties of CH₃NH₃PbI₃ perovskite prepared by a two-step sequential deposition technique. It was revealed that the NaI additive helps in the complete conversion of PbI₂ into CH₃NH₃PbI₃, leaving no unreacted PbI₂ and enhancing the crystallinity. Furthermore, KPFM measurements showed a reduction in work function (towards Au metal) for contact-potential difference (CPD) and proved the chemical passivation of perovskite surface due to additive incorporation in the precursor. Additionally, the hypothesis of partial substitution of Pb²⁺ with monovalent cations Na was discarded, because replacing Pb²⁺ with the Na cations required high energy, which could not be obtained at room temperature, since additives and films were processed at room temperature [150]. Similar reports were published from Chu and co-workers who investigated alkali metal chloride additives (LiCl, NaCl, and KCl) in MAPbI₃ and suggested that mixed halide formation does not occur as Cl atoms easily evaporate due to the annealing process, improving the crystallinity and carrier charge transport [151]. However, as the size of the nuclei increases, the perovskite shows partial replacement and forms a perovskite with a double cation (i.e., in the case of RbX and CsX, where X represents halide) [152]. The partial substitution of cation was also observed when alkaline earth metals were employed as additives in the precursor. Hence, they are not the center of attraction here and it is suggested that alkaline earth metals are best suited to replace Pb due to their divalent nature [153,154]. The chemical structures of alkali metal additives are presented in Figure 21. The example of the influence of alkali metal additives on the stability of MAPbI₃ PSC is shown in Figure 22. Further, the role of alkali metal additives in the MAPbI₃ framework is summarized in Table 11.

3.2. Transition Metals Additives

Additionally, some transition metals were also reported as additives in MAPbI₃ precursor. One such example is n-type goethite (FeOOH) quantum dots that act as multifunctional additives. The addition of FeOOH QDs into precursor solution improves not only the performance, but also stability. The investigation by Wang and et al. showed that FeOOH QDs could produce heterogeneous nucleation, passivate the trap states, and obstruct the ion migration. The investigation demonstrated that the oxygen (in FeOOH) as a Lewis base could coordinate with Lewis acid Pb²⁺. The –OH group (in FeOOH) can coordinate with hydrogen atoms of MA⁺. This interaction delays crystal growth kinetics, resulting in good quality of perovskite films that result in high PCE. Further, the iron in FeOOH QDs as a Lewis acid interact with Lewis base I⁻. Thus, ion migration of I⁻ and MA⁺ is controlled, resulting in enhanced intrinsic stability of solar cells [157]. Further, the transitional metal halides, either with monovalent cations (i.e., AgI, CuI, CuBr), divalent cation (NiCl₂, CuCl₂, ZnCl₂, CdCl₂) [158,159,160,161], or trivalent cation (RhI₃) [162] frequently pointed out the improvement in crystallinity and grain boundary passivation.

Interestingly, in all these reports, chlorine-based additive salts were reported to form the MAPbI₃ phase without mixed iodide and chloride as it was proposed that Cl atoms evaporate while annealing the films. Similarly, trivalent cation, such as Rh³⁺, did not replace lead atoms when used in small quantities (e.g., 1 mol%). However, the addition of 5% could result in partial replacement of the Pb atom. Figure 23 and Figure 24 demonstrate the chemical structures and the effect of transition metal additives on the stability of MAPbI₃ PSC, respectively. Further, Table 12 summarizes the details associated with transitional metal additives.

3.3. Other Metals Additives

However, the most widely reported metal additive is PbI₂. Several groups have suggested using excess PbI₂ as an additive and studied the effect of the stoichiometric and non-stoichiometric composition of PbI₂ in MAPbI₃ perovskite [163,164]. Reports suggest that the addition of excess PbI₂ in perovskite increases power conversion efficiency [163,165]. However, the influence of excess PbI₂ on photochemical stability is debatable [166]. Some research groups claim that excess PbI₂ passivates grain boundary [167]; thus, creates extra passivation [168]; enhancing performance and stability overall [164,169]. On the contrary, some reports showed that excess PbI₂ could increase PCE, but decreased PSC stability [170,171]. To resolve the issue, Stevenson et al. demonstrated that the stability associated with excess PbI₂ is affected by solvent coordination capacity with Pb atom, and suggested that excess PbI₂ can work as a stabilizer to improve intrinsic stability if the correct solvent (NMP) is chosen over commonly-used solvent DMF [172]. Other than PbI₂, adding PbCl₂ also resulted in an equally good perovskite film quality with improved performance, but the outcome was reported as a mixed halide [173,174]. Hence, it is not focused on here. Interestingly, Ngo and the group demonstrated a different approach by using PbS quantum dots as capping ligands in the precursor solution to control nucleation and morphology. This approach allowed improving crystallinity and enhanced grain size, resulting in improved solar cell performance [175]. See Figure 25 for the chemical structures of PbI₂ and PbS. The influence of excess PbI₂ additive on the stability of MAPbI₃ is presented in Figure 26. Further, a relevant summary is presented in Table 13.

3.4. Non-Metal Inorganic Salts

Furthermore, the controlled nucleation, improved morphology, enhanced crystalline size, and grain size with lower trap density were also noticed with additives based on other non-metals salts. During the two-step method, which is one of the commonly used fabrication approaches to fabricate planar heterojunction complex lead halide perovskite solar cells, the complete conversion of PbI₂ into CH₃NH₃PbI₃ is often observed restricted by the inadequate diffusion of CH₃NH₃I into PbI₂ film, which affects the short circuit current density. To overcome this problem, Pathipati and co-workers used ammonium iodide (NH₄I) in a small quantity (5 wt%) in the PbI₂ solution and found this approach increases the porosity of the PbI₂ film, allowing to improve film morphology and increase grain size up to 500 nm. This, in turn, improves the fill factor and short circuit current density, improving the PCE compared to the pristine solar cell [177]. Similarly, a drastic improvement in fill factor (from 27.53 without additive to 80.11 with NH₄Cl additive) was noticed when NH₄Cl was added in the MAPbI₃ precursor. Moreover, as reported earlier, due to the quick evaporation of chlorine atoms, mixed halide formation did not take place [178]. Furthermore, improved performance and higher stability were observed with different ammonium halide salts (NH₄X, where X can be I, Cl, Br) even when using the single-step solution process method. Although, NH₄I showed the highest performance amongst all [177,178,179]. Another ammonium-based additive, NH₄H₂PO₂ (ammonium hypophosphite-AHP), was reported to show similar behavior. Surprisingly, one of the by-products (H₃PO₂) from CH₃NH₃I synthesis was found suppressing the formation of molecular iodine (i.e., the oxidation of I⁻ to I²) [180,181]. This led to the idea of using NH₄H₂PO₂ (ammonium hypophosphite-AHP) as an additive in the PbI₂/CH₃NH₃I precursor. Huang and co-workers found that AHP forms a complex with PbI₂, which leads to improvement in crystallinity and grain size. In turn, this improves PV performance due to crystalline grain boundaries [182]. Moreover, in a recent report, it was illustrated that hydrazinium iodide (N₂H₅I), an iodine quencher in the MAPbI₃ active layer, can form an intermediate complex with PbI₂, and enhance crystallinity and grain size ~1100 nm, causing grain boundary passivation. This, in turn, reduces hysteresis in solar cells, improves efficiency, and intrinsic stability of solar cells up to 4400 h [183]. There were similar reports by Huang et al., who reported hydrazinium chloride (N₂H₅Cl) incorporation in MAPbI₃ [184]. Whereas hypophosphorous acid (HPA) was used to assist crystallization dynamics for large area substrates [185]. The chemical structures and influence of non-metal inorganic additives on the stability of MAPbI₃ are presented in Figure 27 and Figure 28, respectively. A summary of these additives is presented in Table 14.

4. Conclusions and Outlook

To conclude, we covered the progress and updates in the area of additive engineering for the MAPbI₃ photoactive layer in perovskite solar cells. As known, the poor intrinsic and extrinsic stability causes a restriction in the substantial commercialization of the PSC. Intrinsic instability is considered due to the presence of under-coordinated Pb sites or escape of a volatile product or formation of molecular iodine; either of these creates a defect in the perovskite surface. Therefore, in this review, we summarized various additives that can coordinate with the mentioned defect sites and improve stability. Higher efficiency (more than 25%) was achieved, but achieving higher stability is still far away. Further, the role of additives into MAPbI₃ precursor was presented, which influences nucleation growth, film morphology, crystallinity, grain size, and grain boundary passivation via complex/intermediate formation were conferred. To understand the aforementioned, we classified additives based on organic and inorganic compounds. Furthermore, organic additives were scrutinized as per their functional group, and a relevant coordination mechanism that impacted stability was described. Similarly, inorganic additives were classified based on metal and non-metal halides. Moreover, we focused on additive influence on stability concerning different conditions (intrinsic/ambient/mechanical robustness). Our analysis suggests that amines, heterocyclic amines, and their derivatives, followed by carbonyl and acetate functional groups, can improve intrinsic stability. On the other hand, acid, esters, ether, and alcohol, and S atom-based additives can be mainly valuable to boost ambient stability. This summary of additives further aims to boost designing new additives that can finally help achieve stability challenges.

Yet, further developments are required while adopting the additive approach in the fabrication of MAPbI₃-based PSCs. So far, additives employed in the MAPbI₃ light-absorbing layer do not have any rule of selection. The majority of additives have opted from existing literature available for DSSCs or organic solar cells, utilizing the N/O/S donor atoms to combine with under-coordinated Pb²⁺ sites to improve stability because of the Lewis acid–base reaction. Hence, the first and the topmost prospect is to design an additive that can help sustain MAPbI₃ under operational conditions, such as illumination, heat, moisture, oxygen, water. To do so, applying machine learning is highly recommended. While additives are primarily being experimented on (on a trial and error basis), the number of published reports are growing exponentially, with time, without any outcome to overcome stability issues. Therefore, a systematic empirical investigation should be conducted using analytical, statistical tools to understand the correlation of the additive, its properties, and its influence on morphology, optoelectronic properties, and stability with various conditions concerning numerous characterization techniques. This might help in the suitable material selections to further experiment by establishing the relationship between the chemical structure of additives and photovoltaic characteristics and lifetime. Thus, it would reduce the time and cost required for the experiment to improve stability, eventually driving industrial interest in product development.

The second prospect includes improved operational stability, which is reported to gain only a few thousand hours. While at least 10,000 h of operational stability is required to commercialize as the indoor application, with respect to thin-film photovoltaics. On the other hand, traditional photovoltaic has a lifetime of ~25 years. Thus, the second vision is to overcome short-term stability issues to commercialize the MAPbI₃-based PSC. Moreover, the duration of operational stability should also be reproducible. Henceforth, fabricating reproducible stability is the third prospect to work on, as testing short- or long-term reproducibility is a time-consuming process. The next challenge is upscaling. Currently, the majority of research reports are based on small area devices. Nevertheless, large-area devices will be required for commercial purpose. However, morphology, performance, distribution of surface defects, grain size, and trap states will be changed when the large area will be used. Therefore, the fabrication of large-area devices is another prospect that requires high PCE and stability. Another future scope of development is in the area of toxicity of PSC. Since some precursors used to prepare MAPbI₃ ink are not environment friendly. Hence, alternative, environment-friendly green solvent/precursors should be further explored to give equally good efficiency and stability.

In the end, we hope this review will help scientists and researchers to design and synthesize new additives that can provide the solution for the stability challenge of MAPbI₃. Thus, ultimately achieving stability by applying additive engineering, commercializing MAPbI₃-based PSC can be achieved.

Funding

This research received no external funding.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interests.

Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Figures and Tables

Figure 1. Chemical structures of amine-based additives for MAPbI3 PSC.

Figure 2. Chemical structures of nitrile additives in MAPbI3 PSC.

View Image - Figure 3. Stability of MAPbI3 photoactive layer due to various additives containing N donor atom. The data are taken from references [33,34,35,39,40,41,47,48,49,50,53,54,55,56,57,59,60,61,62] respectively.

Figure 3. Stability of MAPbI3 photoactive layer due to various additives containing N donor atom. The data are taken from references [33,34,35,39,40,41,47,48,49,50,53,54,55,56,57,59,60,61,62] respectively.

Figure 4. Chemical structures of amide/carbonyl/sulfonyl based additives for MAPbI3 PSC.

View Image - Figure 5. Influence of carbonyl/sulfonyl group onto stability of MAPbI3-based PSCs. The data are collected from references [65,67,68,71,73,74,75,76,77,79,84,85] respectively.

Figure 5. Influence of carbonyl/sulfonyl group onto stability of MAPbI3-based PSCs. The data are collected from references [65,67,68,71,73,74,75,76,77,79,84,85] respectively.

Figure 6. Chemical structures of acid containing additives for MAPbI3 PSC.

View Image - Figure 7. Impact of acidic additives on the stability of MAPbI3-based solar cells. The graph is plotted using the data from references [88,89,90,91,92,93,94,95] respectively.

Figure 7. Impact of acidic additives on the stability of MAPbI3-based solar cells. The graph is plotted using the data from references [88,89,90,91,92,93,94,95] respectively.

Figure 8. Chemical structures of acetate additives for MAPbI3 PSC.

View Image - Figure 9. Influence of acetate-based organic additives onto stability of MAPbI3 perovskite. The graph is plotted with the data taken from references [98,100,102,103,104] respectively.

Figure 9. Influence of acetate-based organic additives onto stability of MAPbI3 perovskite. The graph is plotted with the data taken from references [98,100,102,103,104] respectively.

Figure 10. Chemical structures of ester and ether containing additives for MAPbI3 PSC.

View Image - Figure 11. Influence of ester and ether-based additives on the stability of MAPbI3 perovskite. The graph is plotted with data from [106,107,109,110,114], respectively.

Figure 11. Influence of ester and ether-based additives on the stability of MAPbI3 perovskite. The graph is plotted with data from [106,107,109,110,114], respectively.

Figure 12. Chemical structures of alcohol additives for MAPbI3 PSC.

Figure 13. Influence of alcohols onto stability of MAPbI3 PSK. The data to plot the graph are taken from references [115,116,117].

Figure 14. Chemical structures of oxygen-based multifunctional group containing additives.

Figure 15. Other oxygen-based additives with multiple functional groups [120,121].

Figure 16. Chemical structures of organosulfur additives for MAPbI3 PSC.

Figure 17. Influence of S donor atom onto stability of MAPbI3-based PSC [122,124,125,126,131,132].

Figure 18. Chemical structures of alkane-based additives for MAPbI3 PSC.

Figure 19. Schematic representation of quantum dots with chelating functional group/groups.

Figure 20. Quantum dots-based additives and their influence on stability of MAPbI3. Data taken from [139,141,142,145] respectively.

Figure 21. Chemical structures of alkali metal additives for MAPbI3 PSC.

Figure 22. Influence of alkali metal additives onto stability of MAPbI3. Data taken from references [151,155].

Figure 23. Chemical structures of transition metal additives.

Figure 24. Influence of transition metal additive onto MAPbI3. Data taken from references [157,158,162] respectively.

Figure 25. Chemical structures of other metal additives in MAPbI3.

Figure 26. Ambient and inert stability due to excess PbI2 [171,172].

Figure 27. Chemical structure of non-metal halide additives for MAPbI3.

View Image - Figure 28. Influence of non-metal additives onto stability of the MAPbI3 layer. Data were taken from references [177,179,183], respectively.

Figure 28. Influence of non-metal additives onto stability of the MAPbI3 layer. Data were taken from references [177,179,183], respectively.

Table 1

Investigated additives based on nitrogen donor atom containing amines or nitrile.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, %(with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
excess MAI	FTO/SnO₂/CH₃NH₃PbI₃/PCBM/Ag	15.14	N/A	17.24	molar ratio PbI₂: MAI = 1:1.05	N/A	N/A	Hot casting, improved crystallinity, decrease in defect density, increased PL lifetime	[29]
excess MAI	ITO/PCBM/CH₃NH₃PbI₃/HTL/Au	N/A	N/A	N/A	molar ratio MAI: PbI₂ = 3:1	N/A	N/A	Vacuum deposition, increased PL lifetime, reduced trap states	[30]
excess MAI	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OmATAD/Au	11.13	N/A	13.37	0.2 mM	N/A	N/A	Sequential deposition, good quality perovskite film	[31]
benzylammoniumiodide(BAI)	FTO/TiO₂/CH₃NH₃PbI₃/HTL/metal	6.83	N/A	9.05	molar ratio BAI:MAI = 0.2	N/A	N/A	Better light harvesting property and low charge recombination	[32]
phenethylammonium iodide (PEAI)	FTO/c-TiO₂/m-TiO₂/mp- ZrO₂/CH₃NH₃PbI₃/Carbon	6.3	Retained ~77% PCE after 80 days	8.60	molar ratio PEAI: MAI = 1:20	Retained 90% PCE after 80 days	air, light 100 mW cm⁻²	Better contact with TiO₂, longer exciton lifetime, good quality of perovskite film	[33]
hexylamine hydrochloride(1-HH)	Glass/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/BCP/Ag	14.37	Retained 43% PCE from initial after 16 days	15.70	0.05 wt%	Retained ~85% PCE from initial after 16 days	Unencapsulated, ambient, RT, air, RH = 10–20%	Increases grain size and passivate defects, NH³⁺ group could form N-H…I. hydrogenbond with the I- of the [PbI₆]^4- passivating“A” vacancy; hydrophobic hexane alkyl chain protects against moisture	[34]
1,6-diaminohexane dihydrochloride (1,6-DD)	Glass/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/BCP/Ag	14.37	Retained 43% PCE from initial after 16 days	17.00	0.05 wt%	Retained 90% PCE from initial after 16 days	Unencapsulated, ambient, RT, air, RH = 10–20%		[34]
phenylhydrazinium iodide (PHAI)	FTO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/Rhoda mine/Ag	14.63	(a) Retained ~53% PCE after 60 days(b) died in 20 days	17.2	10 mg mL⁻¹	(a) Retained ~90% PCE after 60 days(b) Retained ~85% PCE after 20 days	(a) unencapsulated, N₂, dark, RH = 20%, T = 26 °C(b) unencapsulated, ambient room environment, dark, 30 ± 5% RH, 24 ± 2 °C	PbI₂ and PHAI complex/intermediate formation results in passivation against vacancy defects, hydrophobic phenyl rings acts as a barrier against moisture	[35]
amphiphilic hexadecyl trimethyl ammonium bromide(CTMAB)	Glass/FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17.05	Retained 70% PCE after 40 days	18.03	10 mg CTMAB in 1 mL DMSO. Used 20 uL of this to add in 1 mL precursor	Retained 95% PCE after 40 days	Non-encapsulated, RH~40%, T = 25 °C, dark	Improved crystallinity and morphology	[39]
ethylammonium chloride (EACl)	Glass/FTO/c-TiO₂/meso-TiO₂/CH₃NH₃PbI₃/HTL/Au	17.35	Retained ~30% of the original PCE after 1000 h	20.3	2.5%, molar %	Retained ~89% of the original PCE after 1000 h	encapsulated	Improves morphology, grain boundary passivation	[40]
1,3-diaminoguanidine monohydrochloride (DAGCl)	Glass/ITO/PolyTPD/CH₃NH₃PbI₃/PC₆₁BM/ZrAcac/Ag	19.1	Retained 70% PCE after 20 days	20.3	0.6%, wt% of MAI	Retained 80% PCE after 20 days	Non-encapsulated, ambient, RH ~ 50%	Increased grain size, reduced trap density, DAG cation can bond with I⁻ via hydrogen	[41]
benzamidine hydrochloride (BMCl)	ITO/TiO₂/PC₆₁BM/CH₃NH₃PbI₃/PTAA/MoO₃/Ag	17.8	N/A	18.4	N/A	N/A	N/A	Enhance work function of perovskite film improves efficiency	[42]
acetamidine salt (AcHc)	ITO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.45	N/A	16.54	molar ratio MAI:AaHc = 1:0.08	N/A	N/A	Smooth film, full and uniform coverage, large grain size, improve carrier lifetime,	[43]
methoxyammonium chloride(MeOCl)	FTO/compact-TiO₂layer/mesoporous-TiO₂ layer/CH₃NH₃PbI₃/Spiro-MeOTAD/Ag	17.15	N/A	19.71	molar ratio PbI₂:MeOCl =1:0.10	N/A	N/A	Improvement in grain size and crystallinity	[44]
2, 2, 2-trifluoroethylamine hydrochloride (TFEACl)	Glass/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/Al	N/A	N/A	4.98	molar ratio of additive:MAI:PbI₂ = 0.4:1:1	N/A	N/A	Compact smooth high quality film	[45]
benzenamine hydrochloride(BACl)				11.07
3-chloropropylaminehydrochloride(3-CPACl)				8.21
diethylamine hydrochloride (DEACl)				9.89
4-ethylamine Phenylphosphate disodium salt (EAPP)	FTO/C-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	18.83	(a) Dead in 6 h (b) Remained 60% from initial PCE after 100 h	17.61	1 mol%	(a) Remained 90% from initial PCE after 12 h (a) Remained ~99% from initial PCE after 100 h	(a) ATM condition, RH = 80%, unencapsulated, (b) inert, N₂, unencapsulated,	Phenylethylamine group protects against moisture and improves ambient stability, phosphatesodium prevents the formation of(CH₃NH₃)₄PbI_6.H₂O	[62]
4,4’-bipyridine	Glass/CH₃NH₃PbI₃	N/A	Died in ~900 h	N/A	5 wt%	Remained active for 1400 h	inert, unencapsulated, light 70-80 mW cm⁻²_, 50-60 °C	Forms complex with PbI_2, thus slows down the formation of metallic lead	[47]
poly 4-vinylpyridine (PVP)	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	6.09	Remained 1.55% PCE as of final PCE (absolute value) after 3 weeks	13.07	0.4 wt%	Remained 6.6% PCE as of final PCE (absolute value) after 3 weeks.	Air, 50% RH, non-encapsulated	Inhibits carrier recombination, reduced defects	[61]
Polyvinylcarbazole (PVC)	ITO/PTAA/CH₃NH₃PbI₃/PCBM/Al	17.4	Died in 1500 h	18.7	1 mass%	Retained ~70% of the initial efficiency after light soaking for 1500 h,	light 50 ± 3 mW cm⁻², 65 ± 2 °C, inert nitrogen,	Defect passivation due to interaction with lone pair of electrons from N atom with Pb²⁺	[48]
pyridine-functionalizedfullerene derivative (C60-PyP)	ITO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17.61	Retained 70% PCE after 30 days	19.82	0.13 wt%	Retained 90% PCE after 30 days	25 ℃, RH = 30%, dark, non-encapsulation,	Enlarged grain size, improved crystallization, interaction b/w N atom of the pyridine moiety within C60-PyP and Pb²⁺ ion within MAPbl₃ leads to thepassivation of trap states of perovskite layer, hydrophobic nature of C60-PyP molecule increases ambient stability	[49]
pyridine-2-carboxylic lead salt (PbPyA₂)	ITO/P3CT-N/CH₃NH₃PbI₃/(PCBM)/C₆₀/(BCP)/Ag	18.86	(a) Retained 20% ofPCE after 480 h (b) retained 20% of PCE after 540 h(c) retained 30% of PCE from initial after 480h	19.96	4 mg mL⁻¹	(a) Retained 80% PCE after 480 h (b) retained 93% of initial PCE after 540 h(c) retained 90% PCE from initial after 480h	(a) 90 °C, RH = 40–60%, dark, not encapsulated, (b)MPP- tracking, non-encapsulated, white light-100 mW cm⁻², inert, 25 °C, (c) Air, non-encapsulated, dark,RH = 40–60%	Controlled crystallization, passivation of grain boundaries, the interaction of pyridine and carboxylate to cations increases hydrophobicity	[50]
polyvinylpyrrolidone (PVP)	Ito/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.33	Retained 76% from initial PCE after 400 h	15.19	1 mg mL⁻¹	Retained 80% of the initial PCE after 60 days	encapsulated, ambient, RH = 10%, RT	Lewis base, the pyridine part (side chain) of the PVP polymer, can passivate the surface defects caused by misaligned lead ions and can fill the iodine vacancy traps on the surface of the perovskite film, C=O also stabilizes, allows not to degrade	[36]
NMP	FTO/ZnO-MgO-EA+/mesoporous-TiO₂/CH₃NH₃PbI₃/spiro-OMeTAD/Au	18.0	N/A	19.2	molar ratio PbI₂:NMP =1:2	N/A	N/A	The same kind of intermediate, regardless of NMP ratio, results in excellent morphology	[51]
NMP	Glass/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/Al	1.50	N/A	7.03	60 μL in 1 mL precursor	N/A	N/A	Lewis acid base interaction	[52]
NEP				10.04				-
CHP				12.87				Suppression of solvate formation
NOP				2.79				Lewis acid–base interaction
DMI	FTO/compact-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	10.72	N/A	14.54	10 vol%	N/A	N/A	Pb-O bond formation due to Lewis adduct between DMI and Pb	[63]
1-(4-ethenylbenzyl)-3-(3,3,4,4,5,5,6,6,7,7,8,8,8-tridecafluorooctylimidazolium iodide (ETI)	FTO/C-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	19.2	(a) Retained 49% PCE from initial 700 h(b) Retained 60% PCE from initial 700 h	19.5	1 mol%	(a)Retained 85% PCE from initial 700 h(b) Retained 80% PCE from initial 700 h	(a) MPPT inert, 60 °C, light 100 mW cm⁻², unencapsulated,(b) RH = 40%,RT, dark, air	Enables the full transformation into precursor,suppresses thermal decomposition pathway and, provides outstanding hydrophobicity within theactive material	[53]
1-methyl-3- propylimidazolium bromide (MPIB)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag.	15.9	retain ~50% of its original PCE after 150 h	18.2	0.5 mgmL⁻¹	retain 78% of its original PCE after 150 h	atmospheric environment, RT,	Passivation of the uncoordinated Pb²⁺ to reduce the defects in the perovskite film dueto the lone-pair electron in its cation group, and beneficial to promote crystal growth to improve film quality	[54]
1-butyl-3- tetrafluoroborate(BMIMBF4)	ITO/NiO_x/CH₃NH₃PbI₃/C₆₀/Ag	18.13	retaining 30% of their initial PCE after thermal ageing of 400 h at 85 °C	18.07	0.4 mol%	retaining 80% of their initial PCE after thermal ageing of 400 h at 85 °C	85 °C,unencapsulated	Thermal stability by effective suppression ofperovskite decomposition	[55]
Spiro-OMeTAD	FTO/Den TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.52	N/A	17.77	0.01 wt%	N/A	N/A	Facilitates charge transport	[64]
triazine-graphdiyne (Tra-GD),	ITO/P3CT-K/CH₃NH₃PbI₃/PC₆₁BM/ZnO/Al	17.90	Died in 1100 h	20.33	2 mg mL⁻¹	Retain above 90% after 1100 h	Unencapsulated	Interacts with Pb²⁺ at grain boundaries and passivates grain boundaries and inhibits ion migration	[56]
graphitic carbon nitride(g-C₃N₄)	FTO/compact TiO₂/CH₃NH₃PbI₃/Spiro-MeOTAD/Au	18	Retained 46% PCE after 300 h	21.6	0.1 wt%	Retained 90% PCE from initial after 500 h	Encapsulated, light 100 mW cm⁻²	Improves grain size and crystallinity, passivates grain boundaries, C=N to interact with Pb²⁺ that forms compact tight bonding resulting in good morphology	[57]
graphitic carbon nitride (g-C₃N₄)	FTO/compact TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/MoO₃/Ag	16.22 ± 0.83	N/A	19.34 ± 0.63	0.4 mg mL⁻¹	N/A	N/A	Passivation, enhanced crystallinity, C=N to interact with Pb²⁺, increases the conductivityand carrier mobility	[58]
1,8- Diazabicyclo[5.4.0]undec-7-ene (DBU)	Glass/ITO/NiO_x/CH₃NH₃PbI₃/PCBM/PEI/Ag	15.98	Retained 50% PCE from initial after 10 days	18.13	3% weight ratio	Retained 80% PCE from initial after 10 days	unencapsulated, inert (N₂,) mpp tracking	Iodine quencher, adduct with PbI₂ (C=N interaction with Pb²⁺), reduced defects, high-quality perovskite film	[59]
ACN	ITO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.04 ± 0.48	Remained ~20% of initial PCE after 150 h	19.7	molar ratio ACN: PbI₂ = 0.5	Remained ~60% PCE after 150 h	light 100 mW cm⁻² RH = 60%–90%, in air without encapsulation	Morphology enhancement	[60]

Table 2

A summary of additives containing amides/carbonyls/sulfonyl functional group in MAPbI₃ active layer.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
urea	Glass/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCMB/BCP/Al	15.1	Retained ~35% from original PCE after 2 h	17	molar ratio urea: lead acetate = 0.5	Retained ~60% from original PCE after 2 h	light, 100 mW cm⁻², 50–60 °C, inert, unencapsulated	Interaction of carbonyl group of urea with PbI₂ results in crystalline film, resulting passivation and improvement in stability	[65]
urea	ITO/PEDOT:PSS/PbI₂/MAI/PCBM/BPhen/Ag	12.75	N/A	18.01	5 wt%, wt% of PbI₂	N/A	N/A	Double step spin coating, urea and PbI₂ together form PbI₂.O=C(NH₂)₂ complex/intermediate, resulting big flat grains	[66]
urea	FTO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.48	Remained 50% from original PCE after 60 days	18.52	20 mol%	Remained 80% from original PCE after 60 days	air, 50% humidity, without any encapsulation	PbI₂-urea adduct results increment in grain size and passivate grain boundaries	[67]
urea	ITO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	16.80	a) Retained 10% PCE as of final PCE after ~27 daysb) retained nearly 90% PCE from initial after 60 min	18.5	4 mol%	(a) Remained 12% PCE as of final PCE after ~27 days(b) retained nearly 100% PCE from initial after 60 min	mppt tracking (a) dark, ambient,(b) 1 sun, in-situ	Adduct formation, high crystallinity, good film, suppress non-radiative recombination and passivates grainboundaries	[68]
formamide	FTO/c-TiO₂/mp-TiO₂//CH₃NH₃PbI₃/ZrO₂ layer mp-ZrO₂/carbon electrode	14.26	N/A	15.21		N/A	N/A	the amide additives shifted the Fermilevel of the MAPbI₃ perovskite from −4.36 eV to −4.63,−4.65, and −4.61 eV, respectively for formamide, acetamide and urea and suppressed non-radiativerecombination. Reduced iodide defects vacancy	[70]
acetamide				15.57		N/A	N/A
urea				15.07		N/A	N/A
biuret	FTO/TiO₂/CH₃NH₃PbI₃/PCBM/Ag	18.26	Maintains ~50%PCE after 12 days	21.16	2 mol%	Preserves 94% of its initial efficiency after 12 day	85 °C, N₂, inert, non-encapsulated,	Increased grain size, reduced trap state, additive acts as Lewis base and interacted with uncoordinated Pb²⁺,improves the thermal stability	[71]
urea	Glass/ITO/NiO_x/CH₃NH₃PbI₃//PC₆₁BM/Ag	15	N/A	18.6	0.05 mmol	N/A	N/A	Passivate the defects and eliminate non-radiative charge recombination due to adduct with PbI₂	[72]
biuret				20.1		N/A	N/A
triuret				19.2		N/A	N/A
benzoquinone (BQ)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/C₆₀/BCP/Au	10.7	Remained ~50% PCE from initial after 900 h	15.6	0.5 mol%	Remained ~80% PCE from initial after 1000 h	unencapsulated, light 1 sun, open circuit, without UV-filter	Reduces trap density	[73]
benzoquinone (BQ)	FTO/TiO₂/CH₃NH₃PbI₃/SpiroOMeTAD/Au	17.37	(a) Dead in 1200 h (b)Dead in ~800 h	18.01	0.25%	(a) Retained 75% PCE from initial after 2400 h(b) Retained ~30% PCE from initial after 1200 h	unencapsulated, without UV-filter (a) RH ~ 20%, RT,(b) ambient air, RH = 40 - 70%, RT	Improves crystal quality, passivate grain boundary, reduce trap states, suppress PbI₂ formation at GB	[74]
triazine perylene diimide (TPDI)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/Ag	8.32	Retained 30% from initial PCE after 400 h	10.84	1.2 mg mL⁻¹	Retained 60% from initial PCE after 400h	Non-encapsulated, ambient	Minimize grain boundary defects and enhance the coverage and crystal grain sizes	[75]
3,4-Dihydroxybenzhydrazide (DOBD)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/C_{6 0}/BCP/Al	14.47	Retained 70%PCE from initial after 35 days	17.58	3 mg mL⁻¹	Retained 85%PCE from initial after 35 days	Non-encapsulated, inert, dark	Increases grain sizeand decrease of grain boundaries, both of which facilitate chargetransportation and suppress charge recombination, due to Lewis acid–base interaction between Pb²⁺ and C=O	[76]
Isatin-Cl	ITO/PTAA:F4TCNQ/CH₃NH₃PbI₃/PCBM/Al	18.13	(a) Retained 60% PCE from initial after 350 h.(b)Retained 30% PCE from initial after 24 h	20.18	0.0001 wt%	(a) Retained 95% PCE from initial after 350 h.(b) Retained 75% PCE from initial after 24 h	unencapsulated, (a) in ambient air, RH = 45%, room temperature,(b) in nitrogen atmosphere at 85 °C	The carbonyl groups and hydrogen-bond structureson Isatin-Cl passivate the defect states in the perovskitegrain boundaries and improved charge transport, suppress charge recombination, hydrophobic ring attached to Isatin-Cl improves stability against humidity	[77]
polycaprolactone (PCL)	glass or PET/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag	10.52	Retained 32% of initial PCE (10.12%) after 300 bending cycles	14.49	0.025 wt%	Retained 90% of initial PCE (10.12%) after 300 bending cycle	mechanical bending stability	Carbonyl (C=O) and Pb²⁺ bond helps the uniform coverage of perovskite, which avoids the defects and achieve the grain boundary regulation on flexible PSC	[78]
IDIS-Th	ITO/P3CT-N/CH₃NH₃PbI₃/PC₆₁BM/Bphen/Ag	17.78	(a)Retained 50% from initial PCE after 300h(b) Retained 78% from initial PCE after 200 h	20.1	0.05 mg mL⁻¹	(a) Retained 80% from initial PCE after 300 h(b) Retained 85% from initial PCE after 200 h	(a) light 100 mW cm⁻², ambient, RH = 30%, non-encapsulated, (b) 85 °C, inert, dark,	Passivate grain boundary, reduce charge recombination, adduct between additive and under coordinatedPb ions can effectively inhibit ion migration andmoisture diffusion to enhance the stability of PSC devices	[79]
IDIC-Th	ITO/P3CT-N/CH₃NH₃PbI₃/PC₆₁BM/Bphen/Ag	17.78		18.78	0.05 mg mL⁻¹	(a) Retained 80% from initial PCE after 300 h(b) Retained 78% from initial PCE after 200 h			[79]
NMP	FTO/TiO₂/PbI₂/MAI/Spiro-OMeTAD/Au	12.25	Died after 14 days	14.66	30% NMP in 1 mL precursor	N/A			[84]
DMSO				16.17	20% DMSO in 1 mL precursor	Retained 66% PCE from initial after 14 days	in air	Morphology control based on Lewis basicity-based, donor number and boiling point
HMPA				12.06	5% HMPA	N/A
tetramethylene sulfone (TMS)	FTO/bl-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	8.7	Retained ~70% from initial PCE after30 days	16.2	molar ratio =PbI₂:MAI:TMS= 2:2:1	Retained 80% from initial PCE after30 days	RT, RH = 10 - 40%, un encapsulated, dark	Intermediate phase via cross-linking. PbI₂ act as Lewis acid TMS with S=O group acts as Lewis base	[85]
tetrahydrothiophene oxide (THTO),	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/Al	N/A	N/A	12.1	molar ratio THTO:Pb = 3:1	N/A	N/A	Additive alters the nucleation and growth processes, lowered the free energy of the precursor by incorporating a sulfoxide (S=O), whichstrongly interacts with MAPbI₃ precursors, allowing an unprecedented degree of control over thenucleation density and growth rate.	[86]

Table 3

A summary of acid additives for the MAPbI₃ active layer.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
5-aminovaleric acid (5-AVA)	ITO/C₆₀/CH₃NH₃PbI₃/PTAA/Au	15.4	N/A	13.7	5% wt	N/A	N/A	Larger grain size, improved crystallinity, improved mechanical robustness	[87]
amino valeric acidAVA	FTO/compact TiO₂/mesoporous TiO₂/mesoporous ZrO₂/mesoporous carbon	11.1	Died in 110 h	9.1	molar ratio AVA: MAI=3%	Retained 50% PCE from initial after 110 h	RH = 15%, 1 Sun, non-encapsulated,	AVA located at grain boundaries isable to passivate surface defect sites, resulting in enhanced resistivityto oxygen-induced degradation.	[88]
5-ammonium valeric acid iodide (5-AVAI)	FTO/TiO₂/CH₃NH₃PbI₃/ZrO₂/Carbon	N/A	N/A	6.68	0.072M of AVAI	5.62% PCE as of final PCE after 75 days	ambient,	Big area 0.25 cm², lower charge transport resistance	[89]
aminovaleric acid iodide (AVAI)	TiO₂/ZrO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	~7	N/A	~9	AVA:PbI₂= 3 mol%	N/A	N/A	Controls ion migration-	[96]
aminopropanoic acid (APPA)	ITO/PTAA/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag,	17.51	Remained 6% as of absolute value of PCE after 90 days	19.23	weight ratio MAI:APPA= 0.56	Remained 13% as of absolute value of PCE after90 days	unencapsulated, RH = 10%	Smaller grain size, smooth surface, suppress non-radiative charge recombination, resulting in enhanced J_SC and V_OC	[95]
Polyacrylic acid (PAA)	FTO/NiO_x:Zn/CH₃NH₃PbI₃/PC₆₁BM/bathocuproine (BCP)/Ag	10.3	Retained 60% from initial PCE after 24 days	14.9	5 mg mL⁻¹	Retained 80% from initial PCE after 24 days	RT, air, ambient, RH ~ 30 ± 5%, non-encapsulated	Using the doctor blade method, a smooth, uniform, and pin-hole free film of high electronic quality, passivate defects in large area devices (1 cm²)	[90]
thioctic acid (TA)	FTO/ c-TiO₂/TiO₂-Poly(TA)/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17.4	(a) Died after 180 min(b) Died after 400 hc) N/A	20.4	20 mg mL⁻¹	(a) Retained 98% of its original PCE after 450 min(b) 97% PCE after 2100 h (c)retained 92% PCE from initial after 600 h	(a) under UV irradiation (35.8 mW cm⁻²).(b) air, RH = 50 ± 10%, (c) mppt, inert,1.5 AMG	Carboxylic acid moieties binds at TiO₂ surface. Then five-membered ring-containingthe dynamic covalent disulfide is bonded to the other end ofthe molecule through the thermal-initiated ring-opening, and interacts with Pb, forming high-quality perovskite film due to the Lewis acid–base reaction between S and Pb²⁺. Extra passivation on TiO₂ helps for efficient charge extraction and stability under UV illumination and ambient conditions	[91]
terephthalic acid (TPA)	FTO/compact-TiO₂/CH₃NH₃PbI₃/Carbon layer	11.5 ±0.67	(a)Retained 81% PCE from initial after 21 days(b) ~6% PCE as of final PCE after 700 h(c) retained 79% PCE from initial after 40 min	14. 29 ± 0	8 mg mL⁻¹	(a) Retained 94% PCE from initial after 21 days(b) 10.7% PCE as of final PCE after 700 h(c) retained 90% PCE from initial after 40 min	(a) unencapsulated, air, RH = 35%, 25 °C, ambient, dark, (b) 60 °C(c) 365 nm UV illumination 250 mW cm⁻²	(–COO⁻) from TPA can strongly attract Pb²⁺ ions crosslinking additive within perovskite, resulting in compact, dense improved morphology,the rigidity of the phenyl skeleton allows moisture and thermal resistance	[92]
trimesic acid (TMA)	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	14.27	(a)Retained 49% from initial PCE after 10h(b) retained 46% from initial PCE after 20 days	17.21	1.0 mol L⁻¹ PbI₂precursor solution	(a) Retained 49% from initial PCE after 10 h(b) retained 71% from initial PCE after 20 days	(a) 100 °C, air, ambient, dark, non-encapsulated, (b)RT, air, RH ~ 30%, dark, non-encapsulated,	TMA with abenzene ring and three carboxyl groups maintained stability. The strong hydrogen bondbetween the hydroxyl group and iodide to suppress the loss of iodide ion, preventing the perovskite from decomposing. Moreover, the benzene ring with rigidity and the π-π bond effect, and the hydrophobic alkyl chains further protects the perovskite from reacting with water	[93]
3,3’,5,5’-azobenzene-tetracarboxylic acid(H₄abtc)	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	14.25	(a) Remained 25% after 20 h(b) retained 66% of its initial PCE after 30 d	17.67	2.0% (mass ratio with respect to PbI₂	(a) Remained 61% after 20 h(b) retained 84% of its initial PCE after 30 d	(a) 100 °C without encapsulation, air, light 100 mW cm⁻² (AM 1.5), (b) RT, RH = 30%without encapsulation.	High-quality perovskite film, H4abtccan passivate grain boundaries by reacting with the lead cation, therefore leading to good thermal stability and anti-moisture of perovskite films due to rigidity of the benzene ring and azo bond	[94]
4-methylbenzenesulfonic acid (4-MSA)	FTO/bl-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au.	14.05	N/A	17.58	6 mg mL⁻¹	N/A	N/A	Improved performance, reduced hysterias, improve J-V characteristics, the sulfonic group is chemically bonded tomp-TiO₂ and phenyl backbone has p-conjugated structure. J_sc and V_oc of 4-MSA doped PSC are enhanced.	[97]

Table 4

Acetate-based additives in MAPbI₃ active layer.

Additive in Active Layer	architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
formamidine acetate salt (FAAc)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/Al	12.13	(a) N/A(b) N/A	16.59	5 mol%	(a) Retained 90% PCE from initial after 30 days(b) 16.10 as of final PCE after 320 s @ (0.87 V)	inert, unencapsulated,	controlfilm morphology and crystallinity, improves optical andelectrical properties reduceshysteresis	[98]
methylammonium acetate (MAAc) and thiosemicarbazide (TSC), combined	FTO/NiO/CH₃NH₃PbI₃/PCBM/Ag	N/A	N/A	19.19	10–15% MAAc (molar ratio)3–5% TSC (molar ratio)	(a) Retained 90% PCE from initial after 1000 h (b) Retained 80% PCE from initial after 500 h	(a) light AM 1.5, 25 °C andRH < 25%, mppt(b) dark, 85 °C, RH < 25%	large-area (aperture area of 1.025 cm²) using one step solution process, high crystalline quality of film	[100]
ammonium acetate (NH₄Ac)	FTO/TiO₂/CH₃NH₃PbI₃/spiro-OMeTAD/Au	13.82	N/A	17.02	10 wt%	N/A	N/A	Improved film morphology and increased surface coverage	[101]
ammoniumacetate CH₃COONH₄ (NH₄Ac)	FTO/TiO₂/CH₃NH₃PbI₃/carbondevices	11.11	Remained 60% from initial PCE after 1900 h	13.9	molar ratio MAI/PbI₂/NH₄Ac 1:1:x = 0.08%	Remained 96% from initial PCE after 1900 h	Dark, RH = 40%	Carbon electrode-based device, improved crystallinity	[102]
zinc acetateZn(CH₃COO)₂ (ZnAc₂)	FTO/TiO₂/CH₃NH₃PbI₃/carbondevices	11.11	Remained 60% from initial PCE after 1900 h	12.30	molar ratio MAI/PbI₂/ZnAc₂ 1:1−x:x = 7%	Remained 89% from initial PCE after 1900 h	Dark, RH = 40%	Carbon electrode-based device, improved crystallinity	[102]
lead acetate (PbAc₂)	Glass/ITO/PTAA/CH₃NH₃PbI₃/PCBM/BCP/Ag	17.25	Retained 80% PCE from initial after 20 days	19.07	molar ratio PbAc₂/PbI₂=3%	Retained 95% PCE from initial after 20 days	unencapsulated, inert	PbAc₂ additive aids cross-linking to form a strong hydrogen bond with MAI, leading to a morestable perovskite intermediate phase, retards crystallization process, resulting, perovskite thin films with better morphology and larger grains	[103]
barium acetate (BaAc₂)	ITO/P3CTN/CH₃NH₃PbI₃/PC₆₁BM/C₆₀/BCP/Ag	18.99	Retained only 20% from initial PCE after 400 h	19.82	2 mg mL⁻¹	Retained 90% from initial PCE after 400 h	Non encapsulated, inert, 90 °C, dark,	suppression of ions migration, high quality perovskite film, grain boundary passivation	[104]

Table 5

Ester and ether-based additives for MAPbI₃ and their role.

Additive in Active Layer	architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
[6,6]-phenyl-C₆₁-butyric acid methyl ester	FTO/c-TiO₂/m-TiO₂/mZrO₂/CH₃NH₃PbI₃/m-carbon	8.58	N/A	12.36	0.25 mg mL⁻¹	N/A	N/A	Improved morphology, intermediate formation between C=O of PCBM and PbI₂	[105]
PCBM	Glass/ITO/CH₃NH₃PbI₃/PCBM/BPhen/Ag	13.94	Retained ~9% (absolute value) as of final PCE after 10 days	15.94	3.5 mg mL⁻¹	Retained ~12% (absolute value) as of final PCE after 10 days	without encapsulation, ambient RH = 25–50%,	Improves crystallinity, passivates defects, suppress non radiative recombination	[106]
C₆₀ -Ta				16.46	1.5 mg mL⁻¹	Retained ~12% (absolute value) as of final PCE after 10 days
C₆₀				16.59	0.1 mg mL⁻¹	Retained ~11% (absolute value) as of final PCE after 10 days
poly(propylene glycol) bis(2-aminopropyl ether) (PEA)	FTO/c-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17.18	Maintains ~55% of its original PCE after 30 days	18.87	1 wt%	Maintains 95% of its original PCE after 30 days	dark, ambient, air, RH = 30 ± 5%	Grain boundary passivation, the oxygen atom from ether in PEA, acts as a crosslinking agent, reduces trap density and hysteresis	[107]
jeffamine	ITO/NiO_x/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag	14.5	Showed major cracks	16.8	0.05 wt%	Retained original morphology	10 cycles of stretching at 30% strain	Defect passivation through Lewis acid–base reaction of N atom and O atom with Pb ²⁺/or interaction of MA⁺ and hydrogen bond of Jeffamine decrease trap density,enhances the ductility of the perovskite film to prevent cracking during stretching	[108]
ethyl cellulose (EC)	FTO/c-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/MoO₃/Ag	17.11	Completely died in 30 days	19.27	0.1 mg mL⁻¹	Retained 80% PCE from initial after 30 days	non –encapsulated, dark, ambient, air, RH = 45%	Hydrogen bonding between EC and MAI passivates defects at the grain boundary, reduces hysteresis and improves stability	[109]
tetraethyl orthosilicate(TEOS)	TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	15.96	Retained 73% of its initial PCE after 28 days	18.38	0.3 mol%	Retained 77% of its initial PCE after 28 days	ambient, 25 °C, RH = 30%, non-encapsulated,	Reduce trap density, improves carrier lifetime	[110]
THF	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	11.3	Retained 35% PCE from initial after 20 days	15.1	THF: DMF (1:10) v/v	Retained 80% from initial PCE after 20 days	RH = 50%, unencapsulated,	Complex formation due to Lewis acid–base reaction	[113]
diethyl ether	Glass/ITO/NiO_x/CH₃NH₃PbI₃/PCBM/BCP/Ag	13.28	N/A	15.09	the molar ratio of 4% with matrix solvent	N/A	N/A	Grain size improvement	[114]

Table 6

Alcohol-based additives and their role in MAPbI₃ perovskite framework.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
dibutylhydroxytoluene (BHT)	ITO/PEDOT: PSS/CH₃NH₃PbI₃/PC₆₁BM/ZnO/Al	17.1	Retained 85% from initial PCE after 180 min	18.1	0.02 M	Retained 93% of initial PCE after 180 min	light 100 mW cm⁻², RT, non-encapsulated, RH < 5%	intermolecular hydrogenbonds between the MA⁺ and −OH groups of the BHTadditive improves film crystallinity, reducing the sub-Eg states and carriertraps,	[115]
methanol	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	16.53	Retained 40% from initial PCE after 30 days	19.51	5 vol%	Retained 90% from initial PCE after 30 days	Dark, ambient, nonencapsulated,	morphology control/enhancement	[116]
2-methoxyethanol ME	ITO/ZnO/CH₃NH₃PbI₃/Spiro-OMeTAD/MoO_x/Ag	14.2	N/A	16.7	30 µL to 1 mL MAI solution	N/A	N/A	two-step interdiffusion protocol to prepare pin-hole free perovskite films, glycol ethers changes the lead iodide to perovskiteconversion dynamics and enhances PCE resulting in more compactpolycrystalline films, and it creates micrometer-sized perovskite crystals vertically-alignedacross the photoactive layer	[118]
2-ethoxyethanol(EE),				13.2
2-propoxyethanol (PE)				15.1
isopropanol (IPA)	FTO/compact-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	16.02	Retained 40% PCE from initial after 40 days	19.70	precursor: IPA volume ratio = 4:1	Retained 85% PCE from initial after 40 days	unencapsulated, air, ambient, RT	morphology enhancement/control	[117]
n-butanol	FTO/CT-IO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	13.8	N/A	15.5	5.0 v% for 1 mLprecursor	N/A	N/A	morphology enhancement	[119]

Table 7

Other oxygen atom-based additives with multifunctional group.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
Reduced graphene oxide (rGO)	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	13.8	Retained 20% of their initial PCE after 50 days	16.5	9 μg mL⁻¹	Retained 40% of their initial PCE after 50 days	dark, RH = 10%, unencapsulated,	Defect-free perovskite films of enhanced crystallinity, larger and evenlydistributed grains, enhanced lightharvesting potential, increasing the photocurrent density and the resultingimproved PCE	[120]
Poly(amic acid) (PAA)	ITO/NiO_x/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag	14.16	(a) Remained 13% as of final PCE after 500 h(b) Retained 50% from initial PCE after 70h	17.85	0.0497 mg mL⁻¹	(a) Remained 16.57% as of final PCE after 500 h(b) Retained 88% from initial PCE after 70 h	Inert, dark, non-encapsulated, (b) 85 °C, RH = 45% without encapsulation, dark, in the glovebox	The O atoms in PAA andPI form hydrogen bonds with H atoms in CH₃NH₃⁺ and lone pair of electrons of N atoms interact with Pb ions,which stabilized the PVSK framework.	[121]
polyimide (PI)	ITO/NiO_x/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag	14.16		16.49	0.0990 mg mL⁻¹	N/A	N/A		[121]

Table 8

S atom-based additive in MAPbI₃.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
DS	MgF₂/PET/ITO/Nb₂O₅/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17.03	(a) Retained 50% PCE from initial after 60 days(b) N/A	18.40	10 vol% in 1 mL precursor	(a) Retained 86% PCE from initial after 60 days(b) 15.24 (83% of initial) as of final PCE after 5000 cycles	(a) unencapsulated, RH = 35%, dark, RT(b) bending stability- bending radius of 4 mm	Intermediate between Pb²⁺ and S atom	[122]
thiourea	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/Ag	13.4	N/A	16.2	0.5 vol%	N/A	N/A	Thiourea promotes grain growth, reduce trap states, passivate grain boundaries	[123]
thioacetamide (TAA)	ITO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17	Retains ~75.1% of its initial performance after aging 816 h	18.9	1.0% (molar ratio to PbI₂)	Retains 88.9% of its initial performance after aging 816 h	RH = 25–35%, unsealed, air,	Interaction of TAA with Pb²⁺improved grain size	[124]
2-pyridylthiourea	FTO/C-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.5	(a) Retained only ~10% PCE from initial after 30 days(b) Retained~55% PCE from initial after 30 days	18.2	0.5 mg mL⁻¹	(a) Retained~95% PCE from initial after 30 days(b) Retained~92% PCE from initial after 30 days	ambient,air, dark(a) RH = 55 ± 5%, dark, RT(b) 65 °C, RH = 30%,dark	N-donor and S-donor coordinate with PbI₂ and slow down the formation of PbI₂. improved morphology, larger crystalline size, smooth compact, homogeneous film	[125]
ITU for I− and thiourea	ITO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	17.75	Retained 30% of the initial PCE after 100 h	20.3	0.003 mM	Retained 80% of the initial PCE after 100 h	AM 1.5 light, ambient atmosphere	Reduction of iodine ions and reduces defect state concentration, and defect passivation of grain boundaries crystalline quality, improve charge transport	[126]
lead thiocyanate Pb(SCN)₂	FTO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.57	N/A	17.80	5% Pb(SCN)₂ (molar ratio with respect to PbI₂	N/A	N/A	Forms volatile products HSCN and CH₃NH₂, resulting in formation of excess PbI₂ that passivates GB	[127]
potassium thiocyanate(KSCN)	FTO/c-TiO₂/m-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	19.38	N/A	19.6	1 mol%	N/A	N/A	Grain size and crystallinity improvement reduced recombination density	[129]
methylammonium thiocyanate (MASCN)additive	Glass/FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.81	Died in 150 h.	18.71	40 mol%	Retained 16.34% as of final PCE after 1000 h ~89.7% from initial	air, RH = 20–25%, withoutencapsulation,	Rapid vacuum-based drying approach, high crystallinity, large carrier lifetimes	[131]
guanidinium thiocyanate (GuSCN)	FTO/TiO₂/CH₃NH₃PbI₃/PCBM/Ag	15.57	Retained 60% PCE from initial PCE after 15 days	16.70	10% mmol	Retained 90% PCE from initial PCE after 15 days	unencapsulated, dark, RH = 30–40%,	Enhance the crystallinity, enlarge the crystal size, and reduce the trap density of theperovskite film	[132]

Table 9

Alkane-based additives and their role within MAPbI₃ framework.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
poly(vinylidenefluoride-co-hexafluoropropylene) (PVDF-HFP)	FTO/cTiO₂/CH₃NH₃PbI₃/Spiro-MeOTAD/Au	7.2	N/A	10.6	N/A	N/A	N/A	Interact with uncoordinated MAI molecule through hydrogen bonds between fluorine atoms. This can improve the carrier lifetimes and reduce the charge transfer resistance, whichcontributes to enhancing PCE	[135]
polyvinylidene fluoride-trifluoroethylene polymer P(VDF-TrFE)	FTO/c-TiO₂/mesoporous-TiO₂/CH₃NH₃PbI₃/Spiro-MeOTAD/Ag	9.57 ± 0.25%	N/A	12.54 ± 0.40	N/A	N/A	N/A	Two-step deposition, improved crystallinity and morphology, reduced carrier recombination of charge carrier, increased carrier lifetime	[136]
diiodomethane CH₂I₂	Glass/FTO/TiO₂/MAPbI₃/Spiro-OMeTAD/Au	10.0	N/A	16.5	0.25 mL in 1 mL precursor	N/A	N/A	Iodine liberation, morphology enhancement	[138]
DiiodooctaneDIO	Glass/ITO/PEDOT:PSS/MAPbI₃/PCBM/Ag	10.61	N/A	17.74	1 vol% in 1 mL precursor	N/A	N/A	Intermediate formation and morphology enhancement	[137]

Table 10

Quantum dots-based additives for MAPbI₃.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
carbon quantum dot (CQD)	ITO/NiO_x/CH₃NH₃PbI₃/PCBM/Ag	15.25	Remained ~10% PCE from initial after 48 h	18.24	0.15 mg mL⁻¹	Remained~73.4% PCE from initial after 48 h	unencapsulated, dark, RT, RH = 80%,	Reduce non-radiative recombination loss, improve the crystallinity of film; thus, passivate grain boundaries and improve stability	[139]
carbon nanodots (CNDs)	ITO/NiO_x/CH₃NH₃PbI₃/PC₆₁BM/BCP/Ag	14.48% ± 0.39%	N/A	16.47% ± 0.26%	10 mg mL⁻¹	Remained ~18% as of an absolute value of PCE after 500 h	dark, 25 °C, RH = 40%air, unencapsulated,	Increase in the crystalsize, lower content of grain boundary defects, longer carrier lifetimes.	[142]
carbon quantum dots (CQDs)	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	17.59	(a) Retained 74% from initial PCE after 1500 h(b) Retained 17% from initial PCE after 216 h	18.81	0.05 mg mL⁻¹	(a) Retained 90% from initial PCE after 1500 h(b) Retained 70% from initial PCE after 216 h	(a) unencapsulated, inert.(b) unencapsulated, RH = 50–60%,	Passivate the grain boundaries and decrease the trap-state density. The bonding between CQDs and MAPbI₃ leads to a stable absorption of CQDs on the MAPbI₃ surface, forming a protective layer to prevent the perovskite from coming in contact with water, thereby enhancing thestability of PSCs	[141]
nitrogen doped CQDs (N-CQDs),	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/Al	8.34	N/A	13.936	3 vol%	N/A	N/A	N-CQDs act like an intermediate and help to form dense and smooth perovskite; passivate the trap states and decrease thenon-radiative charge recombination	[140]
Nitrogen-doped carbon dots (NCDs)	FTO/blTiO₂/_mL-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	12.12 ± 0.28%	N/A	15.93 ± 0.15%	0.05 mg mL⁻¹	N/A	N/A	Coordinatewith the iodide ions and lead cations on the surface ofperovskite, which effectively passivatesthe surface traps and help reduce non-radiativecharge carrier recombination; thenitrogen dopants with lone electron pairs in NCDsoptimize the interfacial energy level to enhancethe charge carrier extraction efficiency at photoactivelayer/TiO₂ interface	[144]
potassium cation (K+) functionalized carbon nanodots (CNDs@K)	ITO/PTAA:F4TCNQ/CH₃NH₃PbI₃/PCBM/BPhen/Ag	18.25	N/A	21.04		N/A	N/A	Defects passivation and crystallization control of the perovskite film; K⁺ in the grain boundary, and prevents excessive cations from occupyinginterstitial sites, thereby reducing microstrain of polycrystalline film, the synergistic effect of tailored crystal size, and suppressed grain boundary defects could reduce charge trap density, facilitate charge generation, and lengthen carrier lifetime	[143]
graphene quantum dots (GQDs)	FTO/c-TiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	16.83	Remained ~15.6% as of final PCE after 30 days	18.34	1.5 mg mL⁻¹	Remained ~17.4% as of final PCE after 30 days	encapsulation, RH = 36%, atm	Promote charge transfer from theperovskite layer to TiO₂ film. Faster electron extraction and a slower recombination ratepassivatehanging bonds at the perovskite GBs	[145]

Table 11

Alkali metal additives and their role in MAPbI₃ perovskite.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
hydroiodic acid(HI)	ITO/PTAA/CH₃NH₃PbI₃/PCBM/Ti/Au	16.1	N/A	18.21	0.004 vol%	N/A	N/A	Grain size improvement	[149]
hydrochloric acid(HCl)	Glass/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	9.96	N/A	14.49	volume ratio 8%,	N/A	N/A	Grain size improvementand morphology enhancement	[156]
hydrobromic acid(HBr)				13.53	volume ratio 6%	N/A	N/A
hydroiodic acid(HI)				15.21	volume ratio 8%	N/A	N/A
lithium iodide(LiI)	FTO/TiO₂/CH₃NH₃PbI₃/electrode	11.3	Remained ~1% PCE as of final value after 25 days	17.01	12mg/mL	Retained ~6% PCE as of final value after 70 days	unencapsulated, ambient, air, RH = 40%,	Larger grain size and higher crystallinity and reduced PbI₂ residue	[155]
sodium iodide (NaI)	FTO/compact TiO₂/mesoporous TiO₂/CH₃ NH₃PbI₃/SpiroMeOTAD/Au	14.01	N/A	15.14	0.02 mol L⁻¹	N/A	N/A	Improved crystallinity and grain boundary passivation	[150]
lithium chloride (LiCl)	Glass/ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/C₆₀/BCP/Al	11.40	Died in 50 days	9.98	0.25%, wt%	N/A	N/A	Improved crystallinity and homogenous nucleation, and crystallization	[151]
sodium chloride (NaCl)				12.77	1.0%, wt%	N/A	N/A
potassium chloride (KCl)				15.08	0.75%, wt%	Remained ~85% after 50 days	unencapsulated, inert,dark

Table 12

Transition metal additives and their role in MAPbI₃ perovskite.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
n-type goethite (FeOOH)	FTO/cTiO₂/mp-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.4	(a) Remained only 5.7% as of final PCE after 360 h.(b) Retained 61% from initial PCE after 60 days.(c) Retained only 42% from initial PCE after 480 h	19.7	0.1 mg mL⁻¹	(a) Retained 94% after 360 h, i.e., 17.9%.(b) Retained 97% from initial PCE after 60 days.(c) Retained 92% from initial PCE after 480 h	(a) inert, 85 °C, dark, non-encapsulated, (b) 10 ± 5% RH, (c) light 100 mW cm⁻², inert, RT, mpp tracking,	Improved quality of perovskite and inhibition of iodine and methylamine ion migration	[157]
silver iodide(AgI)	FTO/compact TiO₂/mesoporous TiO₂/CH₃NH₃PbI₃/SpiroMeOTAD/Au	14.01	N/A	14.18	0.02 mol L⁻¹	N/A	N/A	Improved crystallinity and grain boundary passivation	[150]
copper iodide (CuI)				15.25		N/A	N/A
copper bromide(CuBr)				15.61		N/A	N/A
nickel chloride (NiCl₂)	ITO/SnO₂/CH₃NH₃PbI₃/SpiroMeOTAD/Au	17.25	Retained ~70% PCE after 100 h	20.61	0.03 mM	Retained ~70% PCE after 100 h	en-capsulated, air, light 65 mW cm⁻², ∼25 °C, RH = 45%, without ultraviolet filter	High crystallinity, GB passivation	[158]
copper chloride (CuCl₂)	FTO/NiO_X/CH₃NH₃PbI₃/PCBM/BCP/Ag	9.73	N/A	15.22	2.5 mol%	N/A	N/A	Improves morphology	[159]
cadmium chloride (CdCl₂)	FTO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	11.7	N/A	13.2	1% molar ratio	N/A	N/A	Enhance grain size and crystallinity	[160]
zinc chloride (ZnCl₂)	FTO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	11.7	N/A	13.76	0.1% molar ratio	N/A	N/A	Enhance grain size and crystallinity	[160]
rhodium iodide (RhI₃)	ITO/SnO₂/CH₃NH₃PbI₃/Spiro OMeTAD/Ag	19.09	Retained 75% of efficiency after 500 h	20.71	1 mol%	Retained 92% of efficiency after 500 h	unencapsulated, dry air	Improved crystallinity and grain boundary passivation	[162]

Table 13

Other metal additive for MAPbI₃.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
lead iodide (PbI₂)	FTO/c-TiO₂/m-TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.95	N/A	18.42	10% excess PbI₂	N/A	N/A	Improves the crystallinity	[163]
lead iodide (PbI₂)	Glass/FTO/CH₃NH₃PbI₃/Spiro-OMeTAD/Electrode/Encapsulation(UV-epoxy)	16.2	Retained 80% PCE till 12 h	16.5	10 mg mL⁻¹	Retained 80% PCE till 10days	ambient air, 85 °C, 60% RH, light 1 sun	N/A	[171]
lead iodide (PbI₂)	Glass/ITO/SnO₂/CH₃NH₃PbI₃/PTAA/MoO₃/Al	~8.9%	Remained ~ 40% PCE after 1500 h	~15.6%	15% excess	Remained ~ 95% PCE after 1500 h	light 30 mW cm⁻²_, 40 °C, inert	Excess PbI₂ forms adduct with the cosolvent (NMP), improving PCE and stability.	[172]
lead iodide (PbI₂)	FTO/TiO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Ag	7.23 ± 0.10	N/A	14.32 ± 0.28%	concentration –N/A, by annealing @130 °C	N/A	N/A	Grain boundary passivation	[176]
lead sulfide(PbS QDs)	FTO/SnO₂/CH₃NH₃PbI₃/Spiro-OMeTAD/Au	15.2	N/A	15.7	12.5 mg mL⁻¹	N/A	N/A	Capping ligand for surface functionalization to improve crystallinity	[175]

Table 14

Non-metal additives and their role in MAPbI₃ active layer.

Additive in Active Layer	Architecture	PCE, %(Pristine)	Stability(Pristine)	PCE, % (with Additive)	Amount of Additive	Stability with Additive	Stability Conditions	Role of Additive	Ref
ammonium iodide (NH₄I)	Glass/ITO/PTAA/CH₃NH₃PbI₃/PCBM/Ag	15.2	Retained ~70% PCE after 20 days	17.4	5 wt%	Retained ~80% PCE after 20 days	RH = 50 ± 5%, unencapsulated, ambient, air	Improved morphology, increased crystalline size and grain size, lower trap density	[177]
ammonium chloride (NH₄Cl)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/Al	7.97	N/A	9.93	17.5 mg mL⁻¹	N/A	N/A	Improved morphology, increased crystalline size and grain size, lower trap density	[178]
ammonium fluoride (NH₄F)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PC₆₁BM/LiF/Al	13.74	Retained 70% PCE after 5 weeks	15.15	10 mol%	Retained 82% PCE after 5 weeks	encapsulated, air	Improved morphology, increased crystalline size and grain size, lower trap density	[179]
ammonium chloride (NH₄Cl)				16.88		Retained 87% PCE after 5 weeks
ammonium bromide (NH₄Br)				16.85		Retained 89% PCE after 5 weeks
ammonium iodide (NH₄I)				17.44		Retained 91% PCE after 5 weeks
ammonium hypophosphite NH₄H₂PO₂	ITO/PTAA:F4-TCNQ/CH₃NH₃PbI₃/PC₆₁BM/TrNBr/Ag	9.4 ± 1.0%	N/A	16.5 ± 0.7%	2.5 mg mL⁻¹	N/A	N/A	Intermediate with Pb and improved crystallinity grain size	[182]
hydrazinium iodide (N₂H₅I)	Glass/ITO/SnO₂/CH₃NH₃PbI₃/PTAA/MoO_x/Al	14.98	Retained ~60% PCE after 4400 h	17.03	0.5%, wt%	Retained ~80% PCE after 4400 h	inert, light 60-70 mW cm⁻², 50 °C.	Intermediate between PbI₂ and N₂H₅I, improved crystallinity, grain size	[183]
hydrazinium chloride (N₂H₅Cl)	ITO/PEDOT:PSS/CH₃NH₃PbI₃/PCBM/C₆₀/BCP/Ag	7.14	N/A	12.66	PbI₂/MAI/N₂H₅Cl molar ratio = 1:1:0.2	N/A	N/A	Intermediate between PbI₂ and N₂H₅Cl, improved crystallinity, grain size	[184]
hypophosphorous acid (HPA)	Glass/FTO/TiO₂/CH₃NH₃PbI₃/ETL/electrode	5.1	N/A	8	0.75 uL mg⁻¹ solution in 1 mL of MAI	N/A	N/A	Larger grains with a smoother surface, additive acts as a reducing agent for iodine	[185]

Word count: 16530

Show less

© 2021 by the authors. Licensee MDPI, Basel, Switzerland. This article is an open access article distributed under the terms and conditions of the Creative Commons Attribution (CC BY) license (https://creativecommons.org/licenses/by/4.0/). Notwithstanding the ProQuest Terms and Conditions, you may use this content in accordance with the terms of the License.

Abstract

Translate

Methylammonium lead triiodide (CH₃NH₃PbI₃/MAPbI₃) is the most intensively explored perovskite light-absorbing material for hybrid organic–inorganic perovskite photovoltaics due to its unique optoelectronic properties and advantages. This includes tunable bandgap, a higher absorption coefficient than conventional materials used in photovoltaics, ease of manufacturing due to solution processability, and low fabrication costs. In addition, the MAPbI₃ absorber layer provides one of the highest open-circuit voltages (V_oc), low V_oc loss/deficit, and low exciton binding energy, resulting in better charge transport with decent charge carrier mobilities and long diffusion lengths of charge carriers, making it a suitable candidate for photovoltaic applications. Unfortunately, MAPbI₃ suffers from poor photochemical stability, which is the main problem to commercialize MAPbI₃-based perovskite solar cells (PSCs). However, researchers frequently adopt additive engineering to overcome the issue of poor stability. Therefore, in this review, we have classified additives as organic and inorganic additives. Organic additives are subclassified based on functional groups associated with N/O/S donor atoms; whereas, inorganic additives are subcategorized as metals and non-metal halide salts. Further, we discussed their role and mechanism in terms of improving the performance and stability of MAPbI₃-based PSCs. In addition, we scrutinized the additive influence on the morphology and optoelectronic properties to gain a deeper understanding of the crosslinking mechanism into the MAPbI₃ framework. Our review aims to help the research community, by providing a glance of the advancement in additive engineering for the MAPbI₃ light-absorbing layer, so that new additives can be designed and experimented with to overcome stability challenges. This, in turn, might pave the way for wide scale commercial use.

Details

Title

The Progress of Additive Engineering for CH₃NH₃PbI₃ Photo-Active Layer in the Context of Perovskite Solar Cells

Author

Stevenson, Keith J

First page

814

Publication year

2021

Publication date

2021

Publisher

MDPI AG

e-ISSN

20734352

Source type

Scholarly Journal

Language of publication

English

DOI

https://doi.org/10.3390/cryst11070814

ProQuest document ID

2554485288

The Progress of Additive Engineering for CH₃NH₃PbI₃ Photo-Active Layer in the Context of Perovskite Solar Cells

Jump to:

Full Text

Abstract

Details

Suggested sources

The Progress of Additive Engineering for CH3NH3PbI3 Photo-Active Layer in the Context of Perovskite Solar Cells

Jump to:

Full Text

Abstract

Details

The Progress of Additive Engineering for CH₃NH₃PbI₃ Photo-Active Layer in the Context of Perovskite Solar Cells