Although shallow-level defects are considered benign types of defects due to their much lower charge recombination rate and their little influence on the photovoltaic performance of freshly prepared devices, they possess mobile charge species that can migrate under illumination, heat, and the built-in electric field, leading to unintentional doping effects by accumulating at interfaces
[64]. Light-induced ionic redistribution or the migration of defects such as interstitials, antisites, or vacancies can also cause local band bending and impede charge transportation
[65], leading to anomalous hysteresis in
J-V curve
[66][67], degradation of perovskites or metal electrodes
[68][69][70][71], and the phase segregation
[72][73][74][75].
2.4. Impact of Defect-Induced Non-Radiative Recombination on Device Parameters
The presence of trap states in perovskite thin films and at adjacent interfaces of PSCs, can severely affect their photovoltaic parameters, such as
VOC, short-circuit current (
JSC), and FF, thereby limiting PCE and stability. Under the bias-illumination, incident light excites electrons from the valence band into the conduction band, splitting the Fermi level (E
F) into quasi-Fermi levels of electrons (E
Fn) and holes (E
Fp). The steady-state charge density, which is determined by the balance between charge generation and recombination rates, controls the quasi-Fermi level splitting (QFLS = E
Fn − E
Fp)
[76]. In an ideal case with no recombination in the bulk, at the surface, grain boundaries, and interfaces, the E
F of its corresponding carrier would remain constant at the quasi-Fermi level without any drop, and there would be no energy loss. In that case, the output power of the device would be equal to the QFLS
[77].
However, when non-radiative recombination creates a pathway for the recombination of excess free charge carriers, it reduces the steady-state charge density and QFLS and, ultimately decreases the
VOC of PSCs. Hence, non-radiative recombination is the fundamental source of the open-circuit losses
[78]. The relationship between
VOC, radiative and non-radiative recombination losses can be described by the external photoluminescence quantum efficiency (
ηext)
[79][80]:
where
VOC,rad is the radiative limit of the open-circuit voltage when non-radiative recombination is fully suppressed. Therefore, the deficit in
VOC due to nonreductive recombination can be expressed as
[81][82]:
Thus, the voltage loss due to non-radiative recombination can be quantified by measuring the photoluminescence quantum yield (PLQY) or electroluminescence quantum efficiency (EQE
EL). Improvement in PLQY and EQE
EL in passivated PSCs leads to an increase in V
OC and a decrease in non-radioactive recombination losses, thereby improving PCE. It has been reported that a 1% improvement in PLQY of PSCs can result in a 0.12 V increase in
VOC.
2.5. Defect Induced Hysteresis Behavior and Intrinsic Instability
The hysteretic behavior in the
J-V characteristic of PSCs presents a challenge to accurately characterize their photovoltaic performance. Although the exact reasons for this behavior are still under debate, many studies suggest that charge defects and ions migration
[83][84] are responsible for the anomalous hysteresis observed in the
J-V characteristics of different scanning directions
[85][86]. Despite achieving impressive PCE values, most PSCs still suffer from hysteresis
[87] and instability
[88], which are associated with varying amounts of active charge defect states in the perovskite thin films and device interfaces
[83][84]. Ion migration induces intrinsic defects and affects the electric field distribution at interfaces. By using the time-resolved Kelvin probe force microscopy (tr-KPFM) technique, Stefan et al. demonstrated that the hysteresis in PSCs is caused by the localized positive ionic space charge at the ETL surface and negative ionic space charge across the perovskite layer. These charges form an opposite charge layer at the perovskite/ETL interface upon illuminating or applying external voltage. Thus, they attributed the hysteresis to the formation and release of ionic interface charge caused by the variation in illumination or electric field
[86]. Their results also confirm that the ion migration toward the interface region impedes the smooth charge extraction and transportation. However, the interplay between ion migration and interfacial defects still requires further exploration.
Several approaches have been proposed to suppress hysteresis in PSCs. One of the most effective methods is the use of additives for the interface, GBs, and ionic defects passivation. FA-based and mixed cationic perovskites have also been found to demonstrate less hysteresis than MA-based PSCs. Another promising technique is the fabrication of 2D/3D graded junctions, which has been shown to reduce hysteresis in mixed-dimensional PSCs. Additionally, an appropriately high scanning rate and improving the crystallinity of the perovskite layer have been found to suppress hysteresis in the PSCs. However, it should be noted that sometimes, scanning direction and rate do not influence the hysteresis.
3. Estimation of Defect-Induced Recombination Losses and Techniques for Calculating Defect Density
3.1. Calculating the Bandgap
Accurately estimating the bandgap of semiconductor materials is crucial for precise calculations of the
VOC deficit caused by trap-assisted recombination occurring in bulk or device interfaces. However, the presence of a substantial number of defects and variation in perovskite film thickness can make it challenging to estimate the bandgap accurately, leading to underestimation or overestimation of recombination losses in the form of
VOC deficit in PSCs. Various techniques, such as Kubelka–Munk processes, Tauc plots, and the onset of electroluminescence quantum efficiency (EQE) spectra are used to calculate the bandgap of perovskite thin-film material
[89]. The Kubelka–Munk technique calculates the bandgap by measuring the reflection of incident light, while the Tauc plots method utilizes the absorption of incident light in a wide spectral range to determine the bandgap. However, the accuracy in the calculated bandgap for thicker perovskite film is less reliable due to sub-band absorption, resulting in an underestimation of its value. The observed redshift of the onset of EQE spectra is also due to the absorption by electrically active sub-bands.
3.2. Photoluminescence Quantum Efficiency
High photoluminescence quantum efficiency values approaching unity indicate suppression in non-radiative recombination, which is desirable to achieve PCEs close to the theoretically calculated values for single-junction PSCs. If the PLQE value reaches unity, it can be inferred that all non-radiative recombination pathways have been eliminated, and charges are recombining through the emission of photons. When measuring PLQE, incident photons with excitation intensity equivalent to 1 Sun excite carriers to all accessible states, ignoring any imbalance in carrier transport. The relationship between output
VOC and the photoluminescence quantum yield (PLQY) is given as
[79][90]:
𝑉OC=𝑉OC,rad+KTqln(PLQE). At 1 Sun and excitation density of 10
15 cm
−3, an increase in PLQY from 1% to unity results in 0.12 V increase in
VOC. The obtained PLQY spectra depend on film quality, energy levels matching ETL or HTL with the perovskite layer, and the interfacial recombination channels, as well as other optical losses such as photon escape and parasitic absorption. As PSC is composed of a complex, layered structure, recombination losses in the intrinsic perovskite layer and at the interfaces can be quantified separately.
3.3. External Radiative Efficiency
Estimation of
VOC deficit induced by trap-assisted recombination is often performed using the external radiative efficiency (ERE) under a forward bias with an external voltage source. ERE is typically measured when the injected current under bias is equal to the illumination current. The value of ERE indicates the extent of losses due to non-radiative recombination. A high ERE value indicates low non-radiative recombination losses, suggesting that sufficiently large injected current emits the photons by radiative recombination of carriers
[91]. However, the ERE of a complete PSC is generally lower than the PLQY of a perovskite active layer measured alone or in a complete device due to the inequalities in the spatial distribution of the quasi-Fermi levels. The value of ERE can only be compared with the PLQY if the distribution of QFLS remains flat in both measurements.
3.4. Photoluminescence Imaging
The defect states responsible for non-radiative recombination in perovskite absorbers are distributed randomly throughout the bulk, surface, and interfaces. However, the regions near the surface of perovskite film are believed to have a high concentration of trap states. Hyperspectral absolute photoluminescence imaging is a commonly used technique to identify the origin and spatial distribution of defect states in complete PSCs and effectively quantify the trap-assisted recombination losses caused by the defect states at bulk, bottom, and top interfaces.
By using this technique, Stolterfoht et al.
[92] showed that the non-radiative recombination losses in the active area are sufficiently non-uniform, and their corresponding losses result in decreasing the QFLS. The interfacial recombination after the incorporation of each charge transport layer individually with perovskite layer (such as poly[bis(4-phenyl)(2,4,6-trimethylphenyl)amine] (PTAA) as HTL and fullerence (C
60) as ETL) results in an 80 meV drop in the QFLS at each interface. It is important to note that the loss in
VOC due to non-radiative recombination induced by each layer does not simply add up in complete perovskite device operation. Rather, the overall
VOC deficit is attributed to the increase in the trap-assisted recombination current, which has a logarithmic relation with
VOC.
3.5. Thermal Admittance Spectroscopy (TAS)
Understanding defects and the depths of their energy levels is essential for reducing non-radiative recombination losses in PSCs. TAS is used to obtain detailed information on the trap density of states (tDOS) in a complete PSC. Charged defects in the photoactive layer act as small, localized capacitors, and the trapping-detrapping of carriers in defects is related to the charge-discharge process in the capacitor. By tracing variations in junction capacitance with the frequency of applied alternating current (A.C.) voltage, the features of defects can be deduced. In its working process, first the charged defect states are thermally activated, then they release their charge within the A.C. period and capably foster the admittance signal. The discharging of defects depends on both the depth of the defect energy level and the temperature, which can be reflected by the junction capacitance at varying modulated A.C. frequency. The energy E
ω of the defect energy state at a frequency (ω) could be assessed as
[61][93]:
In the above equation, E
d and E
v represent the depth of defects energy level and the valance band maximum, respectively. The defect density (N
t) derived from angular frequency-dependent capacitance is given by Equation (7):
In Equation (7), ω stands for angular frequency, and C denotes the capacitance.
Vbi is a built-in potential and is derived from the capacitance-voltage (C-V) curve. W represents the depletion width, which is taken from Mott-Schottky analysis and expressed as
[61][94]:
In Equation (8), A and ε
r represent the contact area and relative dielectric constant. Measurements using TAS reveal a larger density of defect states (∼10
18 cm
−3) in a complete PSC compared to the density of defects in a sole perovskite film in isolated form. The defects induced tDOS having different energy depths usually be categorized into three bands: band 1 lies in an energy interval of 0.35–0.40 eV, band 2 lies between 0.40–0.50 eV, and band 3 lies above 0.50 eV. Some useful approaches for reducing the tDOS include coating a layer of phenyl-C61-butyric acid methyl ester (PC
61BM) on the surface of the perovskite active layer, which can effectively decrease the tDOS of band 2 and band 3 almost two orders of magnitude, and surface passivation, which can substantially reduce the deep-level defect states.
3.6. Steady-State PL Emission
In addition to electrical properties, defects can strongly affect the optical properties of perovskite semiconductors. Therefore, steady-state PL emission has been widely used to estimate the defect density in perovskite films for photovoltaic applications
[61][95]. Initially, the perovskite film is photoexcited with pump fluence. After photoexcitation, either the excited charges in perovskite film emits photon through the band-to-band transition, or they become trapped in defect states, resulting in negligible or no emission. If all the defect traps are filled with the photogenerated charges in perovskite thin film, this is indicated by a turning point at low pump fluence, also known as a trap filling turning point. The trap filling turning point at low pump fluence is called a threshold trap pump fluence (
𝑃𝑡𝑟𝑎𝑝𝑡ℎ) which can be determined by the intersection of the pump fluence axis and linearly extrapolated PL intensity. The total defect density
ntrap can be assessed by the following equation
[61][95][96]:
The term α in Equation (9) stands for the absorption coefficient, whereas E represents the energy of a single photon at the laser pulse wavelength. A higher accuracy in calculating the total defect density can be achieved by using an increased pump fluence for PL emission.
3.7. Space Charge Limited Current (SCLC)
The SCLC technique is another widely used characterization tool for quantifying defect density and carrier mobility and understanding defect-induced trap mechanisms inside the PSCs
[97][98][99][100]. In this technique, an adequately large electric field is applied to an electron- or hole-only device via Ohmic contacts and a portion of the ejected electrons/holes is trapped by the defects in perovskite, reducing the density of free charges and limiting the current by the space-charge effect. The dark
J-V curves obtained from this technique exhibit three regions: the Ohmic or the linear region, trap-filling limit (TFL) region, and the SCLC region, which is trap-free. The linear region represents the Ohmic response, where current density and electric field intensity have a linear relation (
I ∝
V). The trap-filling region shows a rapid increase in the current with increasing the electric field (
I ∝
Vn, n > 3), where defect states are continuously filled until all the defects are filled as bias increases. Subsequently, the SCLC trap-free region (
I ∝
V2) occurs. The trap density (n
t) can be calculated using the following equation:
where, ε represents the dielectric constants for the photoactive layer, ε
0 represents the vacuum permittivity, L represents the thickness of the perovskite active layer, and q represents the elementary charge.
VTFL is the bias voltage required to occur the TFL region, which can be obtained from the dark
J-V by fitting. The dielectric constant of the photoactive layer (perovskite) can be calculated from Equation (11):
where, C
g denotes the geometrical capacitance of the active layer, ε
0 = 8.85 × 10
−14 F·cm
−1 is permittivity of free space, and A represents the active area of the device
[101]. Note that this technique only calculates the single type of defects for electron traps or hole traps at a time.
3.8. Deep-Level Transient Spectroscopy (DLTS)
DLTS is a technique that is used to detect deep-level traps that are difficult to detect by other characterization techniques
[61][102][103][104]. It is significant because of its sensitivity, ease of operation, and its ability to set a window for emission rates
[103]. The DLTS utilizes the variation in defect emission rates with temperature to define the energy difference between one of the band edges and the defect states in the forbidden gap and to estimate the capture cross-section of the defects
[102]. The capacitance transients are explored using the DLTS technique by evaluating the variations in capacitance with variation in temperature (from the temperature of liquid nitrogen to the room temperature or above). The defect states are filled up by the charges generated under an initial low-temperature bias pulse. In this case, the emitting rate of a trap state is much lower than its capturing rate and the former can be neglected
[61].
4. Novel Defect Management Strategies to Mitigate Defect-Induced Losses and Instability Issues
4.1. Bulk or the Deep Level Defects Passivation Techniques
4.1.1. Compositional Engineering
Compositional engineering is one of the most successful techniques for regulating the optoelectronic properties of perovskite thin films, including light absorption, carrier mobility, defect density, and carrier concentration. This method allows for the modification of the perovskite film morphology and crystallinity through cationic or ionic doping
[105][106].
Hence, the optoelectronic properties of perovskite are directly or indirectly influenced by A- and B-site cations and X-site anions
[106]. Engineering at the cationic or anionic sites through mixed anions and cations or suitable substitution in standard perovskite structure can suppress non-radiative recombination and improve PCE and stability.
X-site engineering: Early PSCs made with MAPbI
3 exhibited low PCE due to poor crystallinity and morphology of the perovskite film. However, Jeon et al. were able to achieve a PCE of 16.2% by substituting Br for I in the perovskite composition and using the anti-solvent dipping technique to suppress defects during crystal growth
[107]. Noh et al. also achieved a PCE of 12.3% by using a mixed halide MAPb(I
1−xBr
x)
3 composition to tune the bandgap and improve the device stability
[108]. The mixed composition MAPb(I
1−xBr
x)
3 can tune the bandgap in the range from 1.53 eV to 2.97 eV and provides high-efficiency colored PSCs
[108][109].
Both A and X sites engineering: The large bandgap of MAPbI
3 (∼1.55 eV), which is greater than the Shockley–Queisser optimum of ∼1.4 eV for single-junction solar cells, means that it cannot absorb the full solar spectrum. Doping with the larger formamidinium (FA) cation can reduce the bandgap to around 1.48 eV, improving optical and electrical properties and leading to higher
JSC and PCE of PSCs. Additionally, reports suggest that the MA cation rotation can passivate deep-level defects such as iodide and lead vacancies, making A-site cation more influential in the traps, charge transport, and light absorption of perovskite devices. FA is more thermally stable than MA cation, making it a suitable doping candidate for device stability.
Stabilizing the photoactive α-phase of FAPbI3: Compared to MAPbI
3-based PSCs, FAPbI
3-based PSCs have a reduced bandgap of 1.48 eV due to the slightly larger size of FA cation, which enhances light absorption and potentially leads to higher
JSC and PCE closer to the SQ limit. However, their stability is comparatively lower than that of MAPbI
3-based perovskite due to their tolerance factor, which falls close to the upper boundary of the Goldschmidt chart. Moreover, the structural instability of FAPbI
3 at room temperature remains a challenge as it can crystallize to an undesired, photo-inactive hexagonal δ-phase with a wide bandgap
[110]. The room-temperature stable hexagonal phase has a high tolerance factor and activation energy, which can be reduced by using mixed cations, anions, or additives to promote the formation of the desired stable black perovskite phase. However, even the trigonal photoactive α-phase or a black perovskite phase is also sensitive to humidity and high α-phase transition temperature, which makes this composition more challenging.
4.1.2. Bulk Passivation with Alkali Metal Cations
Defects such as iodine interstitials (I
i) in the perovskite absorber are generated during the growth process, resulting in an accelerated non-radiative recombination of photo-generated electron-hole pairs and decreased PCE of the perovskite devices. These iodine interstitials can readily migrate due to their low activation energy (0.29 eV)
[111], causing undesirable current-voltage hysteresis and device instability
[111][112]. Both the theoretical and experimental results confirm that the introduction of alkali metal halides (potassium iodide (KI), cesium iodide (CsI), lithium iodide (LiI), cesium chloride (CsCl), sodium fluoride (NaF, etc.) into the perovskites solution effectively suppresses bulk defects as well as defects along surface and GBs, inhibiting ions migration and anomalous hysteresis, and thereby improving carrier lifetime and the overall device performance.
Abdi-Jalebi et al. demonstrated that the addition of an optimized amount of potassium iodide (KI) solution in triple cations perovskite (Cs
0.06FA
0.79MA
0.15)Pb(I
0.85Br
0.15)
3 solution successfully suppresses the non-radiative recombination by passivating halide vacancies and eliminates hysteresis by suppressing photoinduced ion migration in perovskite films
[72]. The improvement in luminescence yields was attributed to the decrease in bandgap and surface and GBs defects passivation by the formed layer of KI at the surface of perovskite absorber layer. The origin of hysteresis in PSCs, as confirmed by several theoretical studies, is not the migration of iodine vacancies but the formation of Iodine Frenkel (I Frenkel) defects
[41].
4.1.3. Bulk Passivation with Divalent Metal Cations
Divalent metal cations such as calcium cation (Ca
2+), strontium cation (Sr
2+), europium cation (Eu
2+) etc. are frequently used to stabilize the perovskite α-phase and improving device performance, particularly in the inorganic CsPbI
2Br PSCs
[113][114][115]. Han et al.
[113] reported the calcium chloride (CaCl
2) in CsPbI
2Br for n-type doping in perovskite lattice. The Ca
2+ ions passivated the GBs defects by combining with Cl
− ions instead of incorporating in the lattice, increasing the Fermi level splitting, and delivering a very high
VOC of 1.32 V. The defect density decreased from 9.10 × 10
15 cm
−3 to 3.03 × 10
15 cm
−3 in passivated devices. Wang et al. reported the addition of europium ion pair of Eu
3+-Eu
2+ acting as a “redox shuttle” to oxidize deep-level Pb cluster (Pb
0) defect and reduce I
0 defect in a cyclical redox transition process in PSCs
[115]. The redox shuttle transfers electrons to I
0 defects from Pb
0, where Pb
0 is oxidized to Pb
2+ by the Eu
3+ cation and the formed Eu
2+ concurrently reduces I
0 to I
−. The passivated devices demonstrated a high PCE of 21.52% and improved long-term stability by retaining 90% of the initial efficiency after 8000 h. Similarly, the Sr
2+ has been reported for partial substitution of toxic lead with less toxic doped strontium metal and its strong defects passivation in inorganic PSCs. The doped Sr enriched the CsPbI
2Br surface and increased the FF and
VOC by passivating the defects
[114].
4.1.4. Bulk Passivation with Transition Metal Halides
Transition element halides such as NiCl
2, NbF
5, manganese ion (Mn
2+), and cadmium iodide (CdI
2), have been employed to suppress the formation of deep-level defects Pb
0 and undercoordinated I
− ions and I-rich antisites), thereby improving the performance and structural/phase stability of PSCs
[116][117][118]. These transition metals, having filling d-orbits, can form strong bonds with various ligands to create stable coordination and effectively suppress migration.
4.1.5. Bulk Passivation with Halide Anions
The halogen ions such as Cl
−, F
−, I
− are commonly used as additives in perovskite solutions to control the perovskite crystal growth process, suppress defects, and improve the morphology of the perovskite absorber layer
[119]. These ions can be introduced by adding compounds such as ammonium chloride (NH
4Cl), lead chloride (PbCl
2), CsCl, CsI, MACl, lithium fluoride (LiF), formamidine chloride (FACl), NbF
5, trimethylammonium chloride (TACl), and N,1-diiodoformamidine (DIFA). Among them, Cl
− is the most extensively studied ion, as it can improve the morphology of perovskite film by slowing down crystallization and enlarging grain size. Even though Cl
− can quickly escape during thermal annealing, the residue can improve device performance by passivating defects at the GBs
[120][121].
4.2. Grain Boundaries Passivation
4.2.1. GBs Passivation with Alkyl Salts
The performance of p-i-n structure perovskite is generally inferior to regular n-i-p PSCs. However, Zheng et al.
[122] reported the high-efficiency inverted PSCs by using trace amount (<0.3 mol.%) of long-chain alkylamine ligands (AALs) including phenethylamine (PEA), n-butylamine (BA), oleylamine (OA), and octylamine (OAm) directly in the mixed cation perovskite precursors in one-step coating method. The long alkyl chain increases moisture stability while the amine group passivates the A-side vacancy defects. Octylamine was found to have a stronger passivation effect than other alkylamine ligands, with a large improvement in carrier lifetime from 114 ns in pristine to 1049 ns in OAm passivated perovskite films. Furthermore, the passivated devices demonstrated a lower trap density of 4.4 × 10
22 m
−3 eV
−1 at shallower energy (0.32 eV) than 1 × 10
23 m
−3 eV
−1 at 0.35 eV in pristine film at room temperature (300 K). The improved film quality and optoelectronic properties resulting from optimized passivation of OAm led to a significant improvement in
VOC from 1.06 V to 1.17 V and PCE from 20.5% to 23.0%.
4.2.2. GBs Passivation with Zwitterions
Zwitterions are widely reported passivation agents which can coordinate with both positively charged undercoordinated Pb
2+ cationic defects and negatively charged Pb-I antisite defects, because they have both electron donor and acceptor groups. Thus, they are also known as bifunctional molecules
[123]. In 2017, Zheng et al. developed and reported three zwitterion molecules (
L-α-phosphatidylcholine, choline chloride, and choline iodide) for passivating cationic and anionic defects in FA
0.85MA
0.15Pb(I
0.85Br
0.15)
3-based PSCs
[124]. All three passivators showed a remarkable improvement in
VOC and increased carrier lifetimes, with choline chloride delivering the best results, demonstrating a big improvement in
VOC from 1.03 V to 1.14 V with only 0.39 V deficit and PCE from 19.2% to 21.0%. The devices stored in ambient conditions showed no change in PCE after 800 h.
4.2.3. GBs Passivation by Lewis Base Molecules
A diverse range of Lew7is base molecules, including molecules, polymers, and π-conjugated materials containing electron donor sulfur (S), nitrogen (N), and oxygen (O) atoms, are employed for passivating defects in PSCs
[125][126][127][128]. These molecules can effectively suppress the undercoordinated Pb
2+ or Pb cluster defects at GBs or the surface of perovskite thin films by forming Lewis adducts with defective trap-states when an optimized small quantity is added in the precursor solution.
Sanith et al.
[129] initiated defects passivation with Lewis bases using pyridine and thiophene as organic Lewis bases in their study. They demonstrated that the undercoordinated Pb
2+ defects are passivated by the lone pair of electrons on the S atom of thiophene and the N atom of pyridine by forming coordination bonds.
Small molecules containing conjugated carboxyl (C = O) groups have also been proven to improve stability and passivate GBs defects in PSCs with their O donor carboxyl groups. For example, Wang et al.
[130] introduced 1,3,7-trimethylxanthine, also known as caffeine, in MAPbI
3 precursor solution to improve PCE and thermal stability of the devices. The additive has two conjugated carboxyls (C = O) groups that passivate positively charged defects by strongly interacting with Pb
2+ and suppress ionic migration.
4.2.4. GBs Passivation with Lewis Acids
Lewis acids are also often used as additives in precursor solution or incorporated in antisolvent for in-situ passivation during the deposition and crystallization of perovskite films. By adding a small amount of electron acceptor Lewis acids, electron-rich defects such as Pb-I antisite or the undercoordinated iodide (I
−) ions with extraneous electron pairs can be passivated. For example, fullerene (C
60) and its derivatives (indene-C
60 bis-adduct (ICBA), [6,6]-phenyl-C
61-butyric acid methyl ester (PCBM) etc.) have shown good passivation effects due to the strong electron-accepting ability of their fullerene spherical structure. In a study by Wu et al.
[131] the addition of PCBM in PbI
2 precursor solution was shown to form pinhole-free perovskite thin films by a two-step deposition method. The added PCBM passivated the negatively charged vacancy defects at GBs. Although PCBM does not exist in the lattice. It was distributed along the GBs due to its too large size, as confirmed by electron energy loss spectroscopy (EELS) mapping. The improved quality and optoelectronic properties of perovskite films led to a high FF of 0.82 and a high PCE of 16%.
4.2.5. GBs Passivation with Polymers
The long-chain polymers composed of different donor functional groups are commonly used in PSCs to improve their stability and performance by passivating defects predominantly at the GBs
[43][126][132]. Due to their large molecular size, they can distribute along the GBs rather than being incorporated in the perovskite lattice and prevent the moisture penetration through GBs.
4.2.6. GBs Passivation by Multifunctional Agents
The use of multifunctional passivation molecules in PSCs has become increasingly popular due to their ability to improve both device stability and performance by simultaneously passivating multiple trap-assisted recombination pathways
[133]. For example, Cai et al.
[134] reported 2,2-difluoropropanediamide (DFPDA), a multifunctional molecule, into the FA
0.85MA
0.15PbI
3 precursor solution. DFPDA contains fluorine, carbonyl, and amino groups, which can passivate undercoordinated Pb
2+ defects by making a chemical bond with carbonyl group, suppress ion migration by immobilizing the iodide by amino group, and increase the moisture stability by making a barrier on the perovskite film with fluorine group.
4.2.7. GBs Passivation with Ionic liquids (ILs)
Many research groups have highlighted the multifunctional role of ionic liquids (ILs) in the development of PSCs. The structure of ILs contains large cationic functional groups and organic or inorganic anions, and the strong electrostatic force between ions enables them to minimize both negative (halide vacancies) and positive defects (Pb
2+), thereby improving device performance, structural, thermal, and humidity stability of the perovskite devices.
4.2.8. GBs Passivation with Quantum Dots (QDs)
Numerous reports have confirmed that effectiveness of using quantum dots (QDs) as agents for passivating surface and GBs defects passivation agents in PSCs, thereby improving and stabilizing their performance
[135][136]. Carbon QDs, possessing amino, hydroxyl and the carbonyl functional groups, can passivate electronic defects at the GBs, suppressing non-radiative recombination
[137][138]. For instance, Huang et al. reported the passivation of undercoordinated Pb
2+ trap states at GBs by adding carbon QDs with carbonyl and hydroxyl passivation groups. The passivated perovskite films displayed extended carrier lifetime, and higher PL intensity than control perovskite thin films and the corresponding passivated devices demonstrated a higher PCE of 18.24% than that of control MAPbI
3 devices (15.67%).
4.2.9. GBs Passivation with Oxides
Oxides of metals and nonmetals are found to be effective in stabilizing the performance of PSCs by passivating defects. The oxides of Group IV B and II A elements, such as silicon dioxide (SiO
2), aluminium oxide (Al
2O
3), sodium oxide (Na
2O), lithium oxide (Li
2O), and boron oxide (B
2O
3), are especially useful due to their high thermal stability. These oxides have been reported to suppress GBs and interfacial defects, thereby improving the stability and performance of the device.
4.3. Surface Defects Passivation by Post-Treatments
4.3.1. Post-Treatment with Lewis Acids
Lewis acids can effectively passivate not only GB defects by their addition in precursor solution or in antisolvents but also electron-rich defects (undercoordinated I
−) on the surface through post-treatment of crystallized perovskite films. Negative defects act as Lewis bases and donate their electrons to surface passivating Lewis acid, thus forming a Lewis adduct to passivate the surface defects and improve the overall performance of the perovskite device. For instance, Huang et al.
[93] coated a very thin layer of PCBM on the top surface of perovskite and confirmed through thermal admittance spectroscopy results that the fullerene derivative had passivated the defects on the surface and at the GBs. The surface treatment eliminated the photocurrent hysteresis and doubled the PCE by suppressing trap density up to two orders of magnitude.
4.3.2. Post-Treatment with Lewis Base Molecules and Functional Groups
Lewis base small molecules with N, S or O donors, long-chain polymers with
𝜋
-conjugated functional groups such as carbonyl (–C
=
O) and cyanide, having delocalized electrons, and molecules with benzene rings and amino donor groups are commonly used to passivate undercoordinated Pb
2+ or Pb cluster produced by halogen vacancies
[128]. Post-treatments of perovskite active layers with such long-chain polymers improve both efficiency and the moisture stability of the device
[139].
In perovskite solar cells, surface defects passivation with Lewis bases was first initiated by Noel et al.
[129]. They employed thiophene with S donors and pyridine with N donors for surface treatment, which passivated the under-coordinate Pb
2+ defects by lone pair of electrons on the S atom of thiophene and the N atom of pyridine by forming coordination bonds. Between these two additives, the pyridine demonstrated a better passivation effect than thiophene due to the higher electronegativity of the N atom than the S atom of thiophene. Therefore, the strong electron-donating ability enables pyridine to coordinate more strongly with Pb
2+.
4.3.3. Post-Treatment with Hydrophobic Molecules
The long-term stability of the perovskite device is greatly affected by the intrusion of water and oxygen in the atmosphere. Hydrophobic materials are generally non-polar and do not absorb water. They can passivate charge trapping centers on the surface while enhancing the hydrophobicity of the perovskite layer with their specific passivation groups (i.e., carbonyl, fluorine). Therefore, surface treatment with the hydrophobic materials has become a promising approach to simultaneously improve the stability and the PCE of PSCs
[140][141][142].
4.3.4. Post-Treatment with Hydrophilic Molecules
In contrast to the use of hydrophobic passivation agents, Park et al.
[143] reported a novel bifunctional approach of spin-coating hydrophilic materials, 2-aminoethanol hydroiodide (2AEI), and 4-amino-1-butanol hydroiodide (4ABI), onto the surface of the absorber layer to simultaneously enhance stability and device performance. These hydrophilic materials form strong chemical bonds with trap states such as iodide centers and undercoordinated Pb
2+ ions, suppressing the bulk and surface defects. In addition, they improve the crystallinity of the absorber layer. The excellent passivation effects of 4ABI and 2AEI are reflected by the substantial enhancement in PL, extended carrier lifetime, and reduction in defect density. The estimated defect density reduction from 1.2 × 10
16 cm
−3 (control) to 1.0× 10
16 cm
−3 (4ABI and 2AEI) and significant improvement in carrier lifetime (from 245 to 611 ns with 4ABI) demonstrate the suppression in non-radiative recombination of charge carriers.
4.3.5. Post-Treatment with Alkyl Chain Organic Cations
Another approach to manage both anionic and cationic defects on perovskite surfaces and GBs is to use alkyl chain organic cations such as alkylammonium halides as a capping layer on the top of perovskite surface through a post-treatment method. This method passivates ionic defects at the surface and GBs through electrostatic binding and can potentially form a 2D layered perovskite on the top surface of the absorber layer to suppress interfacial recombination and improve stability against moisture. However, the formation of 2D layered perovskite may affect the charge transfer process and lower the performance
[144][145]. Organic cations with long alkyl chains such as NH
3I(CH
2)
8NH
3I (C
8), octylammonium (OA
+), and tertbutylammonium (tBA), are unable to be doped into the perovskite lattice due to their large size and high formation energy, but they can form layered perovskites to suppress defects on the surface and GBs of absorber layer
[146][147].
4.3.6. Post-Treatment with Wide Band Gap Materials as Capping Layer
The use of wide band gap materials as post-treatment capping layers is another approach for surface passivation of perovskite. Typically, anions such as phosphate, sulfate, sulfur, or inorganic oxides can interact with surface dangling bonds or positive lead ions, contributing to the suppressing of non-radiative recombination and improvement in stability.
4.4. Interfacial Defect Passivation
4.4.1. Dimensionality Engineering
The mixed-dimensional perovskites have become an effective approach to improve device performance and stability for their commercialization
[148]. The use of 2D/3D bilayer structure in PSCs is proposed as an efficient approach to eliminate recombination centers at interfaces, surface or GBs, and suppress electron density at HTL and perovskite layer due to electron repelling nature of wide bandgap 2D materials, thereby leading to improving the device stability and PCE
[48][149]. To form a 2D/3D heterojunction, a very thin layer of aliphatic or aromatic alkyl ammonium cations is coated on the top surface of the 3D bulk perovskite layer
[32], or alkylammonium salt is introduced into 3D perovskite precursor solution by in situ formations.
In 2016, Docampo et al.
[150] developed a solution process using MAI and phenylethylammonium iodide (PEAI) in isopropyl alcohol (IPA) to fabricate layered 2D perovskite on the top surface of 3D MAPbI
3 perovskite. The top thin layer of 2D perovskite (PEA)
2(MA)
4Pb
5I
16 serves as a moisture barrier and enables the selective charge extraction owing to the well-aligned energy band, leading to suppression of non-radiative recombination at the interface. The underlying active MAPbI
3 layer guarantees full white light absorption and carrier generation. Due to the significant passivation effects of 2D layered perovskite, a realistic improvement in PCE from 13.61% in pure MAPbI
3 to 16.8% in the mixed (2D/3D) perovskites was achieved. As
VOC and FF values of a device are closely related to trap-assisted recombination, the improvement in
VOC (from 0.99 to 1.11 V) and FF (from 0.70 to 0.73) indicates the suppression of recombination losses in PSCs with this two-layer configuration.
4.4.2. Interfacial Defects Passivation by Interlayer Engineering
PSCs consist of an absorber layer sandwiched between two charge transporting layers, which transport the photogenerated carriers
[151]. The charge extraction and transport ability of these layers are equally important to the charge generation process in the active layer. Therefore, interfaces play a critically important role in the device, especially energy alignment between the absorber and charge transporting layer, which largely influences the device performance and stability. The defect density at all the interface of PSCs is reported to be one to two orders of magnitude higher than that in bulk of the photoactive layer
[152].
The energy level mismatch between E
Fn in the perovskite layer and CB/lowest unoccupied molecular orbital (LUMO) of ETL, or between the E
Fp in the absorber layer and VB/HOMO of HTL, results in band bending at the interfaces
[81]. This band bending reduces the QFLS of the compact device, leading to a decrease in output voltage under illumination. It has been reported that almost all charge transporting layer decrease
VOC due to non-radiative interfacial recombination currents induced by them, except for high-efficiency devices that have well aligned energy bands with absorber layer.
Interfacial layer between HTL and perovskite. To realize the full potential of perovskites as photovoltaic material in PSCs, the suppression of carrier recombination at the perovskite/HTL interface is critical. This is because the built-in electric field at HTL/perovskite interface becomes weak due to the intrinsic self-doping characteristic of perovskites, which hinders the adequate transportation of carriers from the absorber to HTL
[153]. Currently, the most efficient HTL is spiro-OMeTAD, which is often heavily doped to enhance its conductivity, resulting in increased recombination losses at the HTL/perovskite interface. Decreasing the doping concentration in the spiro-OMeTAD has been reported to suppress interfacial recombination, increase
VOC and improve the device performance
[154][155].
Interlayers between ETL and perovskite. The electron transporting layer (ETL) plays a critical role in perovskite devices, as it is essential for effective charge extraction and transportation. A well-aligned energy level between the ETL and perovskite layer and defect-free interface crucial for achieving high
VOC [156]. This goal can be accomplished by introducing a thin interlayer of suitable material between the two layers. While titanium dioxide (TiO
2) is the most efficient and commonly used ETL material, it is susceptible to light-induced instability, particularly under ultraviolet (UV) radiation. Light exposure generates electron-hole pairs in TiO
2. The holes in the valence band recombine with available electrons on oxygen adsorption sites, leaving the positive oxygen vacancies or the Ti
3+ sites on the surface of TiO
2 and the free electrons in the conduction band
[157]. Therefore, introducing an ultra-thin layer between ETL (TiO
2) and perovskite is an efficient approach to mitigate these issues and suppress carrier traps and interfacial recombination, thereby improving stability and the performance of the devices.
5. Defects Passivation Techniques for Large Area Perovskite Solar Cells and Modules
5.1. Influence of Additives in Large-Area MAPbI3 PSCs and Modules
Li et al.
[158] added a small amount of monoammonium zinc porphyrin (ZnP) additive into the perovskite precursor solution for fabricating large-area perovskite films. The ZnP compound can efficiently anchor on the surface and GBs of perovskite film, suppressing the surface and GBs defects. It also prevents the escape of volatile organic cations during thermal annealing and acts as a barrier to moisture invasion. The passivated devices exhibited excellent thermal and moisture stability. Furthermore, the addition of ZnP to the precursor solution reduced the contact angle on the substrate and facilitated full surface coverage in blade coating, resulting in pinhole-free and uniform grain size. Finally, with the remarkable passivating effect of ZnP, large-area (16 cm
2) PSCs with improved thermal and moisture stability were successfully fabricated.
5.2. Influence of Additives in Roll-to-Roll Fabrication of PSCs
The optoelectronic properties of photoactive perovskite material can be altered by the mixed cationic and anionic composition, while additives can passivate defects and control the film growth process, thereby leading to improved PCE and thermal and moisture stability of large-area devices. In 2019, Kim et al. demonstrated the use of two additives, PbCl
2 (2.5 mg/mL) and MACl (2.5 mg/mL) in MA
0.6FA
0.38Cs
0.02PbI
2.975Br
0.025 precursor solution, along with a slightly modified PEDOT:PSS, to stabilize photovoltaic performance and improve the stability of the first fully roll-to-roll (R2R) fabricated PSCs
[159]. The two additives and the polymer modification in the HTL layer improved all the performance parameters and prolonged stability. The MACl additive improved the quality of film, increased carrier life time and increased the current density of the devices
[160]. Similarly, the improvement in
VOC and the FF was attributed to the passivation effects of PbCl
2. Furthermore, the polymer modification in HTL enables the deposition of perovskite in high humidity environment (approx. 55% RH). Finally, fully R2R slot die coated PSC with a remarkable efficiency of 11.7% was reported, except for top contact
[159].
6. Conclusions
Due to the high formation energy of deep-level trap states and low-temperature fabrication of perovskite thin films, substantially reduced nonradioactive recombination sites exist in bulk. However, shallow trap states with low defect densities are easily produced at the surface and GBs of the perovskite layer due to its low-temperature solution fabrication. The existence of shallow trap states at the surface mainly causes non-radiative recombination of photogenerated carriers and results in VOC deficit and reduction in FF of the PSCs. Although the efficiency of single-junction perovskite is approaching theoretically calculated value, state-of-the-art PSCs still exhibit a VOC deficit of 0.32–0.35 V, which suggests the presence of non-radiative recombination channels at the surface, GBs, and interfaces. Photoinduced ion migration and accumulation at interfaces mostly account for the anomalous hysteresis in PSCs. Mixed composition Cs0.05(MA0.17FA0.83)0.95Pb(I0.83Br0.17)3 PSCs exhibit negligible hysteresis compared to MAPbI3 in mesoporous PSCs, making compositional engineering a feasible strategy to suppress bulk defects and improve stability and optoelectronic properties to obtain hysteresis-free devices. Similarly, a mixed perovskite 2D/3D heterojunction is a successful approach for improving stability due to high stability and defect passivation of 2D perovskite at the surface, GBs, and interface. The most stable PSCs, with a stability of over 1 year and an efficiency >
24% has been obtained through this method. However, accurate control of 2D/3D heterojunction formation and understanding the mechanisms involved remain a challenge. Therefore, it is a pressing need to explore the new 2D materials to fine-tune the 2D/3D graded junction. To achieve this, a machine learning tool can be applied, which may provide a complete analysis from materials selection to the device performance.
Interfacial layers have proven to be effective in improving the performance and stability of PSCs by reducing the band bending, ion migration, and accumulation at interfaces. The mismatch between energy levels at the interface causes band bending, leading to a reduced output voltage of PSC under illumination. Interfacial buffer layers minimize this effect, improving the charge extraction and transportation process and resulting in device efficiency up to 23.7% with improved stability. To further enhance the stability and efficiency, exploring new hydrophobic materials with proper energy level alignment and high conductivity is promising.
Chemical additives are commonly used to control perovskite crystal growth, improve thin film morphology and passivate defects, thereby eliminating hysteresis and improving stability and device performance. A variety of passivating additives are available to suppress trap-assisted non-radiative recombination in PSCs, including the alkali metal halides in perovskite solution, which effectively reduce hysteresis and passivate the point defects at the surface and GBs.
Machine learning could be a beneficial tool for designing new passivation agents along with intensive high-throughput experimental investigation. In addition to addressing trap-assisted recombination losses and stability, the scalable fabrication of devices and modules is the third significant challenge. As the coating area increases, the PCE of corresponding devices displays a significant downward shift. Large-area coating processes to produce high-quality crystals pose a challenging task. Chemical additives and physical techniques are usually applied to the large-area fabrication of perovskite films. The additives passivate the trap-assisted recombination of photogenerated charge carriers and facilitate controlling the grain growth process, which leads to improving the quality of perovskite thin films and the performance of the devices.
To further improve the efficiency, stability, and scalability of PSCs, it is crucial to gain a more in-depth comprehension of the origin and nature of non-radiative recombination losses and to judiciously select passivating molecules with the aid of machine learning tools and experimental investigation. Moreover, the combined effect of using the 2D/3D graded heterojunction materials, compositional engineering, and additives to control the crystal growth process may prove more beneficial for improving the stability and PCE of large-area devices.