Phenothiazine-Based Hole Transport Materials for Perovskite Solar Cells.

The promising photovoltaic solar cells based on the perovskite light-harvesting materials have attracted researchers with their outstanding power conversion efficiencies (over 23% certified). The perovskite work has geared up in just under a decade and is competing with well-established semiconductor technologies such as silicon (Si), copper indium gallium selenide (CIGS), and cadmium telluride (CdTe). To commercialize the perovskite solar cells, their stability is the major concern. To address the stability issue, several factors need to be taken into account, and one of them is developing stable hole transport materials (HTMs), which are the essential building blocks. In this mini-review, we will discuss the important features of the HTMs, such as design and development of phenothiazine-based HTMs. Since phenothiazine is a low cost and stable molecule compared to the spiro-OMeTAD, it can be modified further via molecular engineering.

Introduction

Due to the growth of the population and the increasing desire for a comfortable life, the demand for energy is very high. The present source of energy is based on fossil fuels. Considering the scarcity of fossil fuels, researchers are working toward renewable energy sources which are clean and green. In this regard, the contingent option for sustainable development of human society is the conversion of sunlight into electricity. The photovoltaic cell is efficient and a good candidate as a renewable energy source.[1,2] Among the various photovoltaic technologies, dye-sensitized solar cells (DSSCs) have gained more attention from researchers by considering several properties like cost-effectiveness, easy fabrication, eco-friendliness, better stability, flexibility, and high power conversion efficiencies (PCEs). A breakthrough was made by O’Regan and Grätzel in 1991 with the PCE of 7%. Soon after, it reached 13% PCE with a zinc porphyrin photosensitizer and cobalt-based electrolyte system. The DSSC device is facing a stability problem because of the liquid electrolyte system, which does not allow for the commercialization and leads the research toward developing solid-state DSSCs (ssDSSCs).[3] The first ssDSSCs with the heterojunction between the CuSCN and TiO2 were reported by the Tennakone group.[4] However, all efforts yielded lower PCE; therefore, it is essential to work toward the alternate materials and devices. The PCE of 2.56% was achieved by Bach and Grätzel in 1988 with the spiro-OMeTAD (2,2′-7,7′-tetrakis(N,N-di-p-methoxy-phenyl-amine) 9,9′-spirobifluorene) as a hole conductor and Ru(II)L2(SCN)2 (where L is 4,4′-dicarboxy-2,2′-bipyridyl) as a light harvester in ssDSSCs.[5] However, the hole conductor is suffering from the charge combination rate and pore-filling factor. Some of the research groups address these drawbacks by minimizing the thickness of TiO2. The PCEs of 3.8% and 6.5% were achieved with the device with CH3NH3PbI3 as the photosensitizer and iodide/triiodide (I/I3–)-based liquid electrolyte by Miyasaka and Park’s group.[6] Using similar perovskite materials and the different hole conductor spiro-OMeTAD, in 2012 Kim’s group reported the PCE of 9.7% with the Jsc of 17 mA/cm2, a VOC of 0.888 V, and a FF of 0.62. This was the first time the highest PCE with a spiro-OMeTAD-penetrated mesoscopic TiO2 film based device was reported. Further, the PCE was shown to reach up to 10.9% by Snaith et al. Then the perovskite solar cells (PSCs) came into existence, where spiro-OMeTAD as a solid hole-transporting material (HTM) and perovskite as the light-harvesting material are used. It is noted that a huge enhancement in PCE is gained within a decade (3.8% to 24.2%), which is competitive with the commercially available silicon solar cells.[7]

The PSCs have unique properties like better molar extinction coefficients, good charge carrier mobility, tunable band gaps, and effective temperature processability.[8] Tremendous research is being conducted for the advancement of perovskite light-harvesting material and fabrication techniques in PSCs. Generally, the PSC device architecture consists of the five components: transparent conductive oxide layer (FTO conductive substrate), an electron-transporting layer (n-type mesoporous semiconductor metal oxide), light-harvesting material (perovskite), hole-transporting layer (spiro-OMeTAD), and metal electrode (Au). The device architecture, different types of perovskite devices (Figure a–d), energy level diagram (e), energy levels of the existing HTMs (f), and crystal structure (g) are shown in Figure .

Figure 1

(a–d) Different types of perovskite device architecture. (e) Energy level diagram. (f) Energy levels of various HTMs. (g) Crystal structure of perovskite solar cell.

To improve the performance of the devices, we have to enhance the properties of the hole-transporting materials (HTMs). A lot of research is being done on the active layer and hole-transport layer (HTL) to produce stable PSCs for its commercialization.[9] HTMs are crucial components for the PSCs to improve the PCE as well as stability.[10] To become the champion HTMs, they should possess the following properties: better photochemical and thermal stability, good alignment of the highest occupied molecular orbital (HOMO) for facile hole transfer, and better hole mobility. To date, spiro-OMeTAD is the champion HTM for the PSCs with the PCE over 20%. However, its synthesis is tedious and costly, and hole mobility is low (∼10–5 cm2 V–1 s–1), which inhibits poor device performance, thereby limiting the scope of commercialization. To make PSCs a commercial product in the market, many research groups are working on the HTMs, which are essential for better stability and high PCE. Until now, various organic HTMs are studied with the spirobifluorene cores, triphenylamine, tetraphenyl, 3,4-ethylenedioxythiophene, fluorene, carbazole, and tetrathiafulvalene.[11]

Among them, recently, phenothiazine (PTZ)-based HTMs came into the picture for PSCs and were shown to be a good candidate for the PSCs which have also shown good performance in DSSCs. Phenothiazine is a well-known electron-rich heterocyclic compound inbuilt with the heteroatom’s nitrogen and sulfur. It can produce a stable radical cation with reversible oxidation and low potential.[12] The phenothiazine exists in the butterfly confirmation, which prevents molecular aggregation, and good hole-transport capability encouraged their identity in the DSSCs,[13] OLEDs, and OPVs.[14] The optical properties are also affected by the degree of disorder in phenothiazine film and molecular aggregation.[15,16] In this mini-review, we have discussed the optical, electrochemical, and photovoltaic properties of phenothiazine-based small-molecule HTMs.

In 2018, the Wang group reported three D–A–D HTMs with a dithienopyrrolobenzothiadiazole (DTPBT) core with end group triarylamine, a phenothiazine (PTZ), and alkoxy-triarylamine termed as HZ1, HZ2, and HZ3, respectively (Figure ). Among them, the HZ2 contains the donor group phenothiazine, which shows the highest PCE of 14.2% with the Jsc of 20.43 mAcm–2, Voc of 1.026 V, and FF of 68%, and better stability (over 280 h at a dehumidification wardrobe with 20% relative humidity without encapsulation) compared to the HZ1 (7.0%), the HZ2 (10.2%), and close to the state-of-the-art spiro-OMeTAD (14.9%). It is a well-known fact that the phenothiazine moiety will be planar in geometry, which is in favor of intermolecular stacking. The large π-conjugated DTPBT/PTZ made a possible way to get better hole mobility and conductivity. The HTM HZ2 was shown to have a little higher conductivity (3.20 × 10–4 S cm–1) and hole mobility (4.80 × 10–4 cm2 V–1 s–1) than the spiro-OMeTAD. The fill factor is also responsible for the good photovoltaic performance, which was influenced by the shunt resistance (Rsh) and series resistance (Rs). The observed Rsh was 2.08 kΩ cm2 for HZ2 which is higher than the HZ1 and HZ3 and resulted in the enhancement of the short-circuit current of the HZ2. The HZ2 showed the Rs of 9.6 Ω cm2, which is smaller than other devices HZ1 and HZ3. The nanosecond absorption spectroscopy (ns-TAS) showed a τTAS value of 139 ns for the HZ2. These values are a little less than the spiro-OMeTAD (τTAS of 148 ns).[17]

Figure 2

Molecular structures of the HZ1, HZ2, and HZ3 (reproduced with permission from ref (17)).

Grätzel et al. developed three HTMs with PTZ moiety attached by the double bonds with the end groups (4,4-dimethyltriphenylamine (Z28), N-ethylcarbazole (Z29), and 4,4-dimethoxytriphenylamine (Z30)) (Figure ). The HTMs were affordably synthesized in three simple steps including electrophilic substitution followed by the Vilsmeier and Witting reactions. All the HTMs showed intramolecular transitions (ICT) around 400–450 nm. The Z29 showed a blue shift compared to the Z28 and Z30, because of the lower conjugation. The HOMO values of Z28, Z29, and Z30 are −5.93 eV, −5.44 eV, and −5.27 eV, respectively, which are higher than the double cation perovskite (−5.5 eV). The LUMO values were found at −2.83 eV, −2.82 eV, and −2.73 eV, respectively, and well-aligned with the double cation LUMO level for smooth hole transfer.[18]

Figure 3

Molecular structures of Z28, Z29, and Z30 (reproduced with permission from ref (18)).

The hole mobility was measured using the space charge limited current (SCLC). The hole mobility of the Z28, Z29, and Z30 was found to be 6.18 × 10–5, 6.82 × 10–6, and 6.70 × 10–5 cm2 V–1 s–1, respectively. The highest PCE of 19.17% with the Jsc of 23.53 mA cm–2, Voc of 1.114 V, and FF of 0.73% was observed in Z30 compared to the Z28 PCE of 17.77% (Jsc of 23.01 mA cm–2, Voc of 1.087 V, and FF of 0.60%) and Z29 (Jsc of 22.35 mA cm–2, Voc of 1.114 V, and FF of 0.73%) (Figure ). The Z28 showed lower PCE because of the HOMO energy level, which was because the double cation perovskite leads the insufficient driving force of hole injection and less hole mobility. The overall conclusion was that the PCE was affected by the conjugation of the molecular structures. The HTM Z30 containing the highly conjugated 4,4-dimethoxytriphenylamine showed better PCE, and Z28 consists of the less conjugated peripheral group (N-ethylcarbazole), leading to lower PCE. The same strategy was followed in the stability studies also.

Figure 4

(a–d) Current–voltage hysteresis curves of PSCs comprising champion devices with HTMs measured starting with backward scan and continuing with forward scan. The inset is the stabilized power output of three HTM-based devices. (e) The stabilized power output of the corresponding devices. (f) IPCE spectra and integrated current curves of the corresponding devices (figure adapted from ref (18)).

The research group of Roberto Grisorio synthesized two HTMs with the PTZ core attached by the donor group’s diarylamine (PTZ1) and triarylamine (PTZ2) (Figure ). They concluded that the optical and photovoltaic properties of the PSCs are mostly affected by the small variation in the molecular design. The molecules were synthesized by the well-known synthetic steps such as Buchwald–Hartwig and Suzuki–Miyaura cross-couplings with the synthesis cost of PTZ1 (111.90 $/g) and PTZ2 (156.76 $/g), which are much less than that of spiro-OMeTAD (∼600 $/g).

Figure 5

Chemical structures of the PTZ1 and PTZ2 (reproduced with permission from ref (19)).

The absorption maxima were found for PTZ1 at 282 nm with a shoulder peak at the longer wavelength, and for PTZ2 it was observed at 308 and 332 nm. For PTZ1 and PTZ2, HOMO values were found at −4.77 and −5.15 eV, respectively, following the same conditions as the spiro-OMeTAD, showing −5.02 eV. PTZ2 showed higher Voc due to the favorable oxidation potential. The stability studies revealed that PTZ2 (359 °C) is more stable compared to PTZ1 (416 °C) with the Tg of 74 and 135 °C (Figure ). The PSC device of the double cation mixed halide perovskite with PTZ1, PTZ2, and spiro-OMeTAD showed the Jsc of 4.2, 21.1, and 21.6 mA/cm2, a Voc of 0.82, 1.11, and 1.15 V, and FF of 0.61, 0.75, and 0.71 along with a PCE of 2.1%, 17.6%, and 17.7%, respectively.[19]

Figure 6

(A) Thermogravimetric analysis of PTZ1 and PTZ2 measured with a heating rate of 10 °C min–1. (B) Second DSC heating traces of HTMs previously heated and cooled with a scan rate of 10 °C min–1 under nitrogen atmosphere. (C) Absorption spectra of PTZ1 and PTZ2 recorded in dichloromethane (3.0 × 10–5 M) and normalized photoluminescence spectra (λex = 350 nm). (D) Cyclic voltammograms of HTMs in dichloromethane solutions (1.0 × 10–4 M) using Bu4NBF4 (0.1 M) as the supporting electrolyte (figure adapted from ref (19)).

Salunke’s group developed a similar molecular design of PTZ2 and Z30 using low-cost two-phenothiazine-based HTMs (AZO-I and AZO-II) functionalized with azomethine moieties (Figure ). These HTMs are synthesized via Schiff base chemistry which is an eco-friendly, simple Pd-free synthetic route. The AZO-I and AZO-II are the least costly phenothiazine-based HTMs to date (9 and 12 $/gram). The PTZ2 and Z30 were prepared by the Pd-catalyzed Suzuki coupling and yielded 24.9% and 27.7%. In case of the AZO-I and AZO-II, they are synthesized by the Pd-free synthetic route with 51% and 40% yield, respectively. Due to the length of conjugation, λmax was red-shifted in the DCM solvent (AZO-II: 453 nm, AZO-I: 422 nm). The HOMO values of the AZO-1, AZO-II, and spiro-OMeTAD were −4.97, −4.94, and −4.80 eV, respectively, which are well aligned with the mixed cation perovskite. The stability studies revealed that the AZO-II is stable up to 405 °C with the Tg at 120 °C, and AZO-I was up to 392 °C with the Tg at 85 °C. The higher Tg was found in the AZO-II because of the high molecular weight and stiffness. The HTM AZO-II showed higher hole mobility (2 × 10–6 cm2 V–1 s–1) compared to the AZO-I (2 × 10–5 cm2 V–1 s–1) due to the two-electron-donating triarylamine groups on the phenothiazine core.[20]

Figure 7

Chemical structures of the HTMs AZO-I and AZO-II (reproduced with permission from ref (20)).

The PSC devices (ITO/SnO2/Cs0.05MA1–FAPbI3–Cl/HTM/Au) with the HTMs AZO-I and AZO-II exhibited a PCE of 14.3% and 15.6%, with the Jsc of 20.1 mA cm–2 and 21.6 mA cm–2, Voc of 1.00 and 0.95 V, and FF of 0.66 and 0.71, respectively. In AZO-I, the interaction with the perovskite was poor because the high hysteresis resulted in a low PCE. In similar conditions, the champion HTM spiro-OMeTAD showed a PCE of 19.3% with the Jsc of 23.4 mA cm–2, Voc of 1.04 V, and FF of 0.74 (Figure ).

Figure 8

(a) Current density–voltage (J–V) curves for perovskite solar cells (reverse scans) measured with a scan rate of 10 mV/s under AM 1.5G simulated solar light illumination by using spiro-OMeTAD, AZO-I, and AZO-II as HTMs. PCE (b), JSC (c), FF (d), and Voc (e) distributions of PSC devices based on different HTMs (figure adapted from ref (20)).

Recently, Cheng et al. developed two novel phenothiazine 5,5-dioxide (PDO) based low-cost (62.1791 $/g and 61.2761 $/g) HTMs. In PDO1, the PDO N-position with anisole and the PDO2 N-position with 4,4′-dimethoxytriphenylamine and 4,4′-dimethoxydiphenylamine are the end groups (Figure ). These are synthesized by the Buchwald–Hartwig reaction followed by the radical substitution and oxidation. The conversion of PTZ to PDO has resulted in a better charge affinity of the moiety. The λmax was observed at around 350 nm, and HOMO energy levels were calculated as −5.25 and −5.24 eV vs vacuum, for the PDO1 and PDO2, respectively, revealing that the substitution at the N-site of the PDO moiety will not be affected more on the optical properties.[21]

Figure 9

Molecular structures of the PDO1 and PDO2 (reproduced with permission from ref (21)).

The PDO moiety was found as a twisted butterfly and planar conformation with the monoclinic space group C2/c and I2/a in PDO1 and PDO2, respectively. The device was fabricated with the mixed cation and halide perovskite (FAPbI3)0.85(MAPbBr3)0.15 as the light-harvesting material and PDO1 and PDO2 as the HTMs under simulated AM 1.5 G (100 MW cm–2). The observed Jsc of 22.6 mA·cm–2 and 23.9 mA·cm–2, Voc of 1.08 and 1.15 V, and FF of 68.3 and 73.6 with a PCE of 16.7% and 20.2% for the PDO1 and PDO2, respectively. The hysteresis index values were 0.025 and 0.016% observed from the scan of open circuit (OC) to short circuit (SC) (Figure ). Under the similar conditions the spiro-OMeTAD resulted in a PCE of 19.8% with the Jsc of 24.2 mAcm–2, Voc of 1.14, and FF of 71.1 and hysteresis index of 0.020%. The best efficiency was observed for the PDO2, which has a planar structure of the PDO core and good molecular stacking behavior. The successful molecular engineering of the HTMs with the conversion of the electron-donating sulfur atom to the electron-withdrawing sulfone group (from PTZ to PDO) and N-substitution strongly influenced the electron affinity, energy level alignment, photovoltaic properties, and the charge carrier mobility.

Figure 10

J–V characteristic curves of the PSCs contain (a) PDO1, (b) PDO2, and (c) spiro-OMeTAD as HTMs, (d) IPCE spectra of PSCs containing PDO1, PDO2, and spiro-OMeTAD as HTMs, (e) steady-state power outputs at the maximum point, and (f) statistics of PCE for PSCs containing PDO1 and PDO2 as HTMs (figure adapted from ref (21)).

Tsang’s group synthesized the D−π–D skeleton containing PTZ-based dopant-free HTMs (BDT-PTZ and BDT-POZ), for p-i-n PSCs (Figure ). The molecular design consists of the two donor moieties connected through a fused thiophene core, which is responsible for the better hole mobility and electron-donating ability. These are prepared by the simple Suzuki coupling of the bromohexyl donor and fused thiophene moieties. The λmax was noted at around 440 nm, and BDT-POZ was red-shifted compared to the BDT-PTZ in the case of both the solution (chloroform) and solid phase. The HOMO and LUMO values were calculated as −5.42 eV, −5.35 eV and −2.81, −2.78 eV for BDT-PTZ and BDT-POZ, respectively, which are well-matched with the MAPbI3 energy level.[22]

Figure 11

Molecular structures of the HTMs (reproduced with permission from ref (22)).

By using the SCLC method, the hole-based device (indium tin oxide (ITO)/poly(3,4-ethylenedioxythiophene)-poly(styrenesulfonate) (PEDOT:PSS)/HTM/MoO3/Ag) and the HTMs BDT-POZ, BDT-PTZ, and PTAA showed hole mobilities of 2.1 × 10–4 cm2 V–1 s–1, 9.8 × 10–5 cm2 V–1 s–1, and 4.1 × 10–5 cm2 V–1 s–1, respectively. The BDT-POZ showed nearly two-times higher hole mobility compared to the BDT-PTZ and five times more than the PTAA because of the smaller N–N distance between redox centers and proper molecule packing. To know the hole extraction behaviors, steady-state and transient photoluminescence (PL) spectra were recorded for perovskites, BDT-POZ, BDT-PTZ, and bare glass. The strong steady PL peak of MAPbI3 is clearly observed in the MAPbI3/glass, and when coming to the MAPbI3/BDT-PTZ, the peak intensity was decreased compared to the MAPbI3/BDT-POZ, suggesting the best hole extraction efficiency compared to the MAPbI3/BDT-PTZ. This is further confirmed by TRPL, and the average PL lifetimes of 114.9, 42.1, and 25.8 ns were found from MAPbI3/glass, MAPbI3/BDT-PTZ, and MAPbI3/BDT-POZ, respectively. The MAPbI3/BDT-POZ showed less PL, due to the better charge carrier ability (Table ). In order to know the suitability of the HTM, the device architecture with the ITO/HTM(BDT-PTZ) and BDT-POZ as dopant-free HTMs/MAPbI3/[6,6]-phenyl-C(61)-butyric acid methyl ester/bathocuproine/Ag was fabricated. The inverted device with 4 mg mL–1 of BDT-POZ resulted in a Jsc of 22.46 mA cm–2, a Voc of 0.96 V, FF of 84.4%, and overall PCE of 18.20%, and a concentration increase of up to 8 mg mL–1, the small increment of the Jsc from 22.46 to 22.56 mA cm–2, Voc from 0.96 to 1.04 V, and a slight decrease in FF from 84.4% to 81.7% were observed. The p-i-n device with the optimized concentration and dopant-free BDT-PTZ, BDT-POZ, and PTAA resulted in the Jsc of 22.43, 22.56, and 22.26 mA cm–2, Voc of 1.02, 1.04, and 1.08 V, FF of 79.8, 81.7, and 74.2%, and the overall PCE of 18.26, 19.16, and 17.85%, respectively, under AM 1.5 G illumination with the small hysteresis (Figure ).

Table 1

Parameters of Lifetimes (τ) and Weight Fractions (A) Derived from TRPL Decay Studies

HTM	τ1 (ns)	A1 (%)	τ2 (ns)	A2 (%)	τavg (ns)
no HTM	114.9	100	-	-	114.9
BDT-PTZ	46.4	32.3	2.37	67.7	42.1
BDT-POZ	31.2	24.4	2.31	75.6	25.8

Figure 12

(a) J–V curves and (b) external quantum efficiency (EQE) spectra of PSCs with BDT-PTZ and BDT-POZ (figure adapted from ref (22)).

Robertson et al. reported triphenylbenzene (TPB) core based HTMs, 1,3,5-tris(2′-((N,N-di(4-methoxyphenyl)amino)phenyl))benzene (TPB(2-MeOTAD)) and 1,3,5-tris(2′-(N-phenothiazoyl)phenyl)benzene (TPB(2-TPTZ)) (Figure ). First, they replaced the 4,4′-dimethoxydiphenylamine with the PTZ unit. The synthesis involved a low cost two-step starting material 1,3,5-tris(2-bromophenyl)-benzene that was prepared using the aldol condensation and Buchwald–Hartwig coupling, resulting in the final HTMs with notable yields (73% and 50%) and with the cost of 12.98 $ g–1 and 3.09 $ g–1, respectively. The manufacturing cost is less than the standard spiro-OMeTAD (100 to 400 $ g–1). The absorption spectra were recorded in the DCM solvent. The absorption maxima of the TPB(2-TPTZ) were shifted 23 nm toward the red region (323 nm) compared to the 4,4′-dimethoxydiphenylamine-substituted TPB(2-MeOTAD). The calculated HOMO values were −5.29 eV and −5.34 eV, respectively, which are lower than the −5.44 eV (spiro-OMeTAD) and matched with a perovskite (MAPbI3) valence bond for smooth hole injection. The HTMs are stable up to around 120 °C, and Tg values of TPB(2-MeOTAD) and TPB(2-TPTZ) were observed at 89 and 110 °C, respectively, and at 122 °C for spiro-OMeTAD. In order to investigate the performance of SFX-MeOTAD as a hole transport material in perovskite solar cells, the FTO/ZnO-Mg-EA(NH3+)/m-TiO2/MAPbI3/HTM were fabricated and compared with spiro-OMeTAD.

Figure 13

Chemical structures of HTMs (reproduced with permission from ref (23)).

The overall PCEs of TPB(2-MeOTAD) and TPB(2-TPTZ) were 12.14% and 4.32% with the Jsc of 19.32 and 8.89 mA cm–2, Voc of 0.97 and 0.88 V, and the FF of 64.54% and 55.30%, respectively. The state-of-the-art spiro-OMeTAD yielded a PCE of 18.04%. The TPB(2-TPTZ) showed lower efficiency with higher stability. The stability studies were performed using a dry and dark box, at 25 °C, and the relative humidity was 30%. The initial PCEs of 85% (TPB(2-TPTZ)), 75% (TPB(2-MeOTAD)), and 72% (spiro-OMeTAD) were retained over 300 h, respectively. The faster degradation was observed in TPB(2-TPTZ) (85%), which consisted of hydrophilic dimethoxy diphenylamine as a side chain and better stability observed due to the hydrophobic nature of the phenothiazine.[23]

To reduce the cost of the HTMs, Robertson developed a series of spiro[fluorene-9,9′-xanthene] SFX-based HTMs, SFX-TAD, SFX-TCz, SFX-TPTZ, and SFX-MeOTAD (Figure ). These HTMs were synthesized using the Buchwald–Hartwig amination reaction between 2,2′,7,7′-tetrabromo-spiro(fluorene-9,9′-xanthene) in very good yields of 71%, 56%, 35%, and 83%, respectively. The UV–visible spectra were measured in the presence of the DCM solution. There were two absorption bands observed at 307, 367, 307, 379, 291, and 340 nm, for the SFX-MeOTAD, SFX-TAD, and SFXTCz, while SFX-TPTZ showed one broad absorption peak at λmax = 310 nm. From the cyclic voltammetry studies, the HOMO value was determined as −5.34, −5.70, and −5.39 eV for SFX-TAD, SFX-TCz, and SFX-TPTZ and as −5.1 eV for SFX-MeOTAD, which was similar to the spiro-OMeTAD (Figure ). The lower HOMO of the SFX-TAD and SFX-TPTZ resulted in the high Voc.[24]

Figure 14

Chemical structures of HTMs (reproduced with permission from ref (24)).

Figure 15

(a) Cyclic voltammograms and (b) square-wave voltammetry (SWV) traces of the SFX series and spiro-OMeTAD in DCM solution with supporting electrolyte of 0.3 M tetrabutylammonium tetrafluoroborate referenced to ferrocene (figure adapted from ref (24)).

The XRD study reveals that all HTMs were well crystallized in monoclinic C2/c(SFX-TPTZ), triclinic space group P1–(SFX-MeOTAD), and orthorhombic Pbca(SFX-TCz). The three hydrogen bonds are formed in the SFX-MeOTAD with lengths of 2.549 Å and 2.572 Å for OMe–OMe and 2.522 Å for CHO (xanthenes). The dihedral angles 87.54°, 88.89°, and 87.57° were found between xanthenes and fluorene moieties for SFX-MeOTAD, SFX-TPTZ, and SFX-TCz, which are similar to spiro-OMeTAD (89.94°). The thermal study (differential scanning calorimetry) data revealed that the Tg value was observed at 270 °C for SFX-TPTZ and SFXTCz and at 122 °C, 118 °C, and 108 °C for spiro-OMeTAD, SFX-TAD, and SFX-MeOTAD, respectively.

To calculate the efficiency, the device with glass/FTO/compact TiO2/mesoporous Al2O3/CH3NH3PbI3–Cl/HTM/Au and SFX-MeOTAD exhibited the PCE of 12.4%, near the spiro-OMeTAD PCE of 13.0%, and showed higher Voc and less Jsc and FF compared to others. The hole mobility of SFX-MeOTAD (1.6 × 10–5 S cm–1) was also similar to the spiro-OMeTAD (1.4 × 10–5 S cm–1), respectively.

Zhao’s group designed and developed the SFX core-based HTMs termed as SFX-PT1 and SFX-PT2 along with the spiro-PT. The HTMs SFX-PT1 and SFX-PT2 were prepared by the Buchwald–Hartwig amination in good to excellent yield (Figure ). The λmax was found at around 321 nm for both SFX-PT1 and SFX-PT2, while spiro-PT showed 313 nm (Figure ). The cyclic and differential pulse voltammetry studies were recorded to know the HOMO level of HTMs. The HOMO values were observed as −5.08 eV, −5.20 eV, and −5.33 eV for SFX-PT1, SFX-PT2, and spiro-PT, respectively. Spiro-PT, SFX-PT1, and SFX-PT2 possess higher decomposition temperatures (Td) and Tg of 324 °C, 435 °C, 421 °C, 110 °C, 153 °C, and 148 °C, respectively. The hole mobilities of the SFX-PT1, SFX-PT2, and spiro-PT are calculated as 2.08 × 10–3 cm2 V–1 S–1, 2.76 × 10–4 cm2 V–1 S–1, and 1.29 × 10–4 cm2 V–1 S–1, respectively. The hole mobility of SFX-PT1 is more than the spiro-OMeTAD (2.0 × 10–4 cm2 V–1 S–1).[25] Optical and photovoltaic parameters of mentioned HTMs are shown in Table .

Figure 16

Molecular structures of SFX-PT1, SFX-PT2, and spiro-PT (reproduced with permission from ref (25)).

Figure 17

(a) Absorption and photoluminescence spectra. (b) Cyclic voltammograms of SFX-PT1, SFX-PT2, and spiro-PT (figure adapted from ref (25)).

Table 2

Optical and Photovoltaic Properties of the HTMs

HTM	HOMO (eV)	LUMO (eV)	E0–0 (eV)	hole mobility (cm2 V–1 s–1)	JSC (mA cm–2)	VOC (V)	FF	PCE (%)	ref
HZ1	–5.29	–3.00	2.29	3.49 × 10–4	18.30	0.82	46	7.0	(17)
HZ2	–5.30	–3.04	2.26	4.80 × 10–4	20.43	1.02	68	14.2	(17)
HZ3	–5.22	–2.94	2.28	4.06 × 10–5	19.44	0.92	57	10.2	(17)
Z28	–5.39	–2.83	2.56	6.18 × 10–5	23.01	1.12	69	17.77	(18)
Z29	–5.44	–2.82	2.62	6.82 × 10–6	22.35	1.08	60	14.65	(18)
Z30	–5.27	–2.73	2.54	6.70 × 10–5	23.53	1.11	73	19.17	(18)
PTZ1	–4.77	–1.74	3.03	-	4.2	0.82	61	2.1	(19)
PTZ2	–5.15	–2.39	2.76	-	21.1	1.11	75	17.6	(19)
AZO-I	–4.97	–2.67	2.30	2 × 10–5	20.1	1.00	66	14.3	(20)
AZO-II	–4.94	–2.74	2.20	2 × 10–6	21.6	0.95	71	15.6	(20)
PDO1	–5.25	–2.35	2.90	1.76 × 10–4	22.6	1.08	68.3	16.7	(21)
PDO2	5.24	–2.67	2.57	5.93 × 10–4	23.9	1.15	73.6	20.2	(21)
BDT-PTZ	–5.42	–2.81	2.62	9.8 × 10–5	22.43	1.02	79.8	18.26	(22)
BDT-POZ	–5.35	–2.78	2.57	2.1 × 10–4	22.56	1.04	81.7	19.16	(22)
TPB(2-MeOTAD)	–5.29	–1.75	3.54	-	19.32	0.97	64.54	12.14	(23)
TPB(2-TPTZ)	–5.34	–2.02	3.32	-	8.89	0.88	55.30	4.32	(23)
SFX-MeOTAD	–5.16	–2.20	2.96	1.6 × 10–5	21.38	0.98	59.0	12.4	(24)
SFX-TAD	–5.34	–2.27	3.07	-	-	-	-	-	(24)
SFX-TCz	–5.70	–2.31	3.39	-	-	-	-	-	(24)
SFX-TPTZ	–5.39	–2.14	3.25	-	-	-	-	-	(24)
SFX-PT1	–5.08	–1.93	3.15	2.08 × 10–3	-	-	-	-	(25)
SFX-PT2	–5.20	–2.04	3.16	2.76 × 10–4	-	-	-	-	(25)
spiro-PT	–5.33	–2.18	3.15	1.29 × 10–4	-	-	-	-	(25)

Summary and Outlook

In this mini-review, we have summarized the research progress on the PTZ-based HTMs. The HTMs are the crucial components to enhance the PCE along with the stability. This review provided the basic idea about the PSC device architecture and information about phenothiazine-based HTMs. There is rapid growth happening in the perovskite solar cells; therefore, there is a need to develop a highly stable device that consists of a better perovskite layer and an efficient and cost-effective electron/hole transport layers. Until now, the champion spiro-OMeTAD is used as the HTM layer, which includes tedious synthesis and an expensive process. Hence, researchers are looking toward the development of less expensive new transport materials to promote the PSCs into the commercial market. Simultaneously, the novel HTMs should be stable and synthesized from sustainable sources of materials; tunable energy levels with high mobility will provide efficient and stable PSCs. In this scenario, PTZ-based HTMs came into existence because of the favorable optoelectronic properties, cheap synthetic route, suitable electron-donating nature, and better hole mobility. The PTZ is an electron-rich hetero aromatic core, which leads to the production of various HTMs with low-cost production. In this mini-review, we conclude the importance of the PTZ moiety to improve the efficiency as well as stability of the perovskite solar cell devices.