The Role of the Axial Substituent in Subphthalocyanine Acceptors for Bulk-Heterojunction Solar Cells.

Four hexachlorosubphthalocyanines SubPcCl6 -X bearing different axial substituents (X) have been synthesized for use as novel electron acceptors in solution-processed bulk-heterojunction organic solar cells. Subphthalocyanines are aromatic chromophoric molecules with cone-shaped structure, good solution processability, intense optical absorption in the visible spectral region, appropriate electron mobilities, and tunable energy levels. Solar cells with subphthalocyanines as the electron acceptor and PTB7-Th as the electron donor exhibit a power conversion efficiency up to 4 % and an external quantum efficiency approaching 60 % due to significant contributions from both the electron donor and the electron acceptor to the photocurrent, indicating a promising prospect of non-fullerene acceptors based on subphthalocyanines and structurally related systems.

Solution‐processed bulk‐heterojunction (BHJ) organic solar cells (OSCs) are a promising renewable‐energy technology towards future efficient, large‐area, flexible photovoltaic modules.1 The main component of an OSC is its BHJ‐active layer, consisting of an electron‐donor and an electron‐acceptor phase separated into a bicontinuous interpenetrating network morphology.2 Power conversion efficiencies (PCEs) exceeding 11 % have been achieved recently.3 While numerous electron donors, including semiconducting polymers and small molecules, have been assessed,4 electron‐acceptor components are still dominated by fullerene derivatives because of their high electron mobility, ideal frontier orbital energy levels, and isotropic charge‐transport properties.5 However, fullerene derivatives have intrinsic shortcomings, such as high cost of synthesis, low absorption coefficients in the visible spectral region, limited variability in the energy levels, and morphological instability in the blended films.6 The development of new electron acceptors which overcome the drawbacks associated with fullerene‐based acceptors is thus vital for further advancing OSCs.7 Encouragingly, several studies have reported BHJ solar cells with PCEs >8 % based on non‐fullerene acceptors.8

Subphthalocyanines (SubPcs) are aromatic chromophoric molecules with a boron atom at their inner cavity, intense optical absorption in the 460–580 nm spectral region,9 and relatively high electron mobilities.10 Traditionally, they have been used as electron donors in vacuum‐deposited planar‐heterojunction solar cells.9a However, the electronic properties of SubPcs can be easily adjusted by introducing axial and/or peripheral substituents.9a Hence, by rational molecular design, that is, introducing peripheral electron‐withdrawing groups, SubPcs have been transformed into electron‐acceptor molecules.11 For example, non‐fullerene vacuum‐evaporated solar cells containing SubPc molecules achieved a PCE of 8.4 %.12 The cone‐shaped structure of SubPcs prevents excessive aggregation in solution and in the solid state, providing good solution processability even without the assistance of electrically insulating alkyl chains. Nevertheless, only very recently, SubPc molecules have been demonstrated as electron acceptors in solution‐processed BHJ solar cells.13

Herein, we report on four hexachlorosubphthalocyanines (SubPcCl6‐X) bearing different axial substituents, that is, chlorine and differently substituted phenoxy groups, as electron acceptors in BHJ solar cells. SubPcCl6‐Cl has demonstrated great potential as n‐type material in planar‐heterojunction OSCs.11 Modification of the axial substituent results in a slight variation of the electron‐accepting character of the molecule and can greatly affect its aggregation and crystallization behavior. A maximum PCE of 4.0 % has been achieved for SubPcCl6‐Cl, which is the highest value for solution‐processed solar cells based on SubPc derivatives. This work paves the way to a new class of non‐fullerene acceptors with tunable optoelectronic properties and microstructures for efficient BHJ OSCs.

Four axially substituted SubPcCl6‐X derivatives, shown in Figure 1, were used in this study. SubPcCl6‐Cl was prepared according to a literature procedure.11d Reaction with selected phenol derivatives with electron‐donating or ‐withdrawing substituents provided SubPcCl6‐OC6H2(OMe)3, SubPcCl6‐OC6H4 Bu, and SubPcCl6‐OC6F5 in good yields (see the Supporting Information (SI) for synthetic procedures).

Figure 1

Chemical structures of the electron‐acceptor SubPc derivatives and the donor polymer PTB7‐Th used in this work.

All four SubPc compounds feature almost identical absorption spectra in toluene, signifying a small influence of the axial substituents. The Q‐band peaks are found at wavelengths around 570 nm with absorption coefficients of 4.0×104–4.5×104  m −1 cm−1 (Figure S2, Table 1). In films, the absorption spectra of SubPcCl6‐X (Figure 2 a) show a bathochromic shift of about 10 nm compared to the spectra in solution (Table 1). Remarkably, the SubPcCl6‐Cl absorption spectrum in film displays a broader Q band with an additional intense maximum at 558 nm, which could be attributed to the formation of head‐to‐tail columnar stacks (H‐type‐like aggregates) in the solid state, favored by the presence of the small chlorine atom in the axial position. Axial substitution with bulky phenoxy groups in the other three SubPcCl6‐X derivatives precludes this behavior. The fluorescence quantum yield ϕ F of SubPcCl6‐Cl, SubPcCl6‐OC6H4 Bu and SubPcCl6‐OC6F5 in toluene is around 0.35–0.64, but it is only 0.003 for SubPcCl6‐OC6H2(OMe)3. The strong quenching in the latter is attributed to an intramolecular photoinduced electron‐transfer process from the electron‐rich axial phenoxy substituent to the SubPc acceptor.

Table 1

Optical properties and energy levels of the boron subphthalocyanine derivatives SubPcCl6‐X.

X	λ max [nm]		E g opt [eV]	HOMO [eV]	LUMO [eV]	ϕ F
	solution	film
C6H2(OMe)3	572	584	2.16	−6.00	−3.84	0.003
OC6H4 tBu	571	584	2.16	−6.02	−3.86	0.351
Cl	574	582	2.16	−6.06	−3.90	0.643
OC6F5	572	582	2.15	−6.08	−3.93	0.429

Figure 2

SubPcCl6‐X: a) optical absorption spectra of their films and b) their energy levels.

Electrochemical properties of the four SubPcCl6‐X derivatives were investigated by cyclic voltammetry (CV) and square‐wave voltammetry (SWV) in tetrahydrofuran (Figure S4 (SI), Figure 2 b, and Table 1). The LUMO and HOMO energy levels were estimated from the reduction potentials obtained by CV measurements and optical‐band‐gap (E g opt) values. While peripheral electron‐withdrawing chlorine substituents govern SubPcCl6‐X electron affinities, axial substitution allows fine‐tuning of the LUMO and HOMO levels in a 0.1 eV range, resulting in LUMO and HOMO energies spanning from −3.84 and −6.00 eV, respectively, for SubPcCl6‐OC6H2(OMe)3 to −3.93 and −6.08 eV, respectively, for SubPcCl6‐OC6F5 (Table 1).

The photovoltaic properties of the SubPc molecules were evaluated in solar cells with an ITO/ZnO/PTB7‐Th:SubPcCl6‐X/MoO/Ag device architecture under simulated AM1.5G illumination (100 mW cm−2). The current density–voltage (J–V) characteristics and external quantum efficiency (EQE) spectra of the optimized devices are shown in Figure 3 and summarized in Table 2. To accurately determine the PCEs of the solar cells, the short‐circuit current density (J sc) was obtained by integrating the EQE with the AM1.5G spectrum. Results from different fabricating conditions and device statistics can be found in Table S1 and S2. Solar cells with a structure that uses either ITO/PEDOT:PSS or ITO/MoOx as bottom contacts all produced very poor results, possibly caused by an unfavorable vertical phase segregation (Figure S5). The highest PCE of 4.0 % was found for SubPcCl6‐Cl, which offered a J sc of 10.7 mA cm−2, an open‐circuit voltage (V oc) of 0.77 V, and a fill factor (FF) of 0.48. In each case both the polymer donor and the SubPc acceptor contribute substantially to the photocurrent (Figure 3 b). The EQE maxima located at about 710 nm originate from PTB7‐Th, while the peaks at about 570 nm result from the SubPc molecules. The lack of light absorption of PTB7‐Th and SubPcCl6‐X between 350 and 450 nm results in a rather uncommon shape in the EQE spectra, with a valley in this region. At higher wavelengths, an impressive EQE maximum of 0.58 was achieved for SubPcCl6‐Cl, while the other SubPc molecules produced significantly lower EQE and J sc values. As a result, these devices all afforded PCEs below 2.0 %. Notably, except for SubPcCl6‐OC6F5, the SubPc solar cells exhibit a similar V oc value (about 0.8 V) as PTB7‐Th:fullerene devices. Table 2 also shows that a common limitation of these solar cells is their low FF (<0.5), which is considerably lower than that of the state‐of‐the‐art fullerene‐based devices. Understanding the origin of the low FF of these devices is crucial to further develop SubPc‐based acceptors.

Figure 3

a) J–V curves of the PTB7‐Th:SubPcCl6‐X solar cells in dark (dashed lines) and under illumination (solid lines); b) corresponding EQE spectra.

Table 2

Solar‐cell characteristics and electron mobilities of PTB7‐Th:SubPcCl6‐X devices.

X	J sc [a] [mA cm−2]	V oc [V]	FF	PCE [%]	EQEmax	μ e [b] [cm2  V−1 s−1]
C6H2(OMe)3	3.6	0.74	0.40	1.1	0.20	1.5×10−6
OC6H4 tBu	5.3	0.81	0.41	1.8	0.29	5.1×10−6
Cl	10.7	0.77	0.48	4.0	0.58	8.3×10−6
OC6F5	2.1	0.50	0.45	0.5	0.12	1.6×10−6

[a] Determined by integrating the EQE spectrum with the AM1.5G spectrum. [b] Electron mobilities were measured in electron‐only devices.

Hence, the charge‐carrier transport properties and the bimolecular charge recombination of the PTB7‐Th:SubPcCl6‐X blend films were investigated. Electron mobilities (μ e) (Table 2) were estimated from electron‐only PTB7‐Th:SubPcCl6‐X devices by fitting the J–V data (Figure S6) to a space‐charge‐limited current model, resulting in μ e≈10−6 cm2 V−1 s−1 for all four acceptors. Keeping in mind that PTB7‐Th:fullerene blends exhibit a μ e of 10−3–10−2 cm2 V−1 s−1,14 the considerably lower μ e values of the PTB7‐Th:SubPcCl6‐X films are likely causing the low FF.

As a result of the low μ e values, PTB7‐Th:SubPcCl6‐X solar cells exhibit substantial bimolecular charge‐recombination losses. These are evidenced by the large difference between the EQE measured with light bias (EQEbias) and without light bias (EQEnobias) (Figure S7). The average values for ρ=EQEbias/EQEnobias (Figure 4) can be used to estimate the bimolecular recombination efficiency via η BR=1−ρ.15 Hence a low ρ value indicates considerable bimolecular recombination. For state‐of‐the‐art polymer:fullerene solar cells ρ approaches unity. The low ρ values of these PTB7‐Th:SubPcCl6‐X devices evidence severe bimolecular recombination losses, even at short circuit. The highest ρ value is found for PTB7‐Th:SubPcCl6‐Cl, which is consistent with the higher μ e value, FF, and PCE of the SubPcCl6‐Cl solar cell. We speculate that the higher performance originates from the H‐type‐like aggregates of SubPcCl6‐Cl in the solid state, which are favorable for charge transport.

Figure 4

Average EQEbias/EQEnobias values of PTB7‐Th:SubPcCl6‐X solar cells.

Next to bimolecular recombination, also geminate recombination can result in a low FF. The current density of illuminated solar cells shows a substantial increase under reverse bias. This can be a consequence of the enhanced internal electric field promoting charge separation from the donor–acceptor interface.

The morphology of PTB7‐Th:SubPcCl6‐X blend films was investigated by transmission electron microscopy (TEM). The blends based on SubPcCl6‐OC6H4 Bu and SubPcCl6‐Cl show homogeneous films without noteworthy phase separation (Figure 5 b and c). In intimately mixed blends, charge separation is prevented because of the lack of pure domains. High domain purity is beneficial for dissociating photogenerated charges from the donor–acceptor interface, while low domain purity often causes serious geminate recombination.16 In the films based on SubPcCl6‐OC6H2(OMe)3 and SubPcCl6‐OC6F5, there is a slightly increased contrast between the light and dark regions, indicating a more distinct phase separation, but these films lack long‐enough fibrillary structure (Figure 5 a and d). Charge‐carrier transport in such films may thus be impeded because of a poor interconnectivity between neighboring domains. Combined, the low electron mobility, the charge recombination, and the morphology explain why PTB7‐Th:SubPcCl6‐X BHJ solar cells show low FF.

Figure 5

Bright‐field TEM images of the PTB7‐Th:SubPcCl6‐X blend films deposited with the same methods as those for OSC fabrication. Image size: 1.5×1.5 μm2; scale bar: 200 nm.

In conclusion, hexachlorosubphthalocyanines bearing different axial substituents have been synthesized and used as electron acceptors in BHJ polymer solar cells. A PCE up to 4.0 % was achieved, which is the highest reported value for solution‐processed SubPc‐based solar cells. Both the polymer donor and the SubPc acceptor contribute significantly to the photocurrent, indicating promising acceptor properties of subphthalocyanines. The main limitation of these SubPc‐based solar cells is their low fill factor, which is a collective result of low electron mobility, serious bimolecular recombination, and suboptimal BHJ morphology. Further research involving subphthalocyanines and structurally related systems such as subnaphthalocyanines should therefore focus on improving electron mobility, avoiding geminate recombination, and controlling microstructure in solid state through rational molecular design.

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Supplementary

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