Donor-Acceptor Polymer Based on Planar Structure of Alkylidene-Fluorene Derivative: Correlation of Power Conversion Efficiency among Polymer and Various Acceptor Units

This study synthesized a novel polymer, poly(alkylidene fluorene-alt-diphenylquinoxaline) (PAFDQ), based on a planar alkylidene-fluorene and a highly soluble quinoxaline derivative through the Suzuki coupling reaction. We designed a novel molecular structure based on alkylidene fluorene and quinoxaline derivatives due to compact packing property by the planar structure of alkyidene fluorene and efficient intra-molecular charge transfer by quinoxaline derivatives. The polymer was largely dissolved in organic solvents, with a number average molecular weight and polydispersity index of 13.2 kg/mol and 2.74, respectively. PAFDQ showed higher thermal stability compared with the general fluorene structure owing to its rigid alkylidene-fluorene structure. The highest occupied and lowest unoccupied molecular orbital levels of PAFDQ were −5.37 eV and −3.42 eV, respectively. According to X-ray diffraction measurements, PAFDQ exhibited the formation of an ordered lamellar structure and conventional edge-on π-stacking. The device based on PAFDQ/Y6-BO-4Cl showed the best performance in terms of short circuit current (9.86 mA/cm2), open-circuit voltage (0.76 V), fill factor (44.23%), and power conversion efficiency (3.32%). Moreover, in the PAFDQ/Y6-BO-4Cl-based film, the phase separation of donor-rich and acceptor-rich phases, and the connected dark domains, was observed.


Introduction
Conducting molecules have long been utilized for diverse applications such as organic light-emitting diodes [1][2][3], organic solar cells (OSCs) [4][5][6][7][8][9][10][11][12][13][14][15], and organic thin-film transistors [16,17]. In particular, OSCs have received considerable attention because of the focus on economic viability and environmental friendliness. However, the low power conversion efficiency (PCE) of conjugated polymers has primarily hindered their use in OSCs [8]. Nevertheless, the donor-acceptor (D-A)-type conjugated polymer has received significant attention for several decades because its electronic characteristics can easily be tuned owing to the unique synergy between its donor and acceptor units. It can also extend its absorption range for wavelengths in the infrared region [8].
Ideally, in order to improve the efficiency of D-A-type conjugated polymers, the following characteristics are required [18]: (1) band gap property to absorb a wide range of wavelengths, (2) well-ordered orientation to exhibit a better charge transport property, (3) a low level of the highest occupied molecular orbital (HOMO) energy to show a high open-circuit voltage (V OC ), and (4) an appropriate level of the lowest unoccupied molecular orbital (LUMO) energy for effective electron charge transfer to acceptor materials.
Better charge transport properties can be achieved by compact packing between the backbones of the polymer. This could lead to a decrease in the amorphous region by increasing the planar networks and efficient π-π stacking.
Fluorene derivatives exhibit good oxidation stability because of its low HOMO energy level [19]. Moreover, introducing two side chains at its 9-position improves the solubility of the fluorene derived conjugated polymers. However, fluorene has two alkyl side chains connected to the C atom with a "sticking-out" configuration. Therefore, it is difficult to form two-dimensional packing, which can lead to the suppression of compact packing and charge-carrier mobility [19,20]. Alkylidene fluorene instead of fluorene was reported by McCulloch et al. Its -lidene functional group is sp 2 -hybridized, which improves compact packing owing to the planar effect of the alkyl side chain.
In this study, we synthesized (D-A)-type polymers based on alkylidene fluorene and quinoxaline derivatives, and investigated their optical, surface, and morphological characteristics. In addition, their efficiency through optimized device environments (temperature, acceptor) was tested. We design a novel molecular structure based on alkylidene fluorene and quinoxaline derivatives due to compact packing property by the planar structure of alkylidene fluorene and efficient intra-molecular charge transfer by quinoxaline derivative.

Instruments and Characterization
All the reactions were performed under a nitrogen atmosphere. Organic solvents were dried by distillation. Column chromatography was conducted using silica gel (230-400 mesh, Merck). 1 H-NMR spectra were measured with a Bruker ARX 400 spectrometer using solutions of CDCl 3 , and recorded in ppm units with tetramethylsilane as the standard. The elemental analyses were performed with an EA1112 using a CE Instrument. The absorption spectra were measured in an organic solvent with a Cintra 10e UV-Vis spectrophotometer. The cyclic voltammetric properties were measured with a DY2311 potentiostat/bipotentiostat (0.1 M acetonitrile solution including tetrabutyl ammonium hexafluorophosphate (Bu 4 NPF 6 ) as the electrolyte) at a regular scan rate of 50 mV/s under a nitrogen condition. Patterned indium tin oxide (ITO), a Pt plate, and silver/silver chloride (Ag in 0.1 M KCl) were used as the working, counter, and reference electrodes, respectively. The HOMO levels of the polymers were determined using the oxidation onset value. Onset potentials are values obtained from the intersection of the two tangents drawn at the rising current and the baseline changing current of the CV curves. TGA measurements were conducted on the PerkinElmer TGA7. The molecular weight of the conjugated polymer was measured using gel permeation chromatography (GPC, Futecs, P-4000). All GPC analyses were made using tetrahydrofuran(THF) as eluant and polystyrene standard as reference. X-ray diffraction (XRD) patterns were obtained using SmartLab 3 kW (40 kV 30 mA, Cu target, wavelength: 1.541871 ang), Rigaku, Japan. The surface morphology of the blend layers was measured through atomic force microscopy (AFM) in the tapping mode using an XE-100 instrument. The photovoltaic performance of the OSCs was characterized under an AM 1.5 G condition of 100 mW/cm 2 simulated sunlight by a solar cell measurement system (Oriel 96,000 150 W and Keithley 2400). The incident photon-to-current conversion efficiency (IPCE, McScience) was evaluated for the optimal device composition.

Fabrication of OSCs
To fabricate the OSC devices, ITO glass substrates were cleaned by sequential ultrasonic cleaning in detergent solution, 2-propanol, and deionized water. After cleaning, any moisture on the surface of the substrates was eliminated by exposure to N 2 flow and a temperature of 120 • C. The dried substrates were transferred to the UV-ozone cleaner for surface treatment to improve interfacial contact. To fabricate inverted OSC devices, the ZnO precursor solution was deposited on top of the ITO surface by spin coating and annealed at 200 • C in the air to form an electron transport layer (~10 nm). The ZnO precursor solution was prepared according to the reported method [21]. The ZnO-coated ITO substrates were then transferred to a glove box filled with N 2 -gas, and a solution for the photoactive layer was deposited onto the ZnO layer by spin coating and annealed at 120 • C, for 10 min. The solutions were prepared by dissolving 10 mg of donor polymer in chlorobenzene Polymers 2020, 12, 2859 4 of 11 with 10 mg of acceptors, respectively. (6,6)-phenyl C 71 butyric acid methyl ester (PC 71 BM), 3,9-bis(2-methylene-(3-(1,1-dicyanomethylene)-indanone))-5,5,11,11-tetrakis(4-hexylphenyl)-dithieno (2,3-d:2 ,3 -d')-s-indaceno(1-b:5,6-b')dithiophene (ITIC), and Y6-BO-4Cl were used as acceptors. Finally, MoO 3 (5 nm) and Ag anodes (100 nm) were sequentially deposited by thermal evaporation in a high-vacuum chamber (<10 −7 Torr). The active area of the fabricated inverted PSC was 4 mm 2 . We fabricated devices with more than 40 ea to confirm reproducibility.

Characterization of the Polymers
The molecular weight and thermal characteristics of PAFDQ are shown in Table 1. When GPC was performed using polystyrene as the standard, the number-average molecular weights (M n ) and polydispersity index (PDI) of PAFDQ were 13,200 kg/mol and 2.74, respectively. The degree of polymerization in PAFDQ was lower than that of the general polymer, which may be due to the rigid alkylidene-fluorene derivative. TGA of PAFDQ showed a 5% weight loss at 385 • C (Table 1 & Figure A1), indicating higher thermal stability compared to the general donor structure, which can be attributed to the rigid alkylidene-fluorene structure. This high thermal stability makes the polymer applicable in various optoelectronic devices that require thermal stability over 300 • C [11]. We investigated the thermal behavior using DSC (see SI), which revealed no distinct thermal transitions in any of the polymers in the temperature range of 40-250 • C ( Figure A2).

Optical and Electrochemical Properties
The UV-visible (UV-vis) spectra of the polymer in solution and thin-film are exhibited in Figure 1. In solution, the maximum absorption peaks of PAFDQ (λ max ) were observed at 256, 284, 362, and 516 nm. The band near the 300-400 nm range occurred due to the π-π* transition, whereas the one at 530-600 nm occurred due to ICT between the donor and acceptor moieties [12]. The maximum absorption spectra of the polymer in the film were red-shifted compared to those in the solution. In the thin film, the maximum absorption peaks of PAFDQ (λ max ) were observed at 259, 286, 365, and 529 nm, caused by their more-planar organizations in the solid-state. The optical band gap of PAFDQ calculated through the UV onset value of the film was 1.95 eV. The PAFDQ showed less red-shift spectrum (529 nm) compared with quinacridone-quinoxaline-based polymer (538 nm), which means the effective intramolecular charge transfer has not occurred well in PAFDQ backbone than quinacridone-quinoxaline backbone [11,14].
Polymers 2020, 12, x FOR PEER REVIEW 5 of 11 VOC owing to low HOMO levels. The LUMO energy level was calculated from the difference between the HOMO energy levels and optical band gap energies, yielding −3.42 eV.  Therefore, if charge separation occurred after receiving light energy, an electron in PAFDQ would exhibit more effective charge transport to PCBM than an electron in PTB7 in the active layer [18].  [21], ITIC [22], and Y6-BO-4Cl [23] were obtained from reported literature).  Figure 2a shows the cyclic voltammograms of PAFDQ, where a distinct oxidation-reduction peak was observed in PAFDQ because it is D-A structured, unlike poly(quinacridone-bithiophene) (PQA2T), which is of the typical p-type structure [16]. The optical and electrochemical properties of the polymers are summarized in   Therefore, if charge separation occurred after receiving light energy, an electron in PAFDQ would exhibit more effective charge transport to PCBM than an electron in PTB7 in the active layer [18].  [21], ITIC [22], and Y6-BO-4Cl [23] were obtained from reported literature).  [21], ITIC [22], and Y6-BO-4Cl [23] were obtained from reported literature).  Figure 2b presents the band diagram of the energy levels obtained through cyclic voltammetry (CV). The LUMO level of PAFDQ (−3.42 eV) was lower than that of PTB7 (−3.31 eV) by 0.11 eV. Therefore, if charge separation occurred after receiving light energy, an electron in PAFDQ would exhibit more effective charge transport to PCBM than an electron in PTB7 in the active layer [18]. Figure 3 presents the XRD measurements to analyze the order of the structure of PAFDQ and various other acceptors. PAFDQ exhibited sharp diffraction peaks at 2.1 and 2.2 • in the out-of-plane peak (100), indicating the formation of an ordered lamellar structure by the alkyl side chain of alkylidene-fluorene and conventional edge-on π-stacking [11,16]. The d π -spacing with only PAFDQ was 4.0-4.2 nm, whereas the (010) diffraction peak corresponding to the π-π stacking rarely appeared. Similarly, sharp diffraction peaks in the out-of-plane peak were observed for the PAFDQ/ PC 71 BM and PAFDQ/ ITIC films. However, the PAFDQ/Y6-BO-4Cl film exhibited a more prominent (010) diffraction peak corresponding to the π-π stacking in the out-of-plane pattern at 23.0-27.0 • . The π-π stacking distance was 3.30-3.86 Å. This suggests that a large fraction of the PAFDQ/Y6-BO-4Cl film was oriented face-on relative to the substrate due to the interaction between the PAFDQ and Y6-BO-4Cl derivatives. The PAFDQ/Y6-BO-4Cl film exhibited the strongest π-π stacking interaction and face-on orientation compared to other films, which is expected because it exhibited the best fill factor (FF) by a low series resistance [11].

Orientation Analysis
Polymers 2020, 12, x FOR PEER REVIEW 6 of 11 Figure 3 presents the XRD measurements to analyze the order of the structure of PAFDQ and various other acceptors. PAFDQ exhibited sharp diffraction peaks at 2.1 and 2.2° in the out-of-plane peak (100), indicating the formation of an ordered lamellar structure by the alkyl side chain of alkylidene-fluorene and conventional edge-on π-stacking [11,16]. The dπ-spacing with only PAFDQ was 4.0-4.2 nm, whereas the (010) diffraction peak corresponding to the π-π stacking rarely appeared. Similarly, sharp diffraction peaks in the out-of-plane peak were observed for the PAFDQ/ PC71BM and PAFDQ/ ITIC films. However, the PAFDQ/Y6-BO-4Cl film exhibited a more prominent (010) diffraction peak corresponding to the π-π stacking in the out-of-plane pattern at 23.0-27.0°. The π-π stacking distance was 3.30-3.86 Å . This suggests that a large fraction of the PAFDQ/Y6-BO-4Cl film was oriented face-on relative to the substrate due to the interaction between the PAFDQ and Y6-BO-4Cl derivatives. The PAFDQ/Y6-BO-4Cl film exhibited the strongest π-π stacking interaction and face-on orientation compared to other films, which is expected because it exhibited the best fill factor (FF) by a low series resistance [11].  Figure 4 and Table 2 show the evaluation results of the OSCs. The active layer had an optimized blending ratio obtained by dissolving the PAFDQ polymer and acceptors (PC71BM, ITIC, or Y6-BO-4Cl) in chlorobenzene using a concentration of approximately 0.5-1 wt%. The spin-cast film was annealed at 120C for 10 min. The device based on the non-fullerene acceptor (NFA) of Y6-BO-4Cl showed the best performance in terms of short circuit current (JSC) = 9.86 mA/cm 2 , VOC = 0.76 V, FF = 44.23%, and PCE = 3.32%. It is noteworthy that the JSC value was twice that of the PCBM-based device.  Figure 4 and Table 2 show the evaluation results of the OSCs. The active layer had an optimized blending ratio obtained by dissolving the PAFDQ polymer and acceptors (PC 71 BM, ITIC, or Y6-BO-4Cl) in chlorobenzene using a concentration of approximately 0.5-1 wt %. The spin-cast film was annealed at 120 • C for 10 min. The device based on the non-fullerene acceptor (NFA) of Y6-BO-4Cl showed the best performance in terms of short circuit current (J SC ) = 9.86 mA/cm 2 , V OC = 0.76 V, FF = 44.23%, and PCE = 3.32%. It is noteworthy that the J SC value was twice that of the PCBM-based device. This can be attributed to the wider absorption wavelength band of Y6-BO-4Cl/NFA. As observed in the IPCE data (Figure 4b), the device with Y6-BO-4Cl NFA exhibited a higher external quantum efficiency (EQE) and wider absorption band than that of the PC 71 BM-based device.

Morphology Analysis
AFM results show large aggregates in the polymer/NFA acceptor films with a smaller rootmean-square roughness (RRMS) ( Figure 5). In the Y6-BO-4Cl based film (Figure 5e,f), the phase separation of donor-rich (bright domains) and acceptor-rich (dark domains) phases, and connected dark domains was observed. However, in the ITIC-blended film (Figure 5c,d), larger domains were observed without their interconnection. The connected domains can form a charge transport channel, which can improve charge extraction and suppress charge recombination. [24,25]. By using ITIC as the acceptor, higher VOC can be achieved because of the smaller HOMO level offset with the donor

Morphology Analysis
AFM results show large aggregates in the polymer/NFA acceptor films with a smaller root-mean-square roughness (R RMS ) ( Figure 5). In the Y6-BO-4Cl based film (Figure 5e,f), the phase separation of donor-rich (bright domains) and acceptor-rich (dark domains) phases, and connected dark domains was observed. However, in the ITIC-blended film (Figure 5c,d), larger domains were observed without their interconnection. The connected domains can form a charge transport channel, which can improve charge extraction and suppress charge recombination. [24,25]. By using ITIC as the acceptor, higher V OC can be achieved because of the smaller HOMO level offset with the donor polymer, when compared to Y6-BO-4Cl [24][25][26]. However, better phase separation occurred in the Y6-BO-4Cl-blended active layer than in the ITIC-blended film, resulting in higher J SC and FF in the Y6-BO-4Cl-based devices.

Conclusions
In this study, an alkylidene-fluorene-quinoxaline-based polymer was successfully synthesized using the Suzuki coupling reaction by introducing a planar alkylidene-fluorene unit and a highly soluble quinoxaline unit. The polymer exhibited high molecular weights and good thermal stability. According to XRD measurements, PAFDQ exhibited a formation of an ordered lamellar structure and conventional edge-on π-stacking. The device based on PAFDQ/Y6-BO-4Cl showed the best performance in terms of JSC = 9.86 mA/cm 2 , VOC = 0.76 V, PCE = 3.32%, and FF = 44.23%, with the FF being higher than that of PAFDQ/ITC (31.56). In addition, the phase separation of donor-rich and acceptor-rich phases, and connected dark domains was observed in the PAFDQ/Y6-BO-4Cl film.

Conclusions
In this study, an alkylidene-fluorene-quinoxaline-based polymer was successfully synthesized using the Suzuki coupling reaction by introducing a planar alkylidene-fluorene unit and a highly soluble quinoxaline unit. The polymer exhibited high molecular weights and good thermal stability. According to XRD measurements, PAFDQ exhibited a formation of an ordered lamellar structure and conventional edge-on π-stacking. The device based on PAFDQ/Y6-BO-4Cl showed the best performance in terms of J SC = 9.86 mA/cm 2