Elevated Photovoltaic Performance in Medium Bandgap Copolymers Composed of Indacenodi-thieno[3,2-b]thiophene and Benzothiadiazole Subunits by Modulating the π-Bridge

Two random conjugated polymers (CPs), namely, PIDTT-TBT and PIDTT-TFBT, in which indacenodithieno[3,2-b]thiophene (IDTT), 3-octylthiophene, and benzothiadiazole (BT) were in turn utilized as electron-donor (D), π-bridge, and electron-acceptor (A) units, were synthesized to comprehensively analyze the impact of reducing thiophene π-bridge and further fluorination on photostability and photovoltaic performance. Meanwhile, the control polymer PIDTT-DTBT with alternating structure was also prepared for comparison. The broadened and enhanced absorption, down-shifted highest occupied molecular orbital energy level (EHOMO), more planar molecular geometry thus enhanced the aggregation in the film state, but insignificant impact on aggregation in solution and photostability were found after both reducing thiophene π-bridge in PIDTT-TBT and further fluorination in PIDTT-TFBT. Consequently, PIDTT-TBT-based device showed 185% increased PCE of 5.84% profited by synergistically elevated VOC, JSC, and FF than those of its counterpart PIDTT-DTBT, and this improvement was chiefly ascribed to the improved absorption, deepened EHOMO, raised μh and more balanced μh/μe, and optimized morphology of photoactive layer. However, the dropped PCE was observed after further fluorination in PIDTT-TFBT, which was mainly restricted by undesired morphology for photoactive layer as a result of strong aggregation even if in the condition of the upshifted VOC. Our preliminary results can demonstrate that modulating the π-bridge in polymer backbone was an effective method with the aim to enhance the performance for solar cell.


Introduction
By virtue of the intriguing features of environmentally friendly, inexhaustibility, and widespread distribution, solar energy as one kind of green renewable energy has yielded more and more attention [1,2]. Among the multitudinous solar energy utilization technologies, bulk-heterojunction (BHJ) polymer solar cells (PSCs) whose photoactive layer consists of p-type π-conjugated polymers

Polymer Synthesis
The resultant copolymers were synthesized as the following procedures: carefully purified bistin IDTTSn and dibromo-monomer (DTBTBr 2 , TBTBr 2 and TFBTBr 2 ) were fully dissolved into 6 mL degassed dry toluene and 0.8 mL DMF in a 25 mL two-neck round-bottom flask under Ar. The mixture was bubbled with Ar for another 20 min to remove O 2 . Thereafter, Pd 2 (dba) 3 (1.4 mg) and P(o-tolyl) 3 (2.3 mg) were quickly added to the mixture in one portion and the solution was bubbled with Ar for additional 20 min. The mixture was then vigorously refluxed for 48 h under Ar, followed by the subsequent addition of 2-tri(butylstannyl)thiophene and 2-bromothiophene at an interval of 8 h in order to finish ending-capping. After additional reflux at 8 h, the mixture was poured into 300 mL MeOH. The precipitate was collected by filtration and the crude polymer was subjected to Soxhlet extraction successively with MeOH, acetone, hexane, and toluene. Finally, the toluene fraction was condensed to approximately 6 mL and precipitated into MeOH. The black solid was collected and completely dried under vacuum overnight to obtain the target material with a yield of 92~98%.

Fabrication and Characterization of PSCs
The fabrication process for the devices used for photovoltaic performance measurement of the resultant copolymers was prepared according to our reported reference [13].

Hole-Only Device Fabrication and Measurement
The hole mobility of the active layer was measured from the J-V curves obtained under dark current described in our reported reference using the steady state space-charge-limited-current (SCLC) method [24,76].

Molecular Design, Synthesis, and Characterization
Key monomer bistin IDTTSn was synthesized according to our reported work [34]. Unsymmetrical dibromide TBTBr 2 and TFBTBr 2 are described in Scheme S1 in Supporting Information. These key intermediates and comonomers have been identified by 1 H NMR, as depicted in Figure S1−S5 (in Supplementary Materials) and elemental analyses. These studied random copolymers PIDTT-TBT and PIDTT-TFBT as well as the control polymer PIDTT-DTBT were prepared via typical Stille polymerization, as elucidated in Scheme 1 [77] and further purified in the light of the reported method [75]. In the end, the fraction dissolved in toluene was recovered by re-precipitating in MeOH and then dried under vacuum overnight so as to remove the residual solvents. Note that all polymers were obtained as black solids exhibiting metallic luster in the high yields of 92~98%. It was found that these prepared copolymers displayed enough solubility in the chlorinated solvents (i.e., chloroform, chlorobenzene (CB), and o-dichlorobenzene (oDCB)), satisfying the requirements of the solution-processed fabrication procedure.
What is exciting is that the 1 H NMR signals placed in the aromatic regions with regard to these resultant copolymers were all clearly observed, as outlined in Figures S6−S8 (in Supplementary Materials). In detail, peaks in the range of 8.67−7.41 ppm were produced by aromatic hydrogen from main chain of IDTT and DTBT, TBT and TFBT, and ones placed at 7.23 ppm and 7.11 ppm can be ascribed to aromatic hydrogen of hexylphenyl group. While, the peaks located at 2.86-2.84 ppm was belonged to the signal of -CH 2 -directly linked to the thiophene bridge and ones placed at 2.58-2.56 ppm were originated from the signal of -CH 2 -directly linked to phenyl group. Furthermore, the peaks ranged from 1.74 to 1.24 ppm were ascribed to the signals of remainder -CH 2 -of flexible side chains, and ones at 0.86 ppm were assigned to the signals of terminal -CH 3 . Besides, the results obtained from elemental analysis were found to be consistent with the theoretical values. Gel permeation chromatography (GPC) measurement exhibited the values for M n and PDIs to be 32.4 kDa and 1.8 for PIDTT-DTBT, 31.2 kDa and 1.9 for PIDTT-TBT, and 34.4 kDa and 2.1 for PIDTT-TFBT, respectively (Table S1 in Supplementary Materials), suggesting that the influence of the molecular weights on the optoelectronic and photovoltaic properties could be neglected. Seen from Figure S9 and Table S1 (in Supplementary Materials), the control polymer PIDTT-DTBT and two random copolymers PIDTT-TBT and PIDTT-TFBT exhibited the decomposed temperature (T d , 5% weight-loss temperature) of approximately 310, 346, and 366 • C, respectively. Obviously, random polymer PIDTT-TBT with asymmetric π-bridge and further fluorinated PIDTT-TFBT exhibited a gradually elevated T d , which was in line with the enhanced molecular planarity and ordering obtained from the latter XRD analyses and DFT calculation. Materials). In detail, peaks in the range of 8.67−7.41 ppm were produced by aromatic hydrogen from main chain of IDTT and DTBT, TBT and TFBT, and ones placed at 7.23 ppm and 7.11 ppm can be ascribed to aromatic hydrogen of hexylphenyl group. While, the peaks located at 2.86-2.84 ppm was belonged to the signal of -CH2directly linked to the thiophene bridge and ones placed at 2.58-2.56 ppm were originated from the signal of -CH2directly linked to phenyl group. Furthermore, the peaks ranged from 1.74 to 1.24 ppm were ascribed to the signals of remainder -CH2of flexible side chains, and ones at 0.86 ppm were assigned to the signals of terminal -CH3. Besides, the results obtained from elemental analysis were found to be consistent with the theoretical values. Gel permeation chromatography (GPC) measurement exhibited the values for Mn and PDIs to be 32.4 kDa and 1.8 for PIDTT-DTBT, 31.2 kDa and 1.9 for PIDTT-TBT, and 34.4 kDa and 2.1 for PIDTT-TFBT, respectively (Table S1 in Supplementary Materials), suggesting that the influence of the molecular weights on the optoelectronic and photovoltaic properties could be neglected. Seen from Figure S9 and Table S1 (in Supplementary Materials), the control polymer PIDTT-DTBT and two random copolymers PIDTT-TBT and PIDTT-TFBT exhibited the decomposed temperature (Td, 5% weight-loss temperature) of approximately 310, 346, and 366 °C, respectively. Obviously, random polymer PIDTT-TBT with asymmetric π-bridge and further fluorinated PIDTT-TFBT exhibited a gradually elevated Td, which was in line with the enhanced molecular planarity and ordering obtained from the latter XRD analyses and DFT calculation. Scheme 1. The synthetic routes of the random copolymers PIDTT-TBT and PIDTT-TFBT and the alternated copolymer PIDTT-DTBT.

Optical Property
In order to investigate the impact of reducing thiophene π-bridge and further fluorination on absorption behavior, the normalized UV-Vis absorption spectra in CB solution with the concentration of approximately 10 −5 mol L −1 and as solid films were examined. As can be seen from Figure 1 and Table 1, the studied copolymers exhibited two legible absorption peaks, i.e., one situated at 350~500 nm were assigned to the π-π* transition from the resultant polymer backbone, the other one located in the range of 500~750 nm were originated from ICT effect from electron-rich IDTT unit to electron-deficient BT/FBT moiety [34,41]. After reducing the conjugated octylthiophene π-bridge and further fluorination, the decreased and blue-shifted variation (from 442 to 431 then to Scheme 1. The synthetic routes of the random copolymers PIDTT-TBT and PIDTT-TFBT and the alternated copolymer PIDTT-DTBT.

Optical Property
In order to investigate the impact of reducing thiophene π-bridge and further fluorination on absorption behavior, the normalized UV-Vis absorption spectra in CB solution with the concentration of approximately 10 −5 mol L −1 and as solid films were examined. As can be seen from Figure 1 and Table 1, the studied copolymers exhibited two legible absorption peaks, i.e., one situated at 350~500 nm were assigned to the π-π* transition from the resultant polymer backbone, the other one located in the range of 500~750 nm were originated from ICT effect from electron-rich IDTT unit to electron-deficient BT/FBT moiety [34,41]. After reducing the conjugated octylthiophene π-bridge and further fluorination, the decreased and blue-shifted variation (from 442 to 431 then to 428 nm in CB and from 445 to 436 then to 432 nm in film) for absorption peak in the high energy region in both CB and solid film was found, while only red-shifted change in the CB but both red-shifted and enhanced alternation for peak in the low energy region were also observed, these phenomena were identical with other groups' results [41,43]. Ongoing from solution to film state, the red-shifted values for the maximum absorption peaks (λ max ) of 6 nm for PIDTT-DTBT, 8 nm for PIDTT-TBT, and 18 nm for PIDTT-TFBT were observed, respectively. In particular, the fluorinated PIDTT-TFBT exhibited a weak Polymers 2020, 12, 368 7 of 22 peak seated at 590 nm, implying an enhanced molecular aggregation and stacking interaction evoked by fluorination [24,25,68]. Importantly, the absorption coefficient in film state was enhanced after reducing thiophene π-bridge and further fluorination. These changes could preliminarily suggest that the studied CPs exhibited the gradually increasing aggregation ability according to the sequence of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT. Furthermore, the optical bandgaps (E opt g ) values of 1.79 eV for PIDTT-DTBT, 1.76 eV for PIDTT-TBT, and 1.77 nm for PIDTT-TFBT in films were estimated with the absorption edge (λ film onset ) in terms of E opt g = 1240/λ film onset , suggesting that the E opt g exhibited first reduced then slightly increased tendency in the order of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT. Evidently, after the thiophene π-bridge was reduced and further fluorinated, the absorption and absorption coefficient were improved, which was conducive to acquiring the higher J SC . 428 nm in CB and from 445 to 436 then to 432 nm in film) for absorption peak in the high energy region in both CB and solid film was found, while only red-shifted change in the CB but both red-shifted and enhanced alternation for peak in the low energy region were also observed, these phenomena were identical with other groups' results [41,43]. Ongoing from solution to film state, the red-shifted values for the maximum absorption peaks (λmax) of 6 nm for PIDTT-DTBT, 8 nm for PIDTT-TBT, and 18 nm for PIDTT-TFBT were observed, respectively. In particular, the fluorinated PIDTT-TFBT exhibited a weak peak seated at 590 nm, implying an enhanced molecular aggregation and stacking interaction evoked by fluorination [24,25,68]. Importantly, the absorption coefficient in film state was enhanced after reducing thiophene π-bridge and further fluorination. These changes could preliminarily suggest that the studied CPs exhibited the gradually increasing aggregation ability according to the sequence of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT. Furthermore, the optical bandgaps ( ) values of 1.79 eV for PIDTT-DTBT, 1.76 eV for PIDTT-TBT, and 1.77 nm for PIDTT-TFBT in films were estimated with the absorption edge ( ) in terms of = 1240/ , suggesting that the exhibited first reduced then slightly increased tendency in the order of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT. Evidently, after the thiophene π-bridge was reduced and further fluorinated, the absorption and absorption coefficient were improved, which was conducive to acquiring the higher JSC.  was calculated from oxidation potential of the copolymers (EHOMO = -e( + 4.69) (eV)); 3 ELUMO was calculated from reduction potential of the copolymers (ELUMO = -e( + 4.69) (eV)); 4 = ELUMO − EHOMO (eV).
To examine the difference of reducing π-bridge and further fluorination on aggregation in solution, the temperature-dependent absorption (TD-Abs) spectra of the resultant copolymers in CB solution (ca. 10 −5 mol L −1 ) ranging from 105 to 25 °C with a 10 °C interval was tested [24,78]. As elucidated in Figure 2, the studied copolymers exhibited the similar variation tendency, that is, the ICT and π-π* absorption peak were all blue-shifted and the absorption intensity decreased with the elevating temperature. In detail, after temperature was risen from 25 to 105 °C, the blue-shifted   1 Optical bandgap was calculated from the onset of the film absorption (E opt g = 1240/λ film onset ); 2 E HOMO was calculated from oxidation potential of the copolymers (E HOMO = -e(ϕ onset ox + 4.69) (eV)); 3 E LUMO was calculated from reduction potential of the copolymers (E LUMO = -e(ϕ onset red + 4.69) (eV)); 4 To examine the difference of reducing π-bridge and further fluorination on aggregation in solution, the temperature-dependent absorption (TD-Abs) spectra of the resultant copolymers in CB solution (ca. 10 −5 mol L −1 ) ranging from 105 to 25 • C with a 10 • C interval was tested [24,78]. As elucidated in Figure 2, the studied copolymers exhibited the similar variation tendency, that is, the ICT and π-π* absorption peak were all blue-shifted and the absorption intensity decreased with the elevating temperature. In detail, after temperature was risen from 25 to 105 • C, the blue-shifted values (∆λ) and the decreased absorption intensity (∆I) were 14 nm (from 570 to 556 nm) and 15.1% for PIDTT-DTBT, 13 nm (from 602 to 589 nm) and 12.1% for PIDTT-TBT and 16 nm (from 602 to 586 nm) and 14.4% for PIDTT-TFBT, respectively. The observed similar vibration values with respect to absorption peak and intensity implied that the strategies of reducing π-bridge and fluorination produced the little impact on aggregation in CB solution [79]. values (Δλ) and the decreased absorption intensity (ΔI) were 14 nm (from 570 to 556 nm) and 15.1% for PIDTT-DTBT, 13 nm (from 602 to 589 nm) and 12.1% for PIDTT-TBT and 16 nm (from 602 to 586 nm) and 14.4% for PIDTT-TFBT, respectively. The observed similar vibration values with respect to absorption peak and intensity implied that the strategies of reducing π-bridge and fluorination produced the little impact on aggregation in CB solution [79].

Photostability Property
Aimed at achieving the industrialization of PSCs, in addition to the ability of harvesting sunlight, the photo-stability of organic semiconductor materials was also an important issue [18,34,80,81]. Consequently, in order to inspect the effect of reducing conjugated thiophene π-bridge and further fluorination on the photo-stabilities, the absorption variations of the resultant CPs were examined by exposing the diluted CB solution and the polymers' films under AM1.5 sunlight irradiation in air at room temperature. As exhibited in Figure S10 (in Supplementary Materials), we can see that after 4 h of photodegradation in CB solution, PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT exhibited the almost unchanged absorption, that is to say, higher than 98% of their initial light absorption was maintained. As for the solid film, the UV-vis spectra changes of these copolymers are outlined in Figure 3. The peak related to π-π* transition almost remained unchanged and one assigned to ICT transition exhibited gradual descending with the time of light-soaking. In detail, 92.7%, 91.1%, and 93.9% of their initial light absorption for PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT after 9 h of illumination were seen, which was obviously superior to that of PIDTT-DTNT-based copolymers [34]. Based on the above fact, it was concluded that the strategies of reducing thiophene π-bridge and further fluorination produced very tiny impact on the photostability in both CB and solid film.

X-ray Diffraction (XRD) Analysis
X-ray diffraction (XRD) analyses of the pristine polymers were applied to further probe into the influence of reducing π-bridge and further fluorination on crystallinity and molecular packing in solid film state, as disclosed in Figure 4. It was noted that the used films were casted from CB solution onto the glass substrate. There was only one weak diffraction peak at approximately 20.45° in the reference polymer PIDTT-DTBT, which was attributed to π-π stacking distance of 4.34 Å calculated from the Bragg's law (i.e., λ = 2dsinθ) [34]. For PIDTT-TBT and PIDTT-TFBT, there existed two distinct diffractions. The sharp diffraction peaks in a small angle region are located at 2θ of 4.13° for PIDTT-TBT and 4.32° for PIDTT-TFBT, corresponding to the distance of polymer backbone separated by the flexible side were 21.37 and 21.01 Å, respectively. While the broad diffraction peaks placed at wide angle district located at 2θ of 20.55° for PIDTT-TBT and 21.98° for PIDTT-TFBT could be attributed to π-π stacking interaction, which reflected the corresponding ππ stacking distances of 4.32 and 4.04 Å, respectively. It is inescapably clear that the aggregation trend in the film state was enhanced when the thiophene π-bridge was reduced and further fluorinated, which agreed with the previous phenomenon from absorption.

Photostability Property
Aimed at achieving the industrialization of PSCs, in addition to the ability of harvesting sunlight, the photo-stability of organic semiconductor materials was also an important issue [18,34,80,81]. Consequently, in order to inspect the effect of reducing conjugated thiophene π-bridge and further fluorination on the photo-stabilities, the absorption variations of the resultant CPs were examined by exposing the diluted CB solution and the polymers' films under AM1.5 sunlight irradiation in air at room temperature. As exhibited in Figure S10 (in Supplementary Materials), we can see that after 4 h of photodegradation in CB solution, PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT exhibited the almost unchanged absorption, that is to say, higher than 98% of their initial light absorption was maintained. As for the solid film, the UV-vis spectra changes of these copolymers are outlined in Figure 3. The peak related to π-π* transition almost remained unchanged and one assigned to ICT transition exhibited gradual descending with the time of light-soaking. In detail, 92.7%, 91.1%, and 93.9% of their initial light absorption for PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT after 9 h of illumination were seen, which was obviously superior to that of PIDTT-DTNT-based copolymers [34]. Based on the above fact, it was concluded that the strategies of reducing thiophene π-bridge and further fluorination produced very tiny impact on the photostability in both CB and solid film.

X-ray Diffraction (XRD) Analysis
X-ray diffraction (XRD) analyses of the pristine polymers were applied to further probe into the influence of reducing π-bridge and further fluorination on crystallinity and molecular packing in solid film state, as disclosed in Figure 4. It was noted that the used films were casted from CB solution onto the glass substrate. There was only one weak diffraction peak at approximately 20.45 • in the reference polymer PIDTT-DTBT, which was attributed to π-π stacking distance of 4.34 Å calculated from the Bragg's law (i.e., λ = 2dsinθ) [34]. For PIDTT-TBT and PIDTT-TFBT, there existed two distinct diffractions. The sharp diffraction peaks in a small angle region are located at 2θ of 4.13 • for PIDTT-TBT and 4.32 • for PIDTT-TFBT, corresponding to the distance of polymer backbone separated by the flexible side were 21.37 and 21.01 Å, respectively. While the broad diffraction peaks placed at wide angle district located at 2θ of 20.55 • for PIDTT-TBT and 21.98 • for PIDTT-TFBT could be attributed to π-π stacking interaction, which reflected the corresponding π-π stacking distances of 4.32 and 4.04 Å, respectively. It is inescapably clear that the aggregation trend in the film state was enhanced when the thiophene π-bridge was reduced and further fluorinated, which agreed with the previous phenomenon from absorption.

Electrochemical Property
Since the EHOMO and ELUOMO values for photovoltaic materials were regarded as important parameters for estimating the photovoltaic performance, cyclic voltammetry (CV) method was utilized to gain insight into the impact of reducing the thiophene π-bridge and further fluorination

Electrochemical Property
Since the EHOMO and ELUOMO values for photovoltaic materials were regarded as important parameters for estimating the photovoltaic performance, cyclic voltammetry (CV) method was utilized to gain insight into the impact of reducing the thiophene π-bridge and further fluorination

Electrochemical Property
Since the E HOMO and E LUOMO values for photovoltaic materials were regarded as important parameters for estimating the photovoltaic performance, cyclic voltammetry (CV) method was utilized to gain insight into the impact of reducing the thiophene π-bridge and further fluorination on the electrochemical properties. It was noted that the E HOMO and E LUMO were calculated from its oxidation onset potential (ϕ onset ox ) and reduction onset potential (ϕ onset red ), respectively. As displayed in Figure 5a and Table 1, the corresponding ϕ onset ox and ϕ onset red values of 0.59 and -1.22 V for PIDTT-DTBT, 0.66 and -1.11 V for PIDTT-TFBT, and 0.73 and -1.04 V for PIDTT-TFBT were observed, respectively. It was needed to point out that the CV curve was recorded relative to the potential of the standard Ag/AgNO 3 electrode, calibrated by the ferrocene-ferrocenium (Fc/Fc + ) redox pair. The ϕ 1/2 of the Fc/Fc + redox pair was 0.11 V vs. Ag/AgNO 3 electrode. Supposing that the redox potential for Fc/Fc + was −4.80 eV in relative to vacuum energy level, the E HOMO can be estimated from the formula E HOMO = -e(ϕ onset ox + 4.69) (eV) and E LUMO = -e(ϕ onset red + 4.69) (eV), respectively [82]. Consequently, the E HOMO and E LUMO values were estimated to be -5.28 and -3.47 eV for PIDTT-DTBT, -5.35 and -3.58 eV for PIDTT-TBT, and -5.43 and -3.65 eV for PIDTT-TFBT, respectively. Moreover, the electrochemical bandgap (E ec g ) values for PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT were calculated to be 1.81, 1.77, and 1.77 eV, respectively. In order to make a better comparison, the schematic diagram with respect to the energy levels for the resulted copolymers and electron-acceptor PC 71 BM is depicted in Figure 5b. It was seen that the decreasing E HOMO values ca. 0.07 and 0.15 eV were observed after reducing the thiophene π-bridge and further fluorination, respectively. This change trend was instrumental in yielding the higher V OC , since the V OC was maximized with the enlarging difference between the E HOMO of donor and E LUMO of the acceptor [3,83]. Simultaneously, the differences between E LUMO of donor polymers and one of E LUMO of PC 71 BM ranged from 0.55 to 0.73 eV, which could support enough driving force to promote the exciton to dissociate into free charge at the D-A interfaces [3]. Theoretically, these decreased E HOMO levels and the lowered bandgaps were hopeful for improving the V OC and J SC , and thus resulting in the enhanced PCE.
Polymers 2020, 12, x FOR PEER REVIEW 10 of 21 on the electrochemical properties. It was noted that the EHOMO and ELUMO were calculated from its oxidation onset potential ( ) and reduction onset potential ( ), respectively. As displayed in Figure 5a and Table 1, the corresponding and values of 0.59 and -1.22 V for PIDTT-DTBT, 0.66 and -1.11 V for PIDTT-TFBT, and 0.73 and -1.04 V for PIDTT-TFBT were observed, respectively. It was needed to point out that the CV curve was recorded relative to the potential of the standard Ag/AgNO3 electrode, calibrated by the ferrocene-ferrocenium (Fc/Fc + ) redox pair. The φ1/2 of the Fc/Fc + redox pair was 0.11 V vs. Ag/AgNO3 electrode. Supposing that the redox potential for Fc/Fc + was −4.80 eV in relative to vacuum energy level, the EHOMO can be estimated from the formula EHOMO = -e( + 4.69) (eV) and ELUMO = -e( + 4.69) (eV), respectively [82]. Consequently, the EHOMO and ELUMO values were estimated to be -5.28 and -3.47 eV for PIDTT-DTBT, -5.35 and -3.58 eV for PIDTT-TBT, and -5.43 and -3.65 eV for PIDTT-TFBT, respectively. Moreover, the electrochemical bandgap ( ) values for PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT were calculated to be 1.81, 1.77, and 1.77 eV, respectively. In order to make a better comparison, the schematic diagram with respect to the energy levels for the resulted copolymers and electron-acceptor PC71BM is depicted in Figure 5b. It was seen that the decreasing EHOMO values ca. 0.07 and 0.15 eV were observed after reducing the thiophene π-bridge and further fluorination, respectively. This change trend was instrumental in yielding the higher VOC, since the VOC was maximized with the enlarging difference between the EHOMO of donor and ELUMO of the acceptor [3,83]. Simultaneously, the differences between ELUMO of donor polymers and one of ELUMO of PC71BM ranged from 0.55 to 0.73 eV, which could support enough driving force to promote the exciton to dissociate into free charge at the D-A interfaces [3]. Theoretically, these decreased EHOMO levels and the lowered bandgaps were hopeful for improving the VOC and JSC, and thus resulting in the enhanced PCE.

Theoretical Calculation
The density functional theory (DFT) calculation situated at B3LYP/6-31G* basis set (Gaussian 09) was selected to further probe into the effect of reducing thiophene π-bridge and further fluorination on the molecular backbone conformation and the electron density distributions [84]. For simplification, the hexyl side chain from IDTT and octyl side chain attached onto the thiophene bridge were both replaced with the methyl, and oligomers involving one repeating unit (unimer) were used to take the place of the corresponding polymer backbones. Note that the unimer model for the studied random copolymers PIDTT-TBT and further fluorinated PIDTT-TFBT had two different linking patterns, (IDTT-BT-T) and/or (IDTT-T-BT), and (IDTT-FBT-T) and/or (IDTT-T-FBT), respectively. As presented in Figure 6, the HOMO orbitals of all studied compounds are primarily delocalized across the whole conjugated main chain, in contrast, the LUMO orbitals are

Theoretical Calculation
The density functional theory (DFT) calculation situated at B3LYP/6-31G* basis set (Gaussian 09) was selected to further probe into the effect of reducing thiophene π-bridge and further fluorination on the molecular backbone conformation and the electron density distributions [84]. For simplification, the hexyl side chain from IDTT and octyl side chain attached onto the thiophene bridge were both replaced with the methyl, and oligomers involving one repeating unit (unimer) were used to take the place of the corresponding polymer backbones. Note that the unimer model for the studied random copolymers PIDTT-TBT and further fluorinated PIDTT-TFBT had two different linking patterns, (IDTT-BT-T) and/or (IDTT-T-BT), and (IDTT-FBT-T) and/or (IDTT-T-FBT), respectively. As presented in Figure 6, the HOMO orbitals of all studied compounds are primarily delocalized across the whole conjugated main chain, in contrast, the LUMO orbitals are preferentially distributed in electron-deficient BT and/or FBT and lateral thiophene bridges, indicating that there existed the relatively obvious charge-transfer effect from IDTT to BT and/or FBT units. It was seen that the theoretically forecasted values for E HOMO , E LUMO , and bandgap were −4.94, −2.80, and 2.14 eV of PIDTT-DTBT, −4.97, −2.79, and 2.18 eV of IDTT-BT-T, and −4.99, −2.69, and 2.30 eV of IDTT-BT-T for thiophene-bridge-reducing PIDTT-TBT, −5.04, −2.90, and 2.14 eV for PIDTT-FBT-T and −5.02, −2.86, and 2.16 eV of IDTT-T-FBT for further fluorinated PIDTT-TFBT, respectively. We can see that, regardless of the position of thiophene π-bridge, the descending trend of E HOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing. We can see that, regardless of the position of thiophene π-bridge, the descending trend of EHOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing.    We can see that, regardless of the position of thiophene π-bridge, the descending trend of EHOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing.  We can see that, regardless of the position of thiophene π-bridge, the descending trend of EHOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing.  We can see that, regardless of the position of thiophene π-bridge, the descending trend of EHOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing.  We can see that, regardless of the position of thiophene π-bridge, the descending trend of EHOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing.  We can see that, regardless of the position of thiophene π-bridge, the descending trend of EHOMO from PIDTT-DTBT to PIDTT-TBT then to PIDTT-TFBT was observed, which was in accordance with the results obtained from CV testing.  Since the good planarity in polymer backbone is helpful to promote closer π−π stacking, higher charge transfer, and enlarged molecular conjugation so as to generate the lower band gap for harvesting more sunlight [24,75]. Thus, we further inspected the dihedral angles θ 1 between IDTT unit and alkylthiophene bridge, θ 2 and θ 3 between alkylthiophene bridge and BT and/or moiety. According to the data of Table 2, in spite of position of the thiophene π-bridge in the polymer backbone, the backbone planarity was all improved, meanwhile, the fluorination further optimized the backbone planarity. Definitely, these variations concerning energy level and molecular planarity can well agree with the results measured in former CV and XRD analyses.

Photovoltaic Properties
In order to probe into the impact of reducing thiophene π-bridge and further fluorination in IDTT-based polymer backbone on the photovoltaic properties, the devices with the configuration of ITO/PEDOT:PSS/polymers:PCBM/PDINO/Al were fabricated. Note that the photoactive layers were prepared by spin-coating the solution involving the studied copolymers and PC 61 BM and/or PC 71 BM, and the ultrathin interfacial layer (spinning from 1 mg L −1 PDINO solution in methanol) was utilized as cathode-modified interlayer [13]. The photovoltaic performance was optimized by the following processing, screening out the D/A ratio, utilizing the 1,8-diiodioctane (DIO) processing additive and substituting PC 61 BM with PC 71 BM. These device fabrication processes are listed in Supporting Information (Figures S11 and S12 and Table S2 in Supplementary Materials) in detail. After screening the D/A ratios, 1:1, 1:2 to 1:3, it was exhibited that the optimal D/A ratio for PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT was 1:2, as shown in Figure S11. Seen from Table S2, Figure S11.
Since processing solvent additive with high boiling point was conducive to forming more ordered and nano-scaled bicontinuous interpenetration network structure which can improve the dissociation of light-induced exciton into the free charge carriers at the D/A interface and accelerate the transport of free charge carriers [85,86]. Hence, following that, we selected the 3% DIO (DIO/CB, V/V) as a solvent additive to proceed to optimize the device performance, as illustrated in Figure S12 (in Supplementary Materials). Unfortunately, a 14.6% deterioration of PCE (from 2.05 to 1.75%) in the control polymer PIDTT-DTBT-based device was found, mainly originating from the 18.2% decline in FF (from 45.67 to 437.37%) the even though the slight increases of V OC (from 0.81 to 0.84 V) and J SC (from 5.51 to 5.57 mA cm −2 ). As for PIDTT-TBT-based devices, it was exhibited that the 10.3% elevation in PCE (from 4.48 to 4.94%) was observed, chiefly benefiting from the 7.8% enhancement in FF (from 49.30 to 53.14 %) even if V OC and J SC kept relatively constant. A 12.3% increase in PCE (from 2.60 to 2.92%) was inspected in the further fluorination of PIDTT-TFBT-based device, primarily benefiting from slightly enhancements of 5.9% in J SC (from 5.63 to 5.95 mA cm −2 ) and 5.0% in FF (49.08 to 51.54%) under the condition of the almost unchanged V OC . Apparently, positive effect in PIDTT-TBT and fluorinated PIDTT-TFBT but negative impact in the reference material PIDTT-DTBT on the photovoltaic performance were observed.
On account of PC 71 BM possessing relatively higher absorption coefficient and broader absorption band than those of PC 61 BM, herein PC 71 BM was applied to replace PC 61 BM for further enhancing the PCE [87], as displayed in Figure S12. As shown in Table S2, the enhancement of 10.9% (from 1.75 to 1.84%) for PCE in PIDTT-DTBT-based device was achieved, primarily originating from 10.1% increase in FF (from 37.37 to 41.15%). Inspiringly, the remarkable 18.2% improvement of PCE for PIDTT-TBT was obtained, mainly benefiting from concurrently upshifted by 5.1% J SC (from 10.54 to 11.08 mA cm −2 ) and 12.2% FF (from 53.14 to 559.60%) but the stable V OC . However, as for the fluorinated PIDTT-TFBT-based device, a 8.6% decline in PCE (from 2.92 to 2.67%) was obtained, mostly limited by 8.6% drop in J SC (from 5.95 to 5.44 mA cm −2 ) but constant V OC and almost unvaried FF. It was noted that these relevant J SC variations were also confirmed by corresponding EQE curves in Figure S12.
With the assistance of D/A ratio screening, DIO additive and utilizing PC 71 BM to replace PC 61 BM, the optimal J-V characteristics and corresponding EQE spectra were elucidated in Figure 7. Seen from Table 3, for as much as the moderate electron-donating IDTT and strong electron-withdrawing BT subunits was selected to construct the polymer backbone, these yielded photovoltaic devices exhibited relatively higher V OC ranging from 0.81 to 0.95 V. Meanwhile, the gradual increasing tendency of V OC (from 0.81 to 0.88 then to 0.95 V) in the order of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT was in accordance with the above deepened E HOMO predicted by DFT and CV tests [24]. We can see that the best PCE was remarkably increased from 2.05 to 5.84% after reducing the thiophene π-bridge, chiefly benefiting from collaborative 8.6% increase in V OC (from 0.81 to 0.88 V), 101% enhancement in J SC (from 5.51 to 11.08 mA cm −2 ), and 30.5% elevation in FF (from 45.67 to 59.60%). Conversely, 50% downshifted PCE (from 5.84 to 2.92%) was found after further fluorination, which was mainly limited by 46.4% decrease in J SC (from 11.08 to 5.95 mA cm −2 ) and 13.52% drop in FF (from 59.60 to 51.54%) even if the V OC increased by 18% (from 0.88 to 0.95 V). Theses J SC variations were also verified by the corresponding EQE spectra (Figure 7b). Another point that needs to be emphasized is that the integrated J SC values in terms of EQE curves were estimated to be 5.45, 11.00, and 5.80 mA cm −2 for the optimal PIDTT-DTBT:PC 61 BM, PIDTT-TBT:PC 71 BM, and PIDTT-TFBT:PC 61 BM, respectively, indicating there existed the tolerated error (<5%) with respect to J SC values measured from J-V curves, demonstrating these J SC values were reliable. Furthermore, the first enhanced then decreased change trend for FF was also confirmed by the first increased then decreased shunt resistance (R SH ) (from 565 to 604 then to 536 Ω m 2 ) and first decreased then increased series resistance (R S ) (from 43.4 to 7.7 then to 14.9 Ω m 2 ) when reducing the thiophene π-bridge and the further fluorination.
Polymers 2020, 12, x FOR PEER REVIEW 13 of 21 mostly limited by 8.6% drop in JSC (from 5.95 to 5.44 mA cm −2 ) but constant VOC and almost unvaried FF. It was noted that these relevant JSC variations were also confirmed by corresponding EQE curves in Figure S12.
With the assistance of D/A ratio screening, DIO additive and utilizing PC71BM to replace PC61BM, the optimal J-V characteristics and corresponding EQE spectra were elucidated in Figure 7. Seen from Table 3, for as much as the moderate electron-donating IDTT and strong electron-withdrawing BT subunits was selected to construct the polymer backbone, these yielded photovoltaic devices exhibited relatively higher VOC ranging from 0.81 to 0.95 V. Meanwhile, the gradual increasing tendency of VOC (from 0.81 to 0.88 then to 0.95 V) in the order of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT was in accordance with the above deepened EHOMO predicted by DFT and CV tests [24]. We can see that the best PCE was remarkably increased from 2.05 to 5.84% after reducing the thiophene π-bridge, chiefly benefiting from collaborative 8.6% increase in VOC (from 0.81 to 0.88 V), 101% enhancement in JSC (from 5.51 to 11.08 mA cm −2 ), and 30.5% elevation in FF (from 45.67 to 59.60%). Conversely, 50% downshifted PCE (from 5.84 to 2.92%) was found after further fluorination, which was mainly limited by 46.4% decrease in JSC (from 11.08 to 5.95 mA cm −2 ) and 13.52% drop in FF (from 59.60 to 51.54%) even if the VOC increased by 18% (from 0.88 to 0.95 V). Theses JSC variations were also verified by the corresponding EQE spectra (Figure 7b). Another point that needs to be emphasized is that the integrated JSC values in terms of EQE curves were estimated to be 5.45, 11.00, and 5.80 mA cm −2 for the optimal PIDTT-DTBT:PC61BM, PIDTT-TBT:PC71BM, and PIDTT-TFBT:PC61BM, respectively, indicating there existed the tolerated error (<5%) with respect to JSC values measured from J-V curves, demonstrating these JSC values were reliable. Furthermore, the first enhanced then decreased change trend for FF was also confirmed by the first increased then decreased shunt resistance (RSH) (from 565 to 604 then to 536 Ω m 2 ) and first decreased then increased series resistance (RS) (from 43.4 to 7.7 then to 14.9 Ω m 2 ) when reducing the thiophene π-bridge and the further fluorination.    a The values in the parentheses are the integrated currents obtained from the EQE curves; b Shunt resistance (R SH ) and series resistance (R S ) are deduced from the inverse slope at V = 0 and V = V OC in the J−V curves under illumination.

Charge Mobilities
In order to find the reason why reducing thiophene π-bridge and further fluorination in IDTT-based polymer backbone produced different impact on device performance, the vertical hole and electron transport properties were examined by hole-only and electron-only devices with the corresponding device configurations of ITO/PEDOT:PSS/blend/MoO 3 /Ag and ITO/ZnO/blend/MoO 3 /Al, respectively. The prepared photoactive layer films were fabricated under the same conditions with their best PSCs. These charge mobilities were calculated according to SCLC method which can be described by the equation [76]. Note that these thickness values of resultant photoactive layer blend films for PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT were 98, 100, and 105 nm for hole-only devices and 115, 118, and 100 nm for electron-only devices (Tables S3 and S4 in Supplementary Materials), respectively. The J-V curves under dark are presented in Figure S13 (in Supplementary Materials) and the corresponding fitting J 1/2 −V curves for the photoactive layer films are shown in Figure 8.  (Table 4), respectively. Apparently, the hole-mobility showed a first increased then decreased trend, and the electron-mobility exhibited a gradually increased tendency as well as µ h /µ e exhibited a decreased tendency after reducing the thiophene π-bridge in PIDTT-TBT and further fluorinating in PIDTT-TFBT compared to PIDTT-DTBT. These observed increased µ h , µ e and more balanced µ h /µ e values can in part account for the 30.5% increased FF and 101% elevated J SC after reducing the thiophene π-bridge in PIDTT-TBT [88]. Moreover, the decreased µ h after further fluorination in PIDTT-TFBT can explain the reason to some extent why the 13.52% deteriorated FF and 46.39% decreased J SC were observed, which could be further supported by the latter oversized aggregation seen from AFM and TEM analyses.

Charge Mobilities
In order to find the reason why reducing thiophene π-bridge and further fluorination in IDTT-based polymer backbone produced different impact on device performance, the vertical hole and electron transport properties were examined by hole-only and electron-only devices with the corresponding device configurations of ITO/PEDOT:PSS/blend/MoO3/Ag and ITO/ZnO/blend/ MoO3/Al, respectively. The prepared photoactive layer films were fabricated under the same conditions with their best PSCs. These charge mobilities were calculated according to SCLC method which can be described by the equation [76]. Note that these thickness values of  (Table 4), respectively. Apparently, the hole-mobility showed a first increased then decreased trend, and the electron-mobility exhibited a gradually increased tendency as well as μh/μe exhibited a decreased tendency after reducing the thiophene π-bridge in PIDTT-TBT and further fluorinating in PIDTT-TFBT compared to PIDTT-DTBT. These observed increased μh, μe and more balanced μh/μe values can in part account for the 30.5% increased FF and 101% elevated JSC after reducing the thiophene π-bridge in PIDTT-TBT [88]. Moreover, the decreased μh after further fluorination in PIDTT-TFBT can explain the reason to some extent why the 13.52% deteriorated FF and 46.39% decreased JSC were observed, which could be further supported by the latter oversized aggregation seen from AFM and TEM analyses.

Film Morphology
It is known to all that photovoltaic performance are strongly depended on the morphology of the photoactive layer in BHJ PSCs [21,86,[89][90][91]. Consequently, in order to deeply make a thorough inquiry into the causes why reducing the thiophene π-bridge in PIDTT-TBT had a positive impact on PCE but the further fluorination had a negative effect on PCE in PIDTT-TFBT, the morphologies of the photoactive layer films prepared under exactly similar condition with those of optimal device were examined by AFM in a surface area of 5 × 5 µm. As seen from Figure 9, it was exhibited that the both PIDTT-DTBT and PIDTT-TBT-based blend films had very similar surface morphology with the nearest root-mean-square (RMS) roughness of 0.759 and 0.587 nm, respectively, and the fluorinated PIDTT-TFBT-based film displayed greatly increased RMS value of 2.071 nm; these vibrations as a whole were in accordance with the solid aggregation trend observed in the preceding XRD analysis. Furthermore, we utilized the TEM to further examine the in-depth morphology information of the photoactive layers, as depicted in Figure 10. We can see that when reducing thiophene π-bridge in PIDTT-TBT exhibited the slightly optimized phase separation compared with the control polymer PIDTT-DTBT, in the meantime, further fluorination in PIDTT-TFBT exhibited oversized aggregation restricting the effective exciton diffusion and decreasing the exciton dissociation into the free charges via reducing D/A interfacial areas as well as enhancing the charge recombination, which would lead to a detrimental FF and J SC [21]. These morphology information can in part account for the improved photovoltaic performance in PIDTT-TBT-based device but deteriorated performance after further fluorination in PIDTT-TFBT were acquired.

Film Morphology
It is known to all that photovoltaic performance are strongly depended on the morphology of the photoactive layer in BHJ PSCs [21,86,[89][90][91]. Consequently, in order to deeply make a thorough inquiry into the causes why reducing the thiophene π-bridge in PIDTT-TBT had a positive impact on PCE but the further fluorination had a negative effect on PCE in PIDTT-TFBT, the morphologies of the photoactive layer films prepared under exactly similar condition with those of optimal device were examined by AFM in a surface area of 5 × 5 μm. As seen from Figure 9, it was exhibited that the both PIDTT-DTBT and PIDTT-TBT-based blend films had very similar surface morphology with the nearest root-mean-square (RMS) roughness of 0.759 and 0.587 nm, respectively, and the fluorinated PIDTT-TFBT-based film displayed greatly increased RMS value of 2.071 nm; these vibrations as a whole were in accordance with the solid aggregation trend observed in the preceding XRD analysis. Furthermore, we utilized the TEM to further examine the in-depth morphology information of the photoactive layers, as depicted in Figure 10. We can see that when reducing thiophene π-bridge in PIDTT-TBT exhibited the slightly optimized phase separation compared with the control polymer PIDTT-DTBT, in the meantime, further fluorination in PIDTT-TFBT exhibited oversized aggregation restricting the effective exciton diffusion and decreasing the exciton dissociation into the free charges via reducing D/A interfacial areas as well as enhancing the charge recombination, which would lead to a detrimental FF and JSC [21]. These morphology information can in part account for the improved photovoltaic performance in PIDTT-TBT-based device but deteriorated performance after further fluorination in PIDTT-TFBT were acquired.

Conclusions
To conclude, two IDTT-based random CPs, PIDTT-TBT and PIDTT-TFBT as well as the alternating copolymer PIDTT-DTBT as control material, were designed to study the influence of reducing thiophene π-bridge and further fluorination on photostability and photovoltaic performance. Because of selecting the moderate electron-donating IDTT and strong electron-withdrawing BT to construct the polymer backbone, the wide bandgap of 1.76~1.79 eV, lowlying EHOMO ranging from −5.28 to −5.43 eV and excellent photostability were achieved. It was exhibited that the broadened and increased absorption, deepened EHOMO, improved molecular planarity, and thus enhanced film aggregation, but tiny impact on aggregation in CB solution and photostability were observed when PIDTT-DTBT was replaced with PIDTT-TBT and PIDTT-TFBT successively. The best photovoltaic tests disclosed that, PIDTT-TBT-based device yielded 185% increased PCE from 2.05 to 5.84% benefiting from simultaneously elevated VOC of 0.88 V, JSC of 11.08 mA cm −2 , and FF of 59.60% compared to the counterpart, and this improvement was chiefly profited by the broadened and increased absorption, deepened EHOMO, raised μh, and more balanced μh/μe, and slightly optimized morphology of photoactive layer. Conversely, the 50% reduced PCE was observed after further fluorination limited by the minimized JSC and FF, mainly limited by undesired morphology for photoactive layer film as a result of strong aggregation despite of the enlarged VOC. This work suggested tuning the π-bridge in polymer backbone was an easy-to-implement and effectual tactic with a view to enhancing the photovoltaic property.
Supplementary Materials: Detailed experimental procedures and additional characterization data are available online at www.mdpi.com/xxx/s1. Scheme S1: Synthesis of dibromide DTBTBr2, TBTBr2, and TFBTBr2. Figure S1: 1 H NMR spectrum of DTBTBr2 in CDCl3. Figure S2: 1 H NMR spectrum of TBTBr in CDCl3. Figure S3: 1 H NMR spectrum of TBTBr2 in CDCl3. Figure S4: 1 H NMR spectrum of TFBTBr in CDCl3. Figure S5: 1 H NMR spectrum of TFBTBr2 in CDCl3. Figure S6: 1 H NMR spectrum of PIDTT-DTBT in CDCl3. Figure S7: 1 H NMR spectrum of PIDTT-TBT in CDCl3. Figure S8: 1 H NMR spectrum of PIDTT-TFBT in CDCl3. Figure S9: TGA curves of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT. Figure S10: UV-vis absorption spectra changes after illumination of PIDTT-DTBT (a), PIDTT-TBT (b), and PIDTT-TFBT (c) in CB solution and a summary of light absorption intensity changes at the peak of each polymer as a function of light-soaking time (d). Figure S11: The J-V curves of the studied copolymers with different weight ratio to PC61BM and EQE spectra of corresponding PSCs. Figure S12: The J-V curves of polymers without and with 3%DIO, PC61BM replacing with PC71BM and EQE spectra of corresponding PSCs. Figure S13: J-V curves of hole-only (a) and electron-only (b) devices for the studied copolymers. Table S1: Yields, GPC data, thermal properties for the studied copolymers. Table S2: The photovoltaic performance of the PSCs devices under varied fabrication processes. Table S3: Hole mobilities of the optimized devices measured by SCLC model. Table S4: Electron mobilities of the optimized device measured by the SCLC model.

Conclusions
To conclude, two IDTT-based random CPs, PIDTT-TBT and PIDTT-TFBT as well as the alternating copolymer PIDTT-DTBT as control material, were designed to study the influence of reducing thiophene π-bridge and further fluorination on photostability and photovoltaic performance. Because of selecting the moderate electron-donating IDTT and strong electron-withdrawing BT to construct the polymer backbone, the wide bandgap of 1.76~1.79 eV, lowlying E HOMO ranging from −5.28 to −5.43 eV and excellent photostability were achieved. It was exhibited that the broadened and increased absorption, deepened E HOMO , improved molecular planarity, and thus enhanced film aggregation, but tiny impact on aggregation in CB solution and photostability were observed when PIDTT-DTBT was replaced with PIDTT-TBT and PIDTT-TFBT successively. The best photovoltaic tests disclosed that, PIDTT-TBT-based device yielded 185% increased PCE from 2.05 to 5.84% benefiting from simultaneously elevated V OC of 0.88 V, J SC of 11.08 mA cm −2 , and FF of 59.60% compared to the counterpart, and this improvement was chiefly profited by the broadened and increased absorption, deepened E HOMO , raised µ h , and more balanced µ h /µ e , and slightly optimized morphology of photoactive layer. Conversely, the 50% reduced PCE was observed after further fluorination limited by the minimized J SC and FF, mainly limited by undesired morphology for photoactive layer film as a result of strong aggregation despite of the enlarged V OC . This work suggested tuning the π-bridge in polymer backbone was an easy-to-implement and effectual tactic with a view to enhancing the photovoltaic property.
Supplementary Materials: Detailed experimental procedures and additional characterization data are available online at http://www.mdpi.com/2073-4360/12/2/368/s1. Scheme S1: Synthesis of dibromide DTBTBr 2 , TBTBr 2 , and TFBTBr 2 . Figure S1: 1 H NMR spectrum of DTBTBr 2 in CDCl 3 . Figure S2: 1 H NMR spectrum of TBTBr in CDCl 3 . Figure S3: 1 H NMR spectrum of TBTBr 2 in CDCl 3 . Figure S4: 1 H NMR spectrum of TFBTBr in CDCl 3 . Figure S5: 1 H NMR spectrum of TFBTBr 2 in CDCl 3 . Figure S6: 1 H NMR spectrum of PIDTT-DTBT in CDCl 3 . Figure S7: 1 H NMR spectrum of PIDTT-TBT in CDCl 3 . Figure S8: 1 H NMR spectrum of PIDTT-TFBT in CDCl 3 . Figure S9: TGA curves of PIDTT-DTBT, PIDTT-TBT, and PIDTT-TFBT. Figure S10: UV-vis absorption spectra changes after illumination of PIDTT-DTBT (a), PIDTT-TBT (b), and PIDTT-TFBT (c) in CB solution and a summary of light absorption intensity changes at the peak of each polymer as a function of light-soaking time (d). Figure S11: The J-V curves of the studied copolymers with different weight ratio to PC 61 BM and EQE spectra of corresponding PSCs. Figure S12: The J-V curves of polymers without and with 3%DIO, PC 61 BM replacing with PC 71 BM and EQE spectra of corresponding PSCs. Figure S13: J-V curves of hole-only (a) and electron-only (b) devices for the studied copolymers. Table S1: Yields, GPC data, thermal properties for the studied copolymers. Table S2: The photovoltaic performance of the PSCs devices under varied fabrication processes. Table S3: Hole mobilities of the optimized devices measured by SCLC model. Table S4: Electron mobilities of the optimized device measured by the SCLC model.