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Theoretical Study on the Photoelectric Properties of a Class of Copolymers Based on Benzodithiophene for Solar Cells.

1. Introduction

Solar cells are one critical technology for solving world energy needs. Traditional solar cells made from high-purity silicon have been commercialized, but their applications are finite because of high cost and weight. Polymer photovoltaic cells with a bulk heterojunction (BHJ) active layer have attracted attention due to their potentially low cost, lightweight, flexible, and easy manufacturing [1-4]. In the BHJ structure, the active layer that is sandwiched between anode and cathode constitutes of electron-donating conjugated polymer and electron acceptor, and its properties are the most determining factors in the whole performance of polymer BHJ [5].

In the past few decades, many progresses have been made in polymer BHJ which have reached power conversion efficiencies (PCE) of 11% [6]. The limiting factors of PCE are the stabilities, ability of harvesting the photon flux from the sun, effective exciton separation, and carrier mobilities. In order to improve the device performances, one can develop new device architectures [7, 8], synthesize new polymer donors [9, 10] and new electron acceptors [11-14], or work on both ends.

In recent years, developing low bandgap polymers has provided an alternative approach for achieving high PCEs resulting from their important roles in photoelectric conversion process: capturing solar photons from the sun, exciton generation and separation, carrier injection, hole transport, and affecting the size of the open-circuit voltage ([V.sub.oc]) and short-circuit current ([J.sub.SC]), thus affecting PCE ([eta] = [V.sub.OC] x [J.sub.SC] x FF/[P.sub.in]). In order to develop low-bandgap conjugated polymers, the most powerful strategy is to incorporate electron-rich donor segments and electron-deficient acceptor segments into the polymer backbone. Due to the push-pull interaction, efficient internal charge transfer (ICT) can take place from the donor (D) to the acceptor (A) upon photoexcitation, thus leading to a new absorption band at longer wavelengths [15] and producing appropriate molecular energy levels for high [V.sub.oc], good charge transport, and high [J.sub.SC], thus improving PCE [16].

In recent years, some benzo[1, 2-b:4,5-b']dithiophene-containing polymers have been applied to polymer BHJ and field-effect transistor (FET) [17-22] on account of its electron-rich structures. The relatively large and planar molecular structures of thiophene (TH) derivatives not only keep a high mobility but also help to promote cofacial [pi]-[pi] stacking. Given the symmetrical planar structure and high mobility of benzo[1, 2-b:4,5-b']dithiophene (BDT), Huo and his coworkers synthesized a polymer based on BDT, that is, PBDTTBT [23]. PBDTTBT was well soluble in common organic solvents due to its strong octyl chains and presented an excellent thermal stability with a decomposition temperature of 337[degrees]C without the protection of an inert atmosphere. The group fabricated a polymer solar cell device based on PBDTTBT donor and P[C.sub.70]BM (a fullerene derivative) acceptor in 2010. The structure of the device is ITO/PEDOT-PSS/ polymer: P[C.sub.70]BM (1:2, w/w)/Ca/Al, and its [V.sub.OC], [J.sub.SC], fill factor (FF), and PCE are 0.92 V, 10.70 mA x [cm.sup.-2], 57.5%, and 5.66%, respectively [23].

In order to rationalize the experimentally observed properties of known materials and predict those of unknown ones, theoretical investigations on the structure features, charge transport properties, and exciton dissociation abilities of PBDTTBT are indispensable. In the modeling process, we replace the octyls with butyls to reduce the computation cost. Analogously, we replace benzo[c][1, 2,5]thiadiazole with four pyridazine derivatives and designed four polybenzo[1,2-b:4,5-b']dithiophene derivatives, PBDTTTP, PBDTTTO, PBDTTTPD, and PBDTTFPD and study their potentials as donors in polymer BHJ based on P[C.sub.70B]M. Several parameters of determining the performance of solar cells, electronic and structural properties, open-circuit voltage ([V.sub.OC]), charge transfer properties, exciton dissociation abilities, and theoretical PCE have been investigated.

This paper's distribution is as follows. In Section 2, we describe the computational methods to obtain electronic and structural properties. In Section 3, we detailedly describe the influences on the performance of solar cells by comparing PBDTTBT with designed copolymers, and the conclusion is in Section 4.

2. Calculation Methods

Density functional theory (DFT) has been broadly used to investigate the properties of organic compounds because its high accuracy is reasonable with the ab initio method and less computational time cost, and B3LYP, a hybrid functional, is widely used in calculating organic systems [24-27]. In this paper, DFT and time-dependent DFT (TD-DFT) [28] are employed to gain the qualitative properties of all the compounds at b3lyp/6-31[g.sup.*] level [29, 30]. All the optimized structures are the global minima on the potential energy surface. Periodic boundary conditions (PBC) [31] method is used to optimize block polymers at B3LYP/6-31G(d) and B3PW91/6-31G(d) levels [32]. All the calculations are implemented by Gaussian 09 package [33]. As to the copolymers, density topological analyses are examined by atom in molecule (AIM) analyses [34]. Moreover, the nucleus-independent chemical shift (NICS) [35, 36] is also calculated for copolymers at the B3LYP/6-31[G.sup.*] level, and NICS defined as the negative of the magnetic shielding at a ring critical point (RCP) is obtained from the AIM analyses. Furthermore, the bonding characteristics were also investigated by natural bond orbital (NBO) theory [37-40] and AOMix program packages [41].

3. Results and Discussion

3.1. Geometry Optimization. The drafts of the studied copolymers are depicted in Figure 1, and the optimized structures of parent molecules of copolymers by B3LYP/6-31G(d) along with the abbreviations of each segments are shown in Figure 2. The selected bond lengths and bond angles of these copolymers are also given in Figure 1; herein, the C1-C2 (in PBDTTBT) or C2-C3 (in other copolymers) bond is defined as the central bond that connects the donor and acceptor. All the studied copolymers have the same central bonds (1.45 [Angstrom]), and their dihedral angles are smaller than 37[degrees], which suggest that all the polymers are rigid backbones. The nitrogen- (N-) hydrogen (H) or sulfur (S)/oxygen- (O-) nitrogen (N) interactions forming stable six or five-member rings reduce the dihedral angles and keep the molecular coplanarity, thus benefitting to the rigidity of the copolymers. Besides, the densities of bond critical points (BCPs) and RCPs as well as the distances between the two interactional atoms are also presented in Figure 1. It is worth noting that the angles of S1-C4-C5-C6 and C7-C8-C9-S2 in the four designed copolymers are smaller than C4-C5-C6-C7 and C8-C9-C10-C11 angles in PBDTTBT, which leads to better coplanarity than PBDTTBT.

In order to acquire the charge population analysis on central bonds in studied polymers, we calculate the characters of bond critical points (BCPs) in central bonds and list the data in Table 1S in Supplementary Materials. The data indicate that the two atoms in central bonds are relatively accumulated due to sharing interactions.

Furthermore, the HOMO and LUMO diagrams of monomers in Figure 1S not only can qualitatively illustrate the electronic cloud distribution but also reflect the electron-donating and electron-accepting segments. We can clearly see from Figure 1S that the electronic cloud distribution of HOMO of all the monomers localizes near the polymeric axis and mainly localizes on BDT segments in the four designed copolymers, while that of LUMO localizes near the TBT, TTP, TTO, TTPD, and TFPD segments (the segments in rectangle in Figure 2). The molecular orbital diagrams illustrate that the BDT segments contributing to HOMOs in the five copolymers are as electron-donating segments, and the left segments (TBT, TTP, TTO, TTPD, and TFPD) mainly contributing to LUMOs are as electron-accepting segments. Moreover, in order to quantitatively view the components of the HOMOs and LUMOs, the density of state (DOS) and partial DOS (PDOS) of monomers are calculated and given in Figure 3. As shown in Figure 3, TBT segment contributes to both HOMO and LUMO; nevertheless, BDT mainly contributes to HOMO to some degree. The DOS diagrams for other polymers show that the HOMOs are mainly contributed by BDT segments, and the LUMOs are almost entirely from TBT, TTP, TTO, TTPD, and TFPD segments.

In a word, BDT as a donor mainly contributes to HOMO and the left segments mainly contribute to LUMO, and the push-pull interactions in D-A in the four copolymers are formed.

3.2. Conjugational Properties. Generally speaking, favorable structural stability of molecule originates from its favorable conjugated properties to some degree. In order to understand the structural stability of the studied polymers, we investigate their conjugation properties.

NICS is comprehensively used to express the aromaticity of molecules because it can clearly and simply monitor the condition of ring current. Aromatic systems have pretty negative NICS values, antiaromatic systems have strongly positive NICS values, and nonaromatic cyclic systems should have NICS values close to zero [35,42-44]. The NICS values for the repeated units of polymers are calculated and listed in Table 2S, and the positions of all the rings in the molecules are shown in Figure 1.

In Table 1S, the ring NICS values along the polymeric axis (a, b, and c) are more positive than the individual TH (NICS, -13.9 at B3LYP/6-31G(d) level) and benzene (NICS, -9.7 at B3LYP/6-31G(d) level), which originates from the electrons delocalizing to the whole molecule, thus, forming conjugated systems. As to the same rings, the NICS values of center rings are more negative than the terminal rings, such as the NICS values in a2 and a3 rings are more negative than those in a1 and a4, which illustrate that the ring currents mainly accumulate in the molecular center. In addition, the electrons of the molecules delocalize from donors toward acceptors along the polymeric axis because there are push-pull interactions in the systems; therefore, a2, a3, a4, and c rings are full of ring currents but a1 and b rings lack ring currents. Further, inside rings, that is, d rings, where the NICS values are most negative in respective systems, since electron-rich sulfur and nitrogen atoms in the three systems provide large ring currents. Nevertheless, the carbon atoms in PBDTTTPD and PBDTTFPD are relatively electron-deficient in comparison of nitrogen atoms, which results in small ring currents, thus leading to more positive NICS values in d rings.

Through analyzing the ring currents in RCPs, we find PBDTTTP and PBDTTTO have the same conjugation as PBDTTBT and are relatively stable copolymers.

3.3. Absorption Spectra. As shown in Figure 4(a), the experimental absorption spectrum of PBDTTBT has three absorption bands from 300 to 700 nm both in chloroform and as a solid film, and the main absorption peak of PBDTTBT is located at approximately 581 nm in solution [23]. The simulated absorption spectrum of PBDTTBT monomer at the TD-DFT/B3LYP 6-31G(d) level is depicted in Figure 4(a) for comparison, and the effect of the solvent (chloroform) within polarizable continuum model (PCM) [44] is taken into account during the calculation. The main absorption peak of calculated PBDTTBT monomer is located at 607 nm. The agreements between measured and simulated spectra are well in overall spectral shape, though their main absorption peaks are different. Furthermore, the calculated electronic transitions, absorption wavelengths ([lambda]), oscillator strengths (f), and main configuration of PBDTTBT monomer were shown in Table 1. Herein, the [S.sub.1] [left arrow] [S.sub.0] electronic transition mainly comes from HOMO to LUMO (absorption process). In the process of [S.sub.1] [left arrow] [S.sub.0] electronic transition, charges transfer from the conjugation section of homocyclic rings along the polymeric axis to TBT section as shown in the HOMO and LUMO diagrams of PBDTTBT in Figure 1S. In comparison of the charge difference densities of the main electronic excited states of PBDTTBT in Figure 2S, we find that the charge transfer takes place from BDT to TBT, whereas the alkyl groups hardly participate in charge transfer.

At the same calculation level, the simulated absorption spectra of the four designed copolymers are given in Figure 4(b). As shown in Figure 4(b), the absorption spectra of monomers for BDTTTP and BDTTTO have two absorption bands in the range of 300-800 nm, especially the absorption bands (Q band) near to 700 nm, thus benefitting to harvesting influx photons from the sun, and the monomers of BDTTTPD and BDTTFPD have wide absorption bands in the range of 400-600 nm. The above results suggest that the parent molecules of designed copolymers have broad absorption in the visible region.

Moreover, the detailed maximum absorption wavelengths ([lambda]), oscillator strengths (f), the lowest excitation energy ([E.sup.ex]), and the main configuration of monomers are given in Table 1. In Table 1, the maximum absorption peaks of BDTTTP and BDTTTO belonging to Q bands are red-shifted compared with BDTTBT and the [E.sup.ex] values decrease, thus benefitting electronic transition, whereas, these of BDTTTPD and BDTTFPD are blue-shifted. Generally speaking, the larger oscillator strengths (f), the larger electronic transition probability. As shown in Table 1, the oscillator strengths (f) of all the studied monomers are larger than 0.61, and that of BDTTTPD is the largest one (0.96) of all the f. Combining Figure 4 and Table 1, we find that the main configurations with the maximum wavelength of the parent molecules belong to single electron transitions and originate from HOMO to LUMO mainly assigned to [pi] [right arrow] [[pi].sup.*] transition; as shown in Figure 1S, the electrons transfer from donor (BDT) to acceptors (TBT, TTP, TTO, TTPD, and TFPD).

In comparison to the experimental and theoretical absorption spectra of BDTTBT, we find that the PBDTTBT has wide and strong absorption spectra. Moreover, the designed copolymers have wide and strong absorption, and they have smaller transition energy in the visible region. Therefore, these designed copolymers also have the favorable ability of harvesting the flux photons from the sun.

3.4. Frontier Molecular Orbitals. The properties of frontier molecular orbitals (FMOs) of polymers seriously affect stable and photovoltaic properties. In order to harvest the maximum of the photon flux from the sun and obtain high short-circuit current ([J.sub.SC]), the bandgap (Eg) of the polymers should lie between 1.3 and 1.9eV [45]. Further, its HOMO energy level should be between -5.2 and- 5.8 eV if the donor can keep stable toward oxidation from air, meanwhile, its LUMO level should be between -3.7 and- 4.0 eV as shown in Figure 5. Rather, the open-circuit voltage ([V.sub.OC]) of PSC is eventually confined by the difference between the HOMO of the donor and the LUMO of the acceptor [12,46]. It is useful to research the molecular FMOs because the relative levels of the occupied and virtual orbitals can provide reasonable qualitative indications for processes of exciton generation and dissociation.

In the present work, we calculate the LUMO and HOMO energy levels of the five copolymers by exploring several DFT methods. Since only the values at B3LYP/6-31G(d) and B3PW91/6-31G(d) levels get close to the experimental values of PBDTTBT (the detailed calculated results are given in Table 3S in Supplementary materials); therefore, we only list the LUMO and HOMO energy levels based on the above methods in Figure 5.

In Figure 5, we can see that the value at the B3LYP/6-31G(d) level (-5.01 eV) is higher than the one at B3PW91/ 6-31G(d) level (-5.11 eV), and the two calculated values are higher than the experimental one (-5.31 eV). The difference between experimental and calculated values is about 0.2-0.3 eV, and the different environments between experiment and calculation should be responsible for the difference. As to the designed copolymers, the HOMO levels from B3LYP/6-31G(d) level are higher than the corresponding ones from B3PW91/6-31G(d) level as the PBDTTBT; moreover, all the HOMO levels of designed copolymers are lower than the one in PBDTTBT at the same calculated level; therefore, we predict that the experimental HOMO levels of the designed copolymers are lower than the experimental one of PBDTTBT (-5.31 eV), and the designed copolymers have stronger antioxidation properties than PBDTTBT.

In the formula of power conversion efficiency: [eta] = [V.sub.OC] x [J.sub.SC] x FF/[P.sub.in], the three parameters, [V.sub.OC], JSC, and FF, determine the solar cell performance directly. The parameter, open-circuit voltage ([V.sub.OC]) formed in the process of carrier transport, is popularly used to estimate the maximum PCE [9]. As shown in Figure 5, the experimental [V.sub.OC] (exp) is gained when the [J.sub.SC] is equal to zero in J-V curves. There are two models to describe theoretical [V.sub.OC]: one is the metal-insulator-metal (MIM) model [47], the other model is the [HOMO.sup.D]-LUM[O.sup.A] offset model [9, 48]. Moreover, Lo et al. suggest that [V.sub.OC] is described by a combined MIM model with [HOMO.sup.D]-LUM[O.sup.A] offset model; in that model, they find that when the work function deviation ([DELTA][[phi].sub.electrodes]) of ITO from Al electrode is in the range- 3 and 0 eV, [V.sub.OC] enlarges linearly with [DELTA][[phi].sub.electrodes] as prescribed by the MIM model. Outside this range [V.sub.OC] depends on [HOMO.sup.D]-LUM[O.sup.A] offset model [49]. In the work, we assume that [DELTA][[phi].sub.electrodes] is outside the range -3 and 0 eV; thus, we employed the [HOMO.sup.D]-LUM[O.sup.A] offset model, and the [V.sub.OC] of a conjugated polymer-P[C.sub.70]BM solar cell can be estimated by [9]

[V.sub.OC] = 1/e ([absolute value of ([E.sup.Donor]HOMO)] - [absolute value of ([E.sup.PCBM]LUMO)]) - 0.3 V, (l)

where e is the elementary charges, [E.sup.PCBM]LUMO is equal to -4.3 eV (P[C.sub.70]BM), and the 0.3 V is an empirical factor to offset the exciton binding energy [50]. In comparison with the experimental and simulated [V.sub.OC] values of PBDTTBT, the simulated [V.sub.OC] is lower than the measured one by 0.51 (at the B3LYP/6-31[G.sup.*] level) and 0.41 eV (at the B3PW91/ 6-31[G.sup.*] level), which primarily originates from the HOMO level difference between simulation and experiment. For the sake of comparing the [V.sub.OC] size of designed polymers with PBDTTBT, we also simulate the [V.sub.OC] values of designed polymers by [HOMO.sup.D]-LUM[O.sup.A] offset model. As shown in Figure 5, the [V.sub.OC] of the designed copolymers are larger than the one of PBDTTBT based on either B3LYP or B3PW91 functional resulting from the deeper HOMO levels of designed copolymers. Therefore, the four designed copolymers are promising to improve the [V.sub.OC] relative to PBDTTBT in the experiment.

3.5. Charge Transfer Properties. On the basis of band-like theory, the bandwidth (BW) and electron effective mass ([m.sup.*]) are beneficial parameters for predicting the hole and electron-transporting ability of polymers [51-53]. The effective mass of carrier at the band edge representing mobility was gained as the square of [??] multiplied by the reciprocal of the curvature from E(k) with k, and the formulation is defined as

1/[m.sup.*] = 1/[??] ([[partial derivative].sup.2]E(k)/[partial derivative][k.sup.2]). (2)

The kinetic model of mobility ([mu]) is given by the following formula:

[mu] = eT/[m.sup.*]. (3)

The BW and [m.sup.*] data are given in Table 2. According to the band theory, the wider the BW, the smaller the effective mass, and the larger the kinetic model of mobility [54]. The data in Table 2 investigate that PBDTTBT has wide valence band (0.25 eV) and small [m.sup.*] (-4.45 x [10.sup.4]). By using the same methods as PBDTTBT, we calculate the bandwidths and effective masses for designed polymers and list the data in Table 2.

The data in Table 2 investigate that all the designed polymers have wider valence bands (PBDTTTP: 0.38 eV, PBDTTTO: 0.34 eV, PBDTTTPD: 0.33 eV, and PBDTTFPD: 0.30 eV) and smaller [m.sup.*](PBDTTTP: -2.91 x [10.sup.4], PBDTTTO: -2.91 x [10.sup.4], PBDTTTPD: -2.91 x [10.sup.4], and PBDTTFPD: -3.29 x [10.sup.4]) in comparison of PBDTTBT. Moreover, PBDTTTP and PBDTTTO also have wider conduction bands and smaller [m.sup.*] than PBDTTBT; however, PBDTTTPD and PBDTTFPD have narrower conduction bandwidths and valence bandwidths through comparing PBDTTBT. The above investigations indicate that all the designed polymers have better hole transport properties than PBDTTBT; further, PBDTTTP and PBDTTTO have better electron transport properties than PBDTTBT through conduction band properties.

3.6. Exciton Dissociation. After exciton formation, excitons transport to the donor-acceptor interface. In the interface, exciton dissociation competes with possible recombination. The rates of exciton dissociation and charge recombination are evaluated using the Marcus theory [55]:

K = [square root of (4[[pi].sup.3]/[h.sup.2][lambda][k.sub.B]T [[absolute value of ([V.sub.DA])].sup.2] exp (-[([DELTA]G + [lambda]).sup.2]/4[lambda][k.sub.B]T), (4)

where [lambda] is the reorganization energy, [V.sub.DA] is the electronic coupling between donor and acceptor, [DELTA]G is the free energy change for the electron transfer reaction, [k.sub.B] is the Boltzmann constant, h is the Planck's constant, and T is the temperature (we set T = 298 K in our calculations). In the exciton dissociation and charge recombination, [DELTA]G = [DELTA][G.sub.CT] and [DELTA]G = [DELTA][G.sub.CR], respectively. The electronic coupling can be calculated through employing the generalized Mulliken-Hush (GMH) model [56]. In the work, we calculate the ratio of exciton dissociation rate ([K.sub.CT]) and charge recombination rate ([K.sub.CR]); therefore, the parameters [lambda], [DELTA][G.sub.CT], and [DELTA][G.sub.CR] are mainly studied.

The reorganization energy [lambda] is composed of inner and outer reorganization energy. The inner originates from the change in equilibrium geometry of the donor (D) and acceptor (A) sites consecutive to the gain or loss of electronic charge upon electron transfer. The outer arises from electronic and nuclear polarization/relaxation of the surrounding medium. The inner is composed of two terms

[lambda] = [[lambda].sub.1](A) + [[lambda].sub.2](D), (5)

[[lambda].sub.1](A) = E([A.sup.-]) - E(A), (6)

[[lambda].sub.2] (D)= E(D) - E([D.sup.+]), (7)

Here, E([A.sup.-]) and E(A) are the energies of the neutral acceptor A at the anionic geometry and optimal ground-state geometry, respectively, and -E(D) and E([D.sup.+]) are, accordingly, the energies of the radical cation at the neutral geometry and optimal cation geometry. In the condition of corrole-fullerene dyads in nonpolar solvent, the overall reorganization energy is 0.5 eV. Therefore, we assume here a value of 0.5 eV for the overall reorganization energy in our calculations. All the reorganization energies of researched polymers are given in Table 3. The reorganization energy of PBDTTBT, PBDTTTP, PBDTTTO, and PBDTTFPD is 0.69 eV except for 0.67 eV of PBDTTTPD. The [DELTA][G.sub.CR] can be estimated with

[DELTA][G.sub.CR] = E[I.sub.P](D) - [E.sub.EA] (A), (8)

where [E.sub.IP](D) and [E.sub.EA](A) are the ionization potential of the donor and electron affinity of the acceptor, respectively. The calculated [DELTA][G.sub.CR] values are successively -1.76 eV, -1.92eV, -2.10 eV, -2.09 eV, -2.15 eV for PBDTTBT, PBDTTTP, PBDTTTO, PBDTTTPD, PBDTTFPD shown in Table 3.

As shown in Table 3, we also estimated the [DELTA][G.sub.CT] values in accordance with Rehm-Weller equation [57]

[DELTA][G.sub.CT] = -[DELTA][G.sub.CR] - [DELTA][E.sub.0-0] - [E.sub.b] (9)

where [DELTA][E.sub.0-0] is the energy of the lowest excited state of freebase donor and [E.sub.b] is the exciton binding energy. The calculated [DELTA][G.sub.CT] are depicted in Table 3, and they are -0.31 eV (PBDTTBT), -0.14 eV (PBDTTTP), -0.29 eV (PBDTTTO), -0.21 eV (PBDTTTPD), and -0.15 eV (PBDTTFPD). According to the estimated values of [lambda], [DELTA][G.sub.CR], and [DELTA][G.sub.CT], we calculate the ratio of exciton dissociation rate and charge recombination rate ([K.sub.CT] : [K.sub.CR]), and the data of [K.sub.CT] : [K.sub.CR] listed in Table 3 indicate that PBDTTBT has large [K.sub.CT] : [K.sub.CR] (1.62 x [10.sup.6]). Moreover, the designed polymers PBDTTTP, PBDTTTO, PBDTTPD, and PBDTTFPD have larger [K.sub.CT] : [K.sub.CR] values (2.36 x [10.sup.7], 2.13 x [10.sup.11], 1.90 x [10.sup.11], and 2.70 x [10.sup.11], resp.) than PBDTTBT, which suggest that the designed polymers have better exciton abilities than PBDTTBT.

3.7. External Quantum Efficiency. According to the studies of Scharber et al. in 2006 [9], the external quantum efficiency (EQE) of solar cell is related to the bandgap energy and frontier molecular orbital energy levels under the assumptions that any contribution to the short-circuit current from photons absorbed by the fullerene is neglected and the FF is set to 65%. The calculated EQE data of all the studied polymers are listed in Table 3. From Table 3, we can see that the EQE values of all the designed polymers are larger than 3.5% (especially PBDTTTP: 4.1%) and larger than that of PBDTTBT (1.3%).

In a word, the designed polymers, especially PBDTTTP, have better photovoltaic properties than PBDTBT; therefore, the designed polymers are the promising candidates for polymer BHJ.

4. Conclusions

In this contribution, density functional theory (DFT) and time-dependent DFT (TD-DFT) calculations have been employed to model PBDTTBT to rationalize the relationship between the experimentally observed properties and the structural features in polymer BHJ. Besides, according to PBDTTBT, we design four benzodithiophene-like copolymers, PBDTTTP, PBDTTTO, PBDTTTPD, and PBDTTFPD. In order to investigate their potentials as donors in polymer BHJ based on PC70BM, several parameters of determining the performance of solar cells, structural properties, absorption spectra, frontier molecular orbitals, charge transfer properties, and external quantum efficiency have been researched. PBDTTBT's well conjugation benefits its good stability, and its well photovoltaic performance mainly results from its strong absorption spectra in the range of visible light, appropriate FMO levels, well charge transport, and favorable exciton dissociation. Comparing the four designed copolymers with PBDTTBT, we conclude that the four designed copolymers have stronger exciton dissociation ability and larger open-circuit voltage and external quantum efficiencies. Consequently, the four designed copolymers are promising candidates for polymer BHJ solar cells.

https://doi.org/10.1155/2018/3270313

Data Availability

The data used to support the findings of this study are available from the corresponding author upon request.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This work was supported by the Research Project from Chongqing Committee of Education (KJ15012020), "Chunhui Plan" Cooperating Project from the Ministry of Education (Z2015143), Natural Science Foundation of Yangtze Normal University (Grant no.2103XJQN007), and Chinese Scholarship Council. The authors are grateful to the anonymous referees for their suggestions.

Supplementary Materials

Table 1S: BCP properties, Wiberg bond index, and electronic configurations for bonding orbitals of central bonds. Table 2S: NICS for polymers at RCPs. Table 3S: HOMO and LUMO energy levels and bandgaps from the experiment and calculation for PBDTTBT. Figure 1S: HOMO (H) and LUMO (L) diagrams for monomers and dimers. Figure 2S: charge difference densities of the main electronic excited states of PBDTTBT. Figure 3S: orbital interaction diagrams (B3LYP/6-31G *) for dimers. (Supplementary Materials)

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Xiao-Hua Xie, (1) Xin-Wei Zhao, (2) and Ming Li (3)

(1) School of Chemistry and Chemical Engineering, Yangtze Normal University, Chongqing 408100, China

(2) Department of Physics, Tokyo University of Science, 1-3 Kagurazaka, Shinjuku-ku, Tokyo 162-8601, Japan

(3) School of Chemistry and Chemical Engineering, Southwest University, Chongqing 400715, China

Correspondence should be addressed to Ming Li; liming@swu.edu.cn

Received 20 January 2018; Accepted 29 March 2018; Published 30 May 2018

Academic Editor: Xiufu Hua

Caption: Figure 1: Structural parameters of copolymers and locations for calculated NICS.

Caption: Figure 2: The stereograph of optimized parent molecules of copolymers by DFT//B3LYP/6-31G(d).

Caption: Figure 3: DOS and PDOS of monomers.

Caption: Figure 4: (a) Experimental absorption spectra of PBDTTBT as a film and in chloroform solution [23] and simulated absorption spectra of PBDTTBT monomer (the smaller one) in chloroform solution. (b) Absorption spectra of monomers of the four designed copolymers in chloroform solution.

Caption: Figure 5: Photoelectric conversion process diagram and energy levels of polymers. (exp represents the values of the experimental measures).
Table 1: Maximum absorption wavelengths ([lambda]), oscillator
strengths (f), the lowest excitation energies, and main
configuration of monomers.

          [lambda]          [E.sub.ex]
Monomer      (nm)      f        (eV)

BDTTBT       607      0.81      2.04
BDTTTP       706      0.61      1.76
BDTTTO       718      0.63      1.73
BDTTTPD      538      0.96      2.30
BDTTFPD      540      0.85      2.30

Monomer          Main configuration

BDTTBT      HOMO [right arrow] LUMO (99%)
BDTTTP      HOMO [right arrow] LUMO (99%)
BDTTTO     HOMO [right arrow] LUMO (100%)
BDTTTPD    HOMO [right arrow] L + 1 (97%)
BDTTFPD    HOMO [right arrow] L + 1 (83%)

Table 2: Bandwidth (eV) and effective mass ([m.sup.*]).

             Conduction band           Valance band

                     [m.sup.*]               [m.sup.*]
Polymer      BW    (x [10.sup.4])    BW    (x [10.sup.4])

PBDTTBT     0.08        9.45        0.25       -4.45
PBDTTTP     0.13        5.82        0.38       -2.91
PBDTTTO     0.16        5.04        0.34       -2.91
PBDTTTPD    0.03        12.6        0.33       -2.91
PBDTTFPD    0.03        12.6        0.30       -3.29

Table 3: Reorganization ([lambda]), exciton dissociation energy
([DELTA][G.sub.CT]), charge recombination energy ([DELTA][G.sub.CR]),
the ratio of exciton dissociation rate and charge recombination
rate ([K.sub.CT] : [K.sub.CR]), and external quantum efficiency (EQE).

Polymer                         PBDTTBT             PBDTTTP

[lambda] (eV)                    0.69                0.69
[DELTA][G.sub.CR] (eV)           -1.76               -1.92
[DELTA][G.sub.CT] (eV)           -0.31               -0.14
[K.sub.CT] : [K.sub.CR]    1.62 x [10.sup.6]   2.36 x [10.sup.7]
EQE                              1.3%                4.1%

Polymer                         PBDTTTO              PBDTTTPD

[lambda] (eV)                     0.69                 0.67
[DELTA][G.sub.CR] (eV)           -2.10                -2.09
[DELTA][G.sub.CT] (eV)           -0.29                -0.21
[K.sub.CT] : [K.sub.CR]    2.13 x [10.sup.11]   1.90 x [10.sup.11]
EQE                               3.8%                 3.7%

Polymer                         PBDTTFPD

[lambda] (eV)                     0.69
[DELTA][G.sub.CR] (eV)           -2.15
[DELTA][G.sub.CT] (eV)           -0.15
[K.sub.CT] : [K.sub.CR]    2.70 x [10.sup.11]
EQE                               3.6%
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Title Annotation:Research Article
Author:Xie, Xiao-Hua; Zhao, Xin-Wei; Li, Ming
Publication:International Journal of Polymer Science
Date:Jan 1, 2018
Words:7010
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