Regioregular narrow-bandgap-conjugated polymers for plastic electronics

Progress in the molecular design and processing protocols of semiconducting polymers has opened significant opportunities for the fabrication of low-cost plastic electronic devices. Recent studies indicate that field-effect transistors and organic solar cells fabricated using narrow-bandgap regioregular polymers with translational symmetries in the direction of the backbone vector often outperform those containing analogous regiorandom polymers. This review addresses the cutting edge of regioregularity chemistry, in particular how to control the spatial distribution in the molecular structures and how this order translates to more ordered bulk morphologies. The effect of regioregularity on charge transport and photovoltaic properties is also outlined.

Much of what has been learned on how regioregularity impacts the properties of semiconducting conjugated polymers has been through the classic studies of regioregular (RR) poly(3-hexylthiophene) (RR-P3HT), for which higher levels of crystallinity, red-shifted optical absorption 25 , larger charge carrier mobilities 26 and ordered nanostructures 27 are realized when the polymerization reaction introduces the asymmetric 3-hexylthiophene repeat unit in a strict head-to-tail (H-T) manner, see illustration a in Box 1. The presence of other configurations leads to materials that are less prone to crystallization. Furthermore, due to increased steric interference, tail-to-tail couplings decrease the coplanarity of adjacent thiophene heterocycles, and in doing so decrease intrachain electronic coupling. That RR-P3HT is more structurally homogeneous increases the persistence length, the nucleation density and crystallite size 28 . c Regioregular (RR)-conjugated polymers follow a strict orientation of alternating asymmetric repeating units throughout the polymer backbones; in other words, they are described by translational symmetry along the backbone vector. The most representative case is poly(3-alkylthiophene) (P3AT), which has three possible connections, head-to-tail (H-T), head-to-head (H-H) or tail-to-tail (T-T), between two 3-alkylthiophene repeat units (a). RR P3AT has a strict H-T manner, while regiorandom P3AT contain a mixture of three connections. In this case, the regioregularity of P3ATs is denoted as the percentage of the arranged H-T units in the backbone.
In addition to fixing the H-T connections in P3AT structures, an alternative strategy for constructing symmetric thiophene-containing copolymers is to incorporate a p-conjugated spacer between H-H coupled 3-alkyl substituted subunits 41 . A representative example of this type of regiosymmetric polymer is the poly(2,5-bis(3-alkylthiophen-2-yl)thieno [3,2-b]thiophene) (PBTTT), which can be prepared from two symmetrical monomers as shown in the above scheme (b) 44 . The decreased density of alkyl chains in PBTTT with regard to RR-P3ATs allows for greater side-chain interdigitation and closer intermolecular p-p distances that promote self-organization and facilitate high charge carrier mobility.
D-A polymers are also subject to regioregularity considerations when either (or both) of the D or the A moiety is (are) asymmetric. One case in point is the [1,2,5]thiadiazolo [3,4-c]pyridine (also known as pyridyl [2,1,3]thiadiazole, PT) acceptor heterocycle, for which a carbon (C) atom in the widely used benzo [2,1,3]thiadiazole (BT) fragment is replaced by a nitrogen (N) atom 49,50 . This PT for BT modification results in a backbone with higher electron affinity and leads to a narrower optical bandgap, at the expense of reducing the symmetry [51][52][53] . The above illustration (c) shows two generic RR-conjugated polymer systems in which the asymmetric PT fragment is oriented in specific orientations relative to the backbone 66 . In these molecular structures, 'Ar' is a generic, and most typically electron rich, comonomer unit that links the PT units in conjugation, and which can be selected to fine tune optical properties, the promotion of crystalline domains, and/or large charge carrier mobility values. In type I, the PT is positioned along the chain vector so that the pyridyl nitrogens point in same direction, whereas in type II the PT heterocycles alternate in orientation. Of particular interest is that the hole mobility of copolymers with both type I and II RR structures are approximately two orders of magnitude higher than that of their regiorandom counterpart for spun cast films 66  Order across different length scales is often accompanied by improvements of properties relevant to electronic performance. Early work revealed that the chains of a self-assembled P3HT film with a regioregularity of 81% were preferentially oriented parallel to the substrate, whereas the sample with a regioregularity of 91% tended to exhibit lamellae perpendicular to the substrate 26 , and increased charge carrier mobility. For P3HT films with RR 490%, a distinct shoulder located on the long-wavelength side of the absorption maximum is observed as a result of closer interchain packing 29 . Studies of bulk-heterojunction films containing RR-P3HT and [6,6]-phenyl C 61 butyric acid methyl ester (PC 61 BM) reported that the polymer lamellae preferentially orient orthogonal to the substrate, thus providing an increase in the optical anisotropy and a higher absorption of light. A solar cell device based on 95% RR-P3HT gave a power conversion efficiency (PCE) of B4%, much higher than the B1% obtained with a RR of 91% (ref. 25). However, it is worth pointing out that achieving the highest levels of structural precision in P3HTs may not be essential for reaching maximum PCEs 30 . Indeed, a comparison devices prepared using blends containing 86 or 96% RR-P3HT revealed that the lower RR material led to more thermally stable devices as a result of a decreased tendency to phase separate from the fullerene component 31 . These findings provide a glimpse of the challenges and importance of understanding how regioregularity at the molecular level extends to bulk properties and their role in triggering broad interest in the application of RR-P3HT in plastic electronics.
Extraordinary efforts have also been devoted toward developing semiconducting polymers with 'donor-acceptor' type of architectures. These structures feature alternating electron-rich (donor, D) and electron-poor (acceptor, A) moieties along the backbone and this combination leads to optical bandgaps suitable for applications in organic solar cells [32][33][34] . As illustrated in Box 1, the internal organization of D-A copolymers should also be considered when the structural components lack a plane of symmetry perpendicular to the chain vector and the emerging evidence points to improved performance when random permutation of orientations are minimized in the polymer chain, particularly within the context of decreasing energetic disorder 35 . A range of complementary structural characterization techniques have therefore been applied to understand the origin of how structural precision leads to improved properties. These investigations provide an emerging understanding of how the relevant optoelectronic and morphological properties are modulated by the geometrical features of the polymer structures. Thus, it is timely to provide an overview of recently reported RR narrow-bandgap-conjugated polymers and their synthesis, together with studies on how molecular precision translates to increases of morphological order in the bulk and, ultimately, to more desirable properties when considering the fabrication of plastic electronic devices.

Synthesis of RR polymers
Achieving well-defined structures begins with a consideration of the synthetic protocols. Here we provide a largely chronological account of how the challenges of regiochemistry have been overcome through advances in increasingly complex synthetic methods. Early contributions demonstrated the preparation of RR poly(3-alkylthiophene)s through transition metal catalysed methods [36][37][38] . A key synthetic feature is the selective metallation of dibrominated monomer precursors to generate 2-bromo-5metalo-3-alkylthiophenes, which then react preferentially to produce H-T-arranged products. Indeed, the selectivity of these metallation reactions provides the key synthetic handle into achieving RR structures. The polymerization sequence is achieved by using transition metal initiators, such as Ni(dppp)Cl 2 , through a mechanism involving oxidative addition, transmetalation and reductive elimination. Under certain conditions, the reductive elimination step can be controlled to avoid detachment of the growing chain from the metal centre, thus leading to a chain-growth, living polymerization sequence 39,40 .
An alternative strategy to achieve structurally uniform backbones is to react two symmetrical monomer precursors in the polymerization reaction 41 ; this approach is simpler mechanistically and removes any possibility of regioirregularity. Earlier studies 42,43 demonstrated the polymerization of symmetric H-H and T-T dimers of 3-alkylthiophene, affording regiosymmetric polythiophenes. For the representative case of PBTTT, the polymerization is carried out based on two centrosymmetric comonomer units that naturally avoid formation of regiorandom fragments (see the illustration b in Box 1) 44 . Several other RR-conjugated copolymers have been developed using this approach [45][46][47][48] .
While straightforward in design and practice, conventional metal-mediated cross-coupling polymerizations between asymmetric dihalide and bis-stannylated, or bis-boronic ester (acid), starting materials are typically not sufficiently regioselective. Achieving the target materials required developing original synthetic strategies in the case of the asymmetric PT building block [49][50][51][52][53] . As shown in Fig. 1, the reaction of 4,7-dibromo- [1,2,5]thiadiazolo [3,4-c]pyridine (PT-Br 2 ) with mono-or bis-stannyled cyclopenta[2,1-b:3,4-b 0 ]dithiophene (CDT) affords intermediates with precisely controlled orientation of N atoms. These units can be subsequently integrated into the corresponding polymers to generate RR structures. The basis for the specificity of the reaction can be traced to the reactivity of 2,5-dibromopyridine, for which the Pd-mediated cross-coupling of PT-Br 2 with stannylated aromatic compounds was anticipated to occur preferentially at the C-Br adjacent to the pyridyl N atom 54,55 . This specific regioselective reaction can be used to produce two types of intermediates ( Fig. 1) with strictly confined structures, which ultimately enabled a RR orientation of PT and CDT fragments along the backbone. Self-polymerization of the monomer Bu 3 Sn-CDT-PT-Br, containing the two complementary reactive functional groups, yields RR P1, in which all PT units are equally aligned relative to the backbone direction. The reaction of bis-stannyled CDT (CDT-Sn 2 ) with the dibromo-macromonomer Br-PT-CDT-PT-Br provides RR P2 (also known as PCDTPT in the literature), where one finds that nearby PT units point in opposite directions. RA P3 corresponds to the polymer obtained by direct reaction of CDT-Sn 2 with PT-Br 2 . Characterization by 13  Different substitution patterns can also give rise to structural imprecision. A representative case is provided by pentacenecontaining copolymers, which are typically regiorandom 62,63 , due to difficulties in separating regio-isomeric dibrominated precursors. The copolymerization of pure 2,9-and 2,10dibromopentacene derivatives with distannyled bithiophene comonomer gives the well-defined RR copolymers PnBT-2,9 and PnBT-2,10 ( Fig. 3a) 64 . In contrast, mixed dibromopentace starting materials and the same bithiophene reactant yield the regiorandom counterpart PnBT-RRa. Control over regularity of the backbone structure has also been achieved for naphthalenediimide (NDI)-based copolymers (Fig. 3b) 65 . The copolymer RR-P(NDI2OD-T2) can be synthesized via the reaction of NDI2OD-2,6Br 2 with 5,5 0 -bis(trimethylstannyl)-2, 2 0 -dithiophene, while the regiorandom counterpart copolymer RA-P(NDI2OD-T2) can be obtained from the isomeric dibromide mixture of NDI2OD-2,6Br 2 and NDI2OD-2,7Br 2 .
Effects of regioregularity on charge carrier mobility As mentioned previously, RR-P3HT established early on that levels of regioregularity modulate backbone conformations and relevant interchain stacking arrangements in the solid state 24 .   Similar effects are also found in D-A type narrow-bandgapconjugated polymers 66 . Consider, for example, the regio-isomeric copolymers consisting of alternating CDT and asymmetric PT (molecular structures shown in Fig. 4a) 66 . Compared with the regiorandom counterpart, OFETs prepared by spin coating the semiconductor from solution revealed that the RR copolymers with the PT in precisely defined orientations yielded a two orders increase in hole mobility, from 0.005 to 0.6 cm 2 V À 1 s À 1 (Fig. 4c,d) 66 . These initial observations stimulated interest in understanding the structural origins of the improved charge carrier transport and led to the development of related polymer structures with similar regiochemical precision.
Considering the absence of noticeable differences between the optical and electrochemical properties of RR P2 and the regiorandom counterpart RA P3 for samples of similar molecular weights and dispersities, it is reasonable to attribute variations in hole mobility to different structural arrangements or orientations in the thin films. Indeed, grazing-incidence wide-angle X-ray scattering measurements of spin-casted films revealed that the regiorandom RA P3 forms crystallites arranged with a p-p stacking direction mainly perpendicular to the substrate, while in the RR P2 film, crystalline domains adopt a statistical mixture of p-p stacking orientations in the bulk 67 . Interestingly, the lamellar packing distance was observed to be shorter for RA P3 (B2.5 nm) than for RR P2 (B2.1 nm), a feature that was rationalized in terms of possible differences in the tilt angle of the backbone plane or side-chain conformations 67 . Despite that the orientation in the RR film deviates from the generally accepted preferred edge-on manner, such a mixture of ordered lamellar sheets of edge-on and face-on orientation may be beneficial for achieving charge carrier transportation in the three-dimensional network 68,69 . Near-edge X-ray absorption fine structure spectroscopy was also used to determine that the molecular orientation of RR P2 in blade-coated films depends on the nature of the underlying substrate 70 . The films have out-of-plane orientation where the backbones have a preferential 'edge-on' alignment relative to the substrates surface, while the greatest degree of 'in-plane' orientation occurs on the bottom side of a film deposited on a uniaxial nano-grooved substrate with increasing blade-coating rates. In this respect, the RR PT-based polymers provide an interesting platform for investigating how intermolecular stacking affects the charge carrier transport. By combining nano-grooved substrates and a slow drying process, RR P2 can be macroscopically aligned into oriented crystalline fibres. Such highly orientated and ordered polymer chains achieved significant gains in charge mobility. Based on the fractionated sample with a molecular weight of 300 kDa, a hole mobility of 6.7 cm 2 V À 1 s À 1 was reported, for which the transport was anisotropic with a higher mobility in the direction of the fibres 71  REVIEW 300 kDa RR P2 film on nano-grooved substrates was performed by high-resolution atomic force microscopy, as shown in Fig. 4f. The results show that the individual fibres are aligned within the bundles, leading to no obvious grain boundaries. AFM line-cut surface profile shows the width of an individual fibre to be B2-3 nm, which is comparable to the length of the repeat unit; thus the most reasonable way for polymer chains to align is in the direction of the long axis of the fibres. These features are consistent with long-range alignment of the semiconducting polymer chains, such that the transport occurs predominantly along the conjugated backbone with occasional p-p hopping to neighbouring chains. It is worth pointing out that the mobility of 423 cm 2 V À 1 s À 1 (and related higher values in the literature) for RR P2 in Fig. 4e is calculated in the low gate voltage (V g ) regime (|V g |o20 V, dashed line) from devices in which the plot of I d 1/2 (I d is the drain current) versus V g shows double slope characteristics 72 . If one calculates the mobility in the range between À 25 and À 35 V, one obtains a mobility ofB8 cm 2 V À 1 s À 1 . There is substantial lively debate in the literature regarding the physical basis responsible for the departure from the ideal metal oxidesemiconductor field-effect transistor model and its impact on accurate charge carrier mobility determination, as observed for both small molecule and polymer OFETs 73,74 . In the case of RR P2, examination of the device characteristics revealed that the double slope is likely due to electron trapping at the dielectric interface, which not only modifies the I d 1/2 versus V g , but is also responsible for device variability through multiple scans 75 . Gate bias dependence of the contact resistance at the source and drain electrodes can also lead to non-idealities, as described in the literature 73 . Devices with characteristics such as those in Fig. 4e therefore need to be examined with care as they may lead to misassignment of carrier mobilities. Moreover, their unstable performance thus far precludes a practical technological impact.
Copolymers containing CDT and BT units (that is, PBT) exhibit relatively high-lying highest occupied molecular orbital levels (-5.0 ± 0.2 eV), which are borderline for achieving long-term air stability (the highest occupied molecular orbital level is required to be below the air oxidation threshold of approximately -5.3 eV) 76 . To address this issue, the asymmetric monofluoro-substituted BT has been used as the acceptor, see Fig. 4b for molecular structures, which was anticipated to lower the orbital levels of the polymers and improve stability toward oxidation. Comparison of the RR copolymer (P2F) with precisely oriented fluorine atoms along the backbone revealed improved hole mobility (average 0.9 ± 0.2 cm 2 V À 1 s À 1 ) compared with the regiorandom counterpart (PRF, which has the asymmetric FBT units randomly oriented across the polymer backbone, average 0.3 cm 2 V À 1 s À 1 ) 77 .
The effect of regularity on charge transport has also been demonstrated in polymers that differ in terms of the direction of conjugation extension, for example 2,6-/2,7-linked NDI frameworks 65 , 2,9-/2,10-linked pentacene 78 or 1,6-/1,7-linked perylenediimides (PDI) 79 . As shown in Fig. 3b, a recent study reported a correlation between the backbone structure and the charge carrier mobilities of the NDI-based RR polymer RR-P(NDI2OD-T2), and its regiorandom counterpart RA-P(NDI2OD-T2) (also known as RI-P(NDI2OD-T2) in the literature), see Fig. 5 for molecular structures. Despite the greater than 100 nm shift in the optical bandgap in going from RR-to RA-P(NDI2OD-T2) in films coated from chlorobenzene (CB), these polymers exhibited comparable lowest unoccupied molecular orbital (LUMO) energy levels. This observation suggests that the optical shift is not caused by a further disruption of p-conjugation along the backbone of the RI polymer, which is understandable because regiorandom 2,6and 2,7-NDI-thiophene linkages do not modify intramolecular steric demands. Grazing-incidence X-ray diffraction (GIXD) measurements indicated that the RR-P(NDI2OD-T2) film prefers a face-on arrangement, while the RA-copolymer film gave rise to a rather amorphous diffraction pattern, see Fig. 5a,b. By adjusting the film-forming conditions, RR-P(NDIOD-T2) films prepared from CB and chloronaphthalene:xylene solvent mixtures exhibited a similar crystalline structure along the three crystallographic axes, whereas thermal annealing led to larger vertical electron mobility. In contrast, a disordered phase was observed for RA-P(NDIOD-T2) films (Fig. 5b), while the ordered stacks along the lamellar direction did not show detectable p-stacking. Although thermal annealing leads to considerable increase in the coherence length and degree of crystallinity in the lamellar direction, the vertical mobility remains nearly unchanged (Fig. 5b). Moreover, from Fig. 5b, one observes that the RR copolymer exhibits higher vertical electron mobility than the random counterpart.
Pentacene-based copolymers constructed via attachments at the 2,9-or 2,10-positons are also worth considering within the context of structural precision 78 . A synthetic route to obtain pure 2,9-and 2,10-dibromopentacene precursors was reported, see Fig. 3a, which enabled the synthesis of regioregular pentacene-containing copolymers 80 . Despite the relatively low n-type mobility (10 À 4 -10 À 5 cm 2 V À 1 s À 1 ) of the resulting RR copolymers, these values are considerably higher than what is obtained when using the regiorandom counterpart (8 Â 10 À 7 cm 2 V À 1 s À 1 ). RR pentacene-based conjugated polymers consisting of alkylated-bithiophene as the comonomers were examined, please refer to Fig. 3a for their molecular structures. Charge carrier mobility measurements showed that the copolymers based on RR PnBT-2,10 ( Fig. 3a) and the regiorandom counterpart had similar hole mobility in the order of 10 À 4 B10 À 3 cm 2 V À 1 s À 1 , while the hole mobility of about 0.03 cm 2 V À 1 s À 1 that obtained from optimized device fabrication conditions based on RR PnBT-2,9 (Fig. 3a) was much higher. Compared with PnBT-2,10, which has a bent 'zigzag' backbone, PnBT-2,9 has a more linear and rod-like structure and more easily forms ordered domains for better charge transport. GIXD measurements indeed revealed slightly shorter lamellar spacing of 14.5 Å for PnBT-2,9 than that of 15.8 Å for the other two copolymers 64 . These findings provide a relevant metric on how controlling the connectivity for modulating electronic delocalization impacts the thin film order and thereby electronic properties.
Effect of regioregularity on photovoltaic performance Remarkable progress with the certified power conversion efficiency up to 11.5% has been achieved for the application of narrow-bandgap-conjugated polymers for organic solar cells 81 . As illustrated in the preceding examples, controlling the organizational precision within D-A copolymers leads to improved performance factors when included as the OFET semiconductor layer. It stands to reason to examine to what extent these trends extend to the self-organization of bulkheterojunction (BHJ) active layers, in which the D-A copolymer behaves as the p-type component and the fullerene derivatives provide the complementary n-type phase. One consideration is that random permutations of asymmetric units open the possibility of energetic disorder 35 that may localize the charge carrier wave functions and in this way influence charge extraction and recombination. The orientation of asymmetric species also affects the molecular configurations and consequently the self-organization of the blend films. Yet another consideration is that a greater driving force for crystallization for a structurally homogenous polymer can lead to modification of phase separation during the timescale of film evolution. With regard to these effects, the regioregularity of conjugated polymers can affect the current density and fill factor, and thus the overall photovoltaic performance. In addition, as the open-circuit voltage (V OC ) of polymer solar cells is primarily determined by the tail of the density of states 82 , the reduced disorder in such RR narrowbandgap-conjugated polymers offers a platform to study whether structural disorder of the polymer backbone can result in the loss of V OC . To address these issues, an initial investigation of the effects of regiochemistry control on photovoltaic performance was performed using the RR-conjugated polymer PIPT-RR (also known as PIPT-RG in the literature 83 , molecular structures shown in Fig. 6a), which contains PT and indacenodithiophene (IDT) units. In PIPT-RG, the nitrogen atoms in the PT unit are precisely arranged along the backbone so that each one has an adjacent proximal and an adjacent distal counterpart across the two IDT flanking units. Despite a lack of obvious differences in the orbital energy levels and optical bandgaps, the higher charge carrier mobility of the PIPT-RR relative to PIPT-RA improved the photovoltaic performance of the polymer solar cells, compared with the regiorandom counterpart in terms of higher V OC both in conventional and inverted device configurations 83 . These findings were amongst the first to highlight the benefits of controlling the regiochemistry of PT-containing narrowbandgap-conjugated polymers.
The RR narrow-bandgap-conjugated terpolymer PIPCP, and its less structurally precise counterpart PIPC-RA (molecular structures shown in Fig. 6d) have also been constructed by combining two different donor fragments (IDT and CDT), and forcing the pyridyl N-atoms to point towards the CDT unit 84 . Optical spectroscopy reveals an absorption profile of PIPCP that is red-shifted, narrower in width, and exhibits more pronounced vibronic-like features, relative to PIPCP-RA. Grazing-incidence wide-angle X-ray scattering measurements of PIPCP show a strong reflection peak preferentially aligned in the out-of-plane direction at q ¼ 1.47 Å À 1 that corresponds to p-p stacking, and an intense reflection at q ¼ 0.24 Å À 1 , which is assigned to the alkyl chain organization. Both signals extend to the in-plane direction, suggesting that both face-on and edge-on orientations exist in the thin film (Fig. 6b). In contrast, the regiorandom counterpart PIPC-RA shows a higher contribution from an amorphous-like ring, instead of clear peaks (Fig. 6c). This structural insight indicates that the molecular precision of PIPCP translates into BHJ films with higher levels of morphological order in the donor phase. Figure 6e,f shows the current densityvoltage characteristics (J-V) and the external quantum efficiency spectra of the solar cells, one finds considerable improvements with the regioregular structure. This increase in PCE is attributable to the increased current density.
Of particular relevance is the low photon energy loss (E loss ). E loss is defined here as E g À eV OC , where E g is the optical bandgap of the donor polymer, and eV OC is obtained from BHJ blends prepared with PIPCP and either PC 61 BM or [6,6]-phenyl C 71 butyric acid methyl ester (PC 71 BM). The E loss value of the PIPCP blends was measured to be 0.52 ± 0.02 eV (ref. 85), which is lower than the majority of narrow-bandgap-conjugated polymer reported in the literature, and is lower than the widely referenced   86 . The high morphological order, low Urbach energy, and low energetic disorder indicate that reducing disorder (energetic and morphological) can minimize voltage losses, as proposed by a recent theoretical contribution 87 .
Despite that PTB based copolymers show excellent PCEs of about 10%, the backbone structures remain relatively undefined due to the asymmetric TT moiety. To address this issue, the RR polymer of PBDTTT-C-T was developed by controlling the orientation of sulfur atoms in the intermediate, with the molecular structures shown in Fig. 6g. Compared with the random counterpart, the RR copolymer shows a narrower optical bandgap (Fig. 6h), higher crystallinity, higher hole mobility, and more uniform morphology with better interpenetrating networks in the blend films. Inverted BHJ solar cells based on RR PBDTTT-C-T exhibit a PCE that is 19% higher than what is observed for the regiorandom counterpart, particularly as a result of increased current density and fill factor (Fig. 6i). The enhanced PCE for RR PBDTTT-C-T presumably correlates with the improved absorption and increased charge carrier mobility as a result of effective ordering between polymer chains 60 . Similar observations have been reported for the recently developed RR copolymer PBDT-TSR that comprises the asymmetric TT unit 88 . Although the orbital energy levels and miscibility with PC 71 BM were not greatly influenced by the backbone configuration, the RR copolymer yielded a PCE of 410%, which was higher than the random counterpart. In addition to the asymmetric TT unit of the PTB series polymers, researchers investigated the symmetry of donor comonomer by constructing thienothiophene quinoidal character with enlarged molecular size 89 . It is worth noting that copolymers with symmetric donor comonomer exhibit comparable PCE at the same order of PTB7, while the copolymer based on the comonomer that only has C1 symmetry exhibits extremely low PCE. These findings further highlight the importance of molecular structure control for attaining high performance.
PDI-based conjugated polymers exhibit regioregularity considerations similar to those mentioned for NDI-containing systems. Indeed, strategic design led to the preparations of the regioregular PDI-based copolymer RR PDI-diTh and the regiorandom counterpart RA PDI-diTh (also known as r-PDI-diTh and i-PDI-diTh in the literature, respectively) 90 . The regioregular copolymer RR PDI-diTh exhibits improved photovoltaic performance with respect to the RA PDI-diTh, due to the higher current density of the former 90 .
As a final illustrative example, FBT RR copolymers also yield improved PCEs relative to their regiorandom analogues 56 . The primary source of improvement was the increased short-circuit current. Furthermore, isomeric RR and random conjugated copolymers have been reported that comprise multicomponents of diketopyrrolopyrrole, thienopyrrolodione, and bithiophene units (molecular structures shown in Fig. 7a) 91 . Comparison of the RR polymer RR-PDPP/TPDalt2T (also known as reg-PDPP/TPDalt2T in the literature 91 ) and its regiorandom counterpart RA-PDPP/TPDalt2T (also known as ran-PDPP/ TPDalt2T in the literature 91 ) revealed that the statistical distribution of monomeric units had a pronounced influence on the optical bandgaps and molecular orbital energy levels. Although the absorption profile of the random polymer broadened towards a longer wavelength (Fig. 7b), the decreased LUMO energy level associated with the coarser morphology (as shown in the transmission electron microscopy (TEM) images in Fig. 7c,d) and a rougher surface led to lower short-circuit current density in the random polymer 91 . There is therefore ample evidence from many research groups that indicate positive improvements in critical device variables through controlling the regiochemistry of narrow-bandgap-conjugated polymers, and related structures.
Outlook and perspective Precise control over the orientation of asymmetric units along the backbone enables the achievement of regioregular narrow-bandgap-conjugated polymers. These materials exhibit advantageous optoelectronic and morphological properties relative to their regiorandom derivatives, and these competitive advantages should be kept in mind when considering asymmetric building blocks, such as 5H-dithieno[3,2-b:2 0 ,3 0 -d]pyran 92 , thieno-benzo-isoindigo 93 , and diketopyrrolopyrrole derivatives that functionalized with aromatic units 94 . Understanding why the integration of regioregular structures into field-effect transistors leads to higher charge carrier mobilities requires a full theoretical understanding of the transport mechanism, including the effects of the intramolecular dipole orientations, the electronic density of states, the general morphological distribution of polymer chains, and supramolecular self-organization in a well-controlled macroscopic alignment of polymer chains. Truly delocalized electron transport in a polymer chain may be attained 95 , which has the potential to elucidate the intrinsic limits of the charge carrier mobility in soft semiconducting matter. The significantly enhanced photovoltaic performances of regioregular donoracceptor narrow-bandgap polymers highlight the need for precise control over the distribution of monomeric units, where increased order can reduce open-circuit voltage losses, and provide a more favourable self-organization of the BHJ films.
To provide a general guideline for the design of RR narrowbandgap polymers for solar cell applications, more fundamental knowledge is required concerning the effects of regioregularity on electronic structures, photochemical stabilities, the exciton dissociation dynamics of the charge carrier process, and more importantly, the correlation between the energy of the different states and specific morphological characteristics. Various thin film characterization techniques such as grazing-incidence X-ray diffraction, resonant soft X-ray scattering, transmission electron microscopy, and tomographic techniques can be used to probe nanoscale and intermolecular organization features, and the evolution of the crystallite nucleation and growth during the film casting procedure.