Side-chain modulation of dithienofluorene-based copolymers to achieve high field-effect mobilities

A new polymer PDTFDPP20 based on dithieno[3,2-b:6,7-b′]fluorene (DTF) unit was developed. This polymer with a face-on orientation has achieved a high field-effect mobility up to 5 cm² V^–1 s^–1.

Abstract

A ladder-type dithieno[3,2-b:6,7-b′]fluorene (DTF), where the central fluorene is fused with two outer thiophene rings at its 2,3- and 6,7-junctions, is developed. The pentacyclic DTF monomers were polymerized with dithienodiketopyrrolopyrrole (DPP) acceptors to afford three alternating donor–acceptor copolymers PDTFDPP16, PDTFDPP20, and PDTFDPP32 incorporating different aliphatic side chains (R₁ group at DTF; R₂ group at the DPP moieties). The side-chain variations in the polymers play a significant role in determining not only the intrinsic molecular properties but also the intermolecular packing. As evidenced by the 2-dimensional GIXS measurements, PDTFDPP16 with octyl (R₁) and 2-ethylhexyl (R₂) side chains tends to align in an edge-on π-stacking orientation, whereas PDTFDPP20 using 2-butyloctyl (R₁) and 2-ethylhexyl (R₂) adopts a predominately face-on orientation. PDTFDPP32 with the bulkiest 2-butyloctyl (R₁) and 2-octyldodecyl (R₂) side chains shows a less ordered amorphous character. The OFET device using PDTFDPP20 with a face-on orientation determined by GIXS measurements achieved a high hole-mobility of up to 5 cm² V^–1 s^–1. The high rigidity and coplanarity of the DTF motifs play an important role in facilitating intramolecular 1-dimensional charge transport within the polymer backbones. The implementation of main-chain coplanarity and side-chain engineering strategies in this research provides in-depth insights into structure–property relationships for guiding development of high-mobility OFET polymers.

Introduction

Organic field-effect transistors (OFETs) have drawn much research attention on account of their promising advantages of good solution processibility, flexibility, and capability for large-area roll-to-roll fabrication.¹ Solution-processable semiconducting conjugated polymers play a key role in promoting the advance of OFETs. It is generally believed that a high degree of crystallinity of the polymers with in-plane (edge-on) π-stacking is essential to achieve superior carrier transporting properties due to the existence of two charge-transporting pathways: intramolecular charge transport within the conjugated backbones, and intermolecular charge hopping through π-stacking on the condition that the polymer backbones or π-stacking directions are aligned parallel to the transistor channels.² Poly(3-hexylthiophene),³ poly(3,3′-dialkyl-quaterthiophene),⁴ and poly(2,5-bis(thiophen-2-yl)thieno[3,2-b]thiophene) (pBTTT)⁵ are well-documented semiconducting polymers with high mobilities in this category. In constrast, a few emergent semiconducting donor–acceptor (D–A) copolymers lacking detectable long-range order or in-plane dominance yet exhibit mobilities close to or higher than 1 cm² V^–1 s^–1, challenging the authority of the high crystallinity and in-plane packing model.⁶ The most representative polymer is the indacenodithiophene–benzothiadiazole (IDT–BT) copolymer exhibiting short-range and preferentially face-on crystallites, reaching a superior hole mobility of 3.6 cm² V^–1 s^–1.⁷ McCulloch and DeLongchamp demonstrated that the backbone rigidity and coplanarity of the indacenodithiophene moiety in IDT–BT are important structural features to facilitate one-dimensional charge transport along the polymer backbones which is the primary mechanism that accounts for the exceptional OFET mobility.⁷ The high molecular weight of such polymers is also important to connect short-range crystallite domains.⁸ The understanding of structure–property relationships in the IDT–BT polymer prompts us to further implement a backbone coplanarity strategy for developing new high-mobility D–A copolymers. Ladder-type conjugated motifs with forced coplanarity therefore are suitable for this purpose.⁹ Tricyclic fluorene is a superior building block to construct a variety of organic semiconducting materials due to its good chemical stability and intrinsic hole-transporting property.¹⁰ Embedding a fluorene unit into a highly rigid and coplanar ladder-type conjugated framework would be a promising molecular design.¹¹ To this end, we recently designed and synthesized a fluorene-based dithieno[3,2-b:6,7-b′]fluorene (DTF) in which the central fluorene is π-extended by fusing with two outer thiophene rings at its 2,3- and 6,7-junctions.¹² Structurally analogous to IDT, the pentacyclic DTF exhibits high coplanarity and rigidity which reduces the energetic disorder of the backbone and thus enhances 1-dimensional intramolecular charge transport. Furthermore, in comparison with the IDT unit having two dialkyl sp³-carbon bridges in the cyclopentadiene (CP) moieties, the singly dialkyl substituted CP ring in the middle of DTF would minimize the inter- and intramolecular steric hindrance between the aliphatic side chains attached to the polymer backbones, which is beneficial to the strength of the intermolecular interactions and maintenance of main-chain coplanarity. To date, however, incorporation of DTF into D–A copolymers for organic optoelectronics has never been explored. It should also be emphasized that the choice of the aliphatic side chains attached to the polymer would dramatically influence the solubility, molecular packing and thin-film morphology which in turn would alter the mechanism of charge transport and thus the mobility.¹³ For instance, Fréchet and co-workers demonstrated that the edge-on and face-on orientations of conjugated polymers in thin films can be manipulated by the variation of their side chains.^13d In this research, newly developed electron-rich DTF units were copolymerized with electron-deficient dithienodiketopyrrolopyrrole (DPP) units to afford a new class of alternating poly(dithienofluorene-alt-dithienoyldiketopyrrolopyrrole) copolymers (denoted as PDTFDPPs) given that the DPP moiety has a planar conjugated bicyclic structure and strongly electron-withdrawing polar amide groups to induce strong intermolecular interactions.¹⁴ With an aim to control the face-on/edge-on π-stacking orientations of the polymers through side-chain engineering, three PDFTDPPs (PDTFDPP16, PDTFDPP20 and PDTFDPP32) incorporating different aliphatic side chains were produced for systematic investigation. In spite of forming short-range crystallites with face-on π-stacking, PDTFDPP20 with the 2-butyloctyl group on DTF and the 2-ethylhexyl group on the DPP moieties achieved an unprecedentedly high OFET mobility of 5 cm² V^–1 s^–1.

Results and discussion

Design and synthesis of stannylated DTFs and PDTFDPPs

Linear octyl and branched 2-butyloctyl solubilizing groups are selected to be installed on the DTF unit in order to tailor the molecular packing of the resulting polymers. Synthesis of the stannylated DTF monomers is depicted in Scheme 1. 3,6-Dibromofluorene (1) was reacted with octyl bromide and 5-(bromomethyl)undecane under basic conditions to form 3,6-dibromo-9,9-dioctylfluorene (2a) and 3,6-dibromo-9,9-di(2-butyloctyl)fluorene (2b), respectively. Selective iodination of 2a and 2b at the 2,7-positions of the fluorenes yielded the key intermediates 3a and 3b, respectively. Sonogashira coupling of 3a and 3b regioselectively occurred at the 2,7-positions to afford 4a and 4b due to the higher reactivity of iodo over bromo. Reaction of 4a and 4b with Na₂S generated the thiolate intermediates which underwent 5-endo-dig cyclization to form two fused thiophenes in 5a and 5b. Stannylation of 5a and 5b was carried out to afford the Sn-DTF-a and Sn-DTF-b monomers, respectively. Similarly, branched 2-ethylhexyl and 2-octyldodecyl groups with different levels of steric hindrance are introduced to the DPP monomer (6a and 6b, respectively). As shown in Scheme 2, Sn-DTF-a and Sn-DTF-b were copolymerized with 2,5-di(2-ethylhexyl)-3,6-di(5-bromothiophen-2-yl)diketopyrrolopyrrole (6a) to furnish two alternating D–A copolymers, PDTFDPP16 and PDTFDPP20, respectively (16 and 20 are the total carbon numbers of the aliphatic side chains in a repeating unit). Sn-DTF-b was polymerized with 2,5-di(2-octyldodecyl)-3,6-di(5-bromothiophen-2-yl)diketopyrrolopyrrole (6b) to yield PDTFDPP32. Different number average molecular weights (M _n) were determined by gel permeation chromatography (GPC) to be 4.5, 68, and 32 kg mol^–1 for PDTFDPP16, PDTFDPP20, and PDTFDPP32, respectively (Table 1), indicating that the magnitude of M _n is essentially governed by the aliphatic side chains flanking the DTF and DPP units. PDTFDPP20 with branched side chains on both the DTF and DPP moieties has the highest M _n, whereas PDTFDPP16 with linear octyl groups on the DTF units shows the poorest solubility in chlorobenzene, which is responsible for its lowest M _n. PDTFDPP32 has a lower M _n than PDTFDPP20 due to the fact that 6b with the bulkiest 2-octyldodecyl group encounters more steric hindrance when reacting with Sn-DFT-b during the polymerization.

Scheme 1. Synthesis of Sn-DTF-a and Sn-DTF-b monomers.

Scheme 2. Synthesis of the three D–A copolymers PDTFDPP16, PDTFDPP20, and PDTFDPP32.

Table 1. Summary of the intrinsic properties of PDTFDPP16, PDTFDPP20, and PDTFDPP32 .

	M n a (kDa)	PDI b	T d c (°C)	E opt g d (film) (eV)	E ele g e (eV)	λ max (nm)		E HOMO (eV)	E LUMO (eV)
						CHCl3	Film
PDTFDPP16	4.5	1.2	442	1.59	1.63	655	641	–5.23	–3.60
PDTFDPP20	68	2.1	456	1.65	1.76	658, 707	643, 704	–5.38	–3.62
PDTFDPP32	32	1.8	432	1.65	1.73	643, 707	643, 704	–5.39	–3.66

^a M _n = number-average molar weight.

^bPDI = polydispersity index.

^c T _d = decomposition temperature at 5% weight loss.

^d E opt g was estimated from the onset of UV spectrum in thin film.

^e E ele g was estimated from cyclic voltammetry.

Thermal properties

The thermal stability of the polymers was analyzed by thermogravimetric analysis (TGA). PDTFDPP16, PDTFDPP20, and PDTFDPP32 exhibited sufficiently high decomposition temperatures (T _d) of 442, 456, and 432 °C, respectively (Fig. S1† and Table 1). No thermal transition in the differential scanning calorimetry measurements (DSC) was observed for PDTFDPP16 and PDTFDPP32, implying their less crystalline character within the range of scanning temperatures. Nevertheless, PDTFDPP20 exhibited a melting point at 311 °C upon heating and a crystallization point at 275 °C upon cooling, implying the semicrystalline nature of PDTFDPP20 (Fig. 1).

Fig. 1. Differential scanning calorimetry of PDTFDPP20 with a ramping rate of 10 °C min^–1.

Optical properties

The UV-vis absorption spectra in CHCl₃ and thin film are depicted in Fig. 2 and summarized in Table 1. It is expected that the three polymers should possess analogous absorption profiles due to their identical backbone composition. Nevertheless, PDTFDPP20 and PDTFDPP32 exhibited a pronounced vibronic structure, which is much less noticeable for PDTFDPP16. PDTFDPP20 and PDTFDPP32 showed lower-lying HOMO energy levels of –5.38 and –5.39 eV, respectively, while PDTFDPP16 exhibited a higher HOMO level of –5.23 eV. The higher HOMO level may be associated with the linear side chain in PDTFDPP16, which results in less distorted polymer chains. PDTFDPP32 might already reach a saturation of the effective conjugated length. Therefore, PDTFDPP20 with higher molecular weight shows an almost identical absorption profile to PDTFDPP32.

Fig. 2. Normalized UV-vis absorption spectra of PDTFDPP16, PDTFDPP20, and PDTFDPP32 in (a) chloroform solutions; (b) thin films.

Electrochemical properties

Cyclic voltammetry (CV) was employed to determine the highest occupied molecular orbital (HOMO) and lowest unoccupied molecular orbital (LUMO) energies of the polymers (Fig. 3, Table 1). PDTFDPP20 and PDTFDPP32 showed lower-lying HOMO energy levels of –5.38 and –5.39 eV, respectively, while PDTFDPP16 exhibited a higher HOMO level of –5.23 eV. This discrepancy might result from the variation in the HOMO electron-density distribution. As for the LUMO, the three polymers have comparable values, which approximate to –3.60 eV.

Fig. 3. Cyclic voltammograms of PDTFDPP16, PDTFDPP20, and PDTFDPP32 in thin films at a scan rate of 100 mV s^–1.

GIXS measurements

The molecular packing of the thin films on an Si/SiO₂ substrate modified by a self-assembled monolayer (SAM) of octadecyltrichlorosilane (ODTS) was investigated using 2-dimensional grazing incidence X-ray scattering (GIXS). The 2-D GIXS images and the corresponding 1-dimensional out-of-plane (q _z) and in-plane (q _xy) diffraction patterns of the polymer thin films annealed at 200 °C for 10 minutes are illustrated in Fig. 4 and 5, respectively. The PDTFDPP20 film exhibited in-plane (h00) signals assigned to a lamellar spacing (d _l) of ca. 21.6 Å corresponding to side-chain interdigitation (Fig. 5b). Meanwhile, PDTFDPP20 also showed an obvious (010) out-of-plane peak at q _z = 1.7 Å^–1 corresponding to periodic π–π stacking with a distance (d _π) of ca. 3.8 Å between the two facing conjugated backbones (Fig. 5a). The out-of-plane (010) peak also reveals that the PDTFDPP20 adopts a predominately face-on orientation with the backbone plane approximately parallel to the substrate. Conversely, judging from the out-of-plane lamellar stacking (q _z = 0.4 Å^–1 corresponding to d _l = 16.1 Å, Fig. 5a) and the in-plane π-stacking (q _xy = 1.7 Å^–1 corresponding to d _π = 3.6 Å, Fig. 5b) peaks, PDTFDPP16 tends to align preferably in an edge-on π-stacking orientation with the polymer backbone roughly perpendicular to the substrate.

Fig. 4. 2-Dimensional GIXS images of the thin films (a) PDTFDPP16, (b) PDTFDPP20, and (c) PDTFDPP32 on the ODTS-treated Si/SiO₂ substrate.

Fig. 5. 1-Dimensional (a) out-of-plane and (b) in-plane GIXS patterns of PDTFDPP16, PDTFDPP20, and PDTFDPP32. The spacings are listed near the peaks.

As for PDTFDPP32, no evident π-stacking peak could be found in the direction of either q _z or q _xy, indicative of its amorphous character.

The correlation length (L _c) derived from the full width at half maximum (FWHM) of a X-ray diffraction peak in GIXS based on Scherrer's equation can be used to estimate the size of a crystallite.^{1f,7,13 d} By combining the lamellar-stacking diffraction peak in the q _xy or q _z direction and the π-stacking peak in the corresponding perpendicular direction (i.e. q _z or q _xy, respectively) in the 2D-GIXS images, we can approximately acquire the vertical and horizontal correlation lengths (L _c) of a 2-dimensional crystallite. We realized that the ratio (R _L) of lamellar stacking L _c to π-stacking L _c is an important parameter in dictating the face-on/edge-on orientations of the PDTFDPPs. The PDTFDPP16 film with a π-stacking L _c of 4.0 nm (q _xy) and a lamellar L _c of 10.1 nm (q _z) leads to a R _L of 2.5, while the PDTFDPP20 film with a π-stacking L _c of 3.4 nm (q _z) and a lamellar L _c of 19.5 nm (q _xy) yields a R _L of 5.7. The relevant parameters are summarized in Table 2. It can be reasonably inferred that a crystallite with a smaller R _L value prefers to align in an edge-on π-stacking orientation perpendicular to the substrate. Increasing the R _L value by lengthening the lamellar-stacking dimension changes the π-stacking from an edge-on alignment to a face-on orientation. The 2-dimensional molecular packing of PDTFDPP16 and PDTFDPP20 is illustrated in Fig. 6. This argument is also valid for other well-investigated polymer systems. It should also be noted that other factors such as side chain density,¹⁵ solvent selection¹⁶ and the branching point position of the side chain¹⁷ might also play important roles in determining the crystalline orientation. For example, P3HT and PBTTT-C12 (ref. 5a ) with smaller R _L values of 2.03 and 1.90, respectively, show edge-on orientations, whereas PDPP3F-BO with a large R _L value of 7.86 favors the face-on packing.^13d This observation is also consistent with the fact that a nanorod with a high aspect ratio (length divided by width) fails to stand vertically on a substrate.¹⁸ Additional GIXS data evidencing this argument are provided in the ESI.†

Table 2. Stacking parameters of the PDTFDPP16 and PDTFDPP20 thin films.

	π-Stacking		Lamellar stacking		R L c
	d a (Å)	L c b (nm)	d a (Å)	L c b (nm)
PDTFDPP16	3.6	4.0	16.8	10.1	2.5
PDTFDPP20	3.8	3.4	21.6	19.5	5.7

^aSpacing of diffraction peak.

^bCorrelation length based on Scherrer's equation.

^cRatio of L _c (lamellar spacing) to L _c (π-stacking).

Fig. 6. Illustration of the 2-dimensional lamellar and π-stacking crystallites of PDTFDPP16 and PDTFDPP20 with R _L of 2.5 and 5.7, respectively.

In addition to the crystallite dimensions, the interactions between the polymers and underlying self-assembled monolayer (SAM) on the Si/SiO₂ substrate may also influence the polymer orientation. Thin films on trichloro(phenethyl)silane (PTS) and trichloro(1H,1H,2H,2H-perfluorooctyl)silane (PFTS) SAM layers were thus prepared and examined in comparison with ODTS. The GIXS measurements of PDTFDPP16 in the q _xy direction (Fig. 7) reveal that the edge-on π-stacking remains essentially intact regardless of the SAM layer; however, the original face-on orientation of PDTFDPP20 on ODTS in the q _z direction is almost diminished when the SAM layer is changed to PTS or PFTS.

Fig. 7. 1-Dimensional GIXS patterns of (a) PDTFDPP16 in the q _xy and (b) PDTFDPP20 in the q _z direction on the SAM layer of PTS, PFTS and ODTS.

The results indicate that the formation of face-on π-stacking is highly dependent on the underlying SAM layer, which may be attributed to the more intimate contact between the face-on π-conjugated plane and the underlying substrate. It should be also mentioned that the GIXS measurements only reflect the bulk orientations of the thin films. The polymer might adopt a different orientation at the semiconductor/dielectric interface which is the channel area where the charge transport occurs.¹⁹

Theoretical calculations

In order to gain insight into the steric effect derived from different side chains installed on PDTFDPP, our own n-layered integrated molecular orbital and molecular mechanics (ONIOM) calculations were performed. ONIOM approaches were developed to compute large molecules with high accuracy and reduced computational time.²⁰ Within the target structure, two or three layers are defined and treated at different levels of theory. In this study, dimeric structures, 2DTFDPP16, 2DTFDPP20, and 2DTFDPP32 were used as the model compounds for simulating PDTFDPP16, PDTFDPP20, and PDTFDPP32, respectively. Geometry optimization was carried out with the B3LYP/6-31G(d) level of theory applied to the conjugated systems and the universal force field (UFF) applied to the alkyl side chains. The optimized structures are depicted in Fig. 8. It is evident from the edge-viewed structures that 2DTFDPP16 has the most planar and linear conjugated backbone among the three model compounds due to the low steric repulsion between the octyl and 2-ethylhexyl side chains in 2DTFDPP16. It is envisioned that PDTFDPP16 would have strong intermolecular π–π stacking, leading to poor solubility during polymerization and thus would have the lowest M _n. In contrast, steric repulsion between the 2-butyloctyl and 2-octyldodecyl groups in 2DFTDPP32 distorts its main-chain coplanarity and linearity, which is disadvantageous for intermolecular π–π stacking (Fig. 8c). The monomeric unit of PDTFDPP32 has the highest molecular weight among all; however, the M _n of PDTFDPP32 is significantly lower than that of PDTFDPP20. This side-chain repulsion obstructs the cross-coupling reaction between two monomeric units, accounting for the modest M _n of PDTFDPP32. 2DTFDPP20 shows a quasi-linear backbone. The 2-butyloctyl and 2-ethylhexyl moieties in PDTFDPP20 are sufficient to solubilize the resulting polymer without hampering the polymerization, leading to the highest M _n. Furthermore, the curved main-chain structure of 2DTFDPP32 is associated with the amorphous character of PDTFDPP32 suggested by the 2D-GIXS. As mentioned previously, the planar and linear conjugated plane might allow PDTFDPP16 to form a longer π-stacking L _c than PDTFDPP20. On the other hand, it is envisaged that PDTFDPP20 with the dense aliphatic chains would assemble into a longer lamellar packing L _c than PDTFDPP16. Accordingly, the variation in the crystallite dimensions results in the disparity in the thin-film orientation between PDTFDPP16 and PDTFDPP20.

Fig. 8. Optimized geometry of dimeric structures (a) 2DTFDPP16; (b) 2DTFDPP20; (c) 2DTFDPP32 (face view and edge view).

Transistor characterization

The OFET mobilities of the DTF-based polymers were measured by devices using a bottom-gate/top-contact configuration with evaporated gold source/drain electrodes (40 nm in thickness). The OFET devices used SiO₂ as the gate dielectric whose surfaces were modified with a SAM layer of ODTS. All of the output and transfer plots of the devices exhibited typical p-type OFET characteristics (Fig. 9). The hole mobilities are calculated from the transfer characteristics of the devices in the saturation regime. As summarized in Table 3, the hole mobility of the PDTFDPP16 device was 1.20 × 10^–2 cm² V^–1 s^–1 with an on–off ratio of 4.98 × 10⁵. PDTFDPP32 with more carbons in the aliphatic side chains exhibited the lowest mobility of 1.04 × 10^–3 cm² V^–1 s^–1. PDTFDPP20 achieved the highest hole mobility reaching 5.00 cm² V^–1 s^–1 in the saturated regime. The mobility extracted from the linear regime showed an even higher value of 5.26 cm² V^–1 s^–1. GIXS measurements reveal that PDTFDPP20 formed short-range and face-on crystallites in the thin film which is in opposition to the conventional point of view that long-range crystallinity and edge-on π-stacking are essential for high-performance OFET materials. According to the work carried out by Salleo and co-workers, efficient charge transport between the short-range crystallites in the polymer thin film can be realized on the condition that they are inter-connected.⁸ Compared to PDTFDPP16, the much higher M _n (68 kg mol^–1) of PDTFDPP20 not only enhances intrachain charge transport but also enables sufficient connection between the different crystalline domains to realize a high OFET mobility. More importantly, the rigidity and coplanarity of the DTF units facilitate intramolecular 1-dimensional charge transport within the polymer backbones. Charge transport to adjacent chains via π-stack hopping is supposed to be the minor pathway.

Fig. 9. Typical output curves (a, b and c) and transfer plots (d, e and f) of the bottom-gate/top-contact OFET devices for PDTFDPP16, PDTFDPP20, and PDTFDPP32, respectively.

Table 3. Bottom-gate/top-contact OFET characteristics of the polymer thin films.

Polymer	SAM layer	Annealing temp (°C)	Mobility a (cm2 V–1 s–1)	On/off ratio	V t (V)
PDTFDPP16	ODTS	200	1.20 × 10–2	4.98 × 105	–19.0
PDTFDPP20	ODTS	240	5.00	8.67 × 105	–26.0
PDTFDPP20	ODTS	200	5.26 b	1.57 × 106	–1.6
PDTFDPP32	ODTS	Pristine	1.04 × 10–3	3.85 × 104	–13.1

^aSaturated mobility.

^bLinear mobility with V _ds of –20 V.

The surface morphologies of the PDTFDPPs were investigated by atomic force microscopy (AFM). As shown in Fig. 10, PDTFDPP16 exhibited obvious aggregation with a high RMS roughness of 20.2 nm due to its poor solubility in chloroform. However, PDTFDPP32 with better solubility showed a more homogeneous thin-film structure with a dramatically reduced roughness of 2.64 nm. In particular, PDTFDPP20 with a roughness of 8.29 nm exhibited a fibrous texture in its phase image, which might be also associated with its highest charge mobility. These results again demonstrate that side-chain engineering of PDTFDPPs plays a pivotal role in determining the thin-film morphology.

Fig. 10. Atomic force microscopy height (a, b and c) and phase (d, e and f) images for PDTFDPP16, PDTFDPP20, and PDTFDPP32, respectively.

Conclusions

We designed and synthesized a pentacyclic dithieno[3,2-b:6,7-b′]fluorene (DTF) where the central fluorene is π-extended by fusing with two outer thiophene rings at the 2,3- and 6,7-junctions. The newly developed DTF units were copolymerized with the DPP acceptors to yield three D–A copolymers PDTFDPP16, PDTFDPP20, PDTFDPP32 with different aliphatic side chains. The side-chain variations in the polymers play a key role in determining not only the intrinsic molecular properties but also the intermolecular packing. The face-on/edge-on π-stacking of the PDTFDPP-based polymers are associated with the ratio (R _L) of the lamellar stacking correlation length to the π-stacking correlation length of the crystallites. Based on GIXS thin film measurements, PDTFDPP16 with a smaller R _L tends to align in an edge-on π-stacking orientation, whereas PDTFDPP20 with a large R _L adopts a predominately face-on orientation. Bottom-gate/top-contact OFET devices using PDTFDPP20 achieved high hole mobilities of up to 5 cm² V^–1 s^–1. To the best of our knowledge, this value represents the highest p-type mobility for solution-processable conjugated polymers with a face-on orientation determined by GIXS. The rigidity and coplanarity of the DTF framework facilitate intramolecular 1-dimensional charge transport within the polymer backbones. A sufficiently high molecular weight to connect the short-range crystalline domains in PDTFDPP20 is also crucial for efficient charge transport.

This research verifies that edge-on dominance and long-range order to achieve high mobility might not be obligatory as long as the short-range crystallites can be interconnected and efficient intrachain 1D-charge transport along the backbone can be established. This work, implementing main-chain coplanarity and side-chain variations, will provide a new direction to guide the development of new high-mobility semiconducting materials.