Semiconducting Properties of the Hybrid Film of Elastic Poly(styrene-b-butadiene-b-styrene) Block Copolymer and Semiconducting Poly(3-hexylthiophene) Nanofibers

We investigated the electrical properties of a composite film loaded with semi-conductive poly(3-hexylthiophene) (P3HT) nanofibers dispersed in poly(styrene-b-butadiene-b-styrene) (SBS). This structure can be regarded as the hybrid of SBS matrix with elastic mechanical properties and P3HT nanofibers with semiconducting properties. The P3HT nanofibers were embedded in the fingerprint pattern of microphase-separated SBS, as observed by scanning force microscopy. Furthermore, the electrical conductivity and field-effect mobility of the composite films were evaluated. The field-effect mobility was estimated to be 6.96 × 10−3 cm2 V−1 s−1, which is consistent with the results of previous studies on P3HT nanofibers dispersed in an amorphous polymer matrix including poly(methyl methacrylate) and polystyrene, and we found that the P3HT nanofiber network was connected in the SBS bulk matrix. The film was stretchable; however, at elongation by two times, the nanofiber network could not follow the elongation of the SBS matrix, and the conductivity decreased drastically. The field-effect transistor of this film was operated by bending deformation with a radius of curvature of 1.75 cm, though we could not obtain an off-state and the device operated in a normally-on state.

Recently, it was reported that P3HT can be recrystallized as nanofibers in conventional noncrystalline polymers such as poly(methyl methacrylate) (PMMA) and polystyrene (PS) to form composite films loaded with P3HT nanofibers [30][31][32]. These composite films exhibit semiconducting properties and can be fabricated into flexible FETs. Using conductive atomic force microscopy and Kelvin probe force microscopy, an effective nanofiber network percolated over these films has been observed [33,34]. In addition, these composite films could be doped and represented as potential flexible films with considerable mechanical strength and high transparency, owing to the transparent matrix, and high conductivity, owing to the well-developed P3HT nanofiber network, with high environmental stability [35]. The FET characteristics of these films have also been investigated, and the rectifying property has been achieved by binding the composite loaded with n-type nanofibers [36]. From these results, it is expected that a P3HT nanofiber composite film can be regarded as a flexible semiconducting substrate that can substitute a nonflexible silicon substrate. However, the matrices of PMMA and PS used in the previous studies were rather brittle; therefore, these composite films loaded with the P3HT nanofibers were not flexible.
In this study, we used poly(styrene-b-butadiene-b-styrene) (SBS) copolymer as a flexible matrix and investigated the electrical properties of SBS composite films loaded with the P3HT nanofibers. The SBS matrix comprises a soft matrix of polybutadiene and hard microdomains of polystyrene and the solid microdomains act as physical cross-linkers in the soft matrix. This structure can be regarded as the hybrid of SBS matrix with elastic mechanical properties and P3HT nanofibers with semiconducting properties. Furthermore, as SBS is one of the suitable block copolymers for observing the phase structure by the scanning force microscope (SFM), we can confirm the formation and dispersion of P3HT nanofibers in SBS matrix by the SFM observation. It has been reported that SBS can be loaded with conductive fillers, such as Ag nanowires and carbon nanotubes (CNTs), to obtain elastic, flexible, and conductive films [37][38][39][40][41][42]. The formation of the P3HT nanofibers dispersed in a matrix with a crystal structure has not been reported so far. SBS has a microphase separation structure; hence, for the formation of conductive networks and good mechanical strength, it is important to investigate the relationship between the microdomains and nanofibers. Furthermore, we investigated the FET properties of the SBS flexible films loaded with the P3HT nanofibers. The novelty of this work is to develop the elastic and semiconducting polymer sheet using conducting polymers with a high elasticity as substitute for the rigid Si wafer. Although poly(3,4-ethyrene dioxythiophene):poly(styrenesulfonate) (PEDOT:PSS) is known to have high conductivity and applied to various applications, PEDOT:PSS is hydrophilic polymer which cannot be dispersed in almost elastomer with hydrophobic properties. The P3HT nanofiber is a realistic option for achieving the elastomer loaded with conducting polymers. There are some reports on this strategy by using polystyrene-b-poly(ethylene-co-butylene)-b-polystyrene [43][44][45], polydimethylsiloxane (PDMS) [46,47], and silicon rubber [48]. In this study, we particularly focused on the relationship between the structure of the microphase separation and P3HT nanofibers, which has not been discussed in the previous study.
The SBS composite films, in which the P3HT nanofibers were dispersed, were prepared by the following procedure for the preparation of PMMA and PS composite films [30]. The P3HT and SBS powders were added to a solvent mixture composed of chloroform and anisole and the solution was stirred for 60 min at 70 • C. Both the solvent mixture components, chloroform and anisole, are good and poor solvents for P3HT, respectively. The solution was prepared at a fixed P3HT weight ratio of 0.05 wt% and an SBS weight ratio of 0.5 wt% to 5 wt%, in a fixed 70: 30 (v/f ) solvent mixture of chloroform/anisole. The solution was cooled gradually to 20 • C at a rate of 15 • C/h without stirring. Further, this transparent yellow solution changed to a turbid reddish-brown suspension when it was left undisturbed in ambient air for one week. Thin films were prepared by spin-casting the suspension on a Si substrate with a thermally oxidized SiO 2 layer (thickness = 255 nm) on top, and self-standing films were prepared by spin-casting the suspension on a glass substrate, followed by peeling it off of the substrate. For the FET measurements under bending deformation, we used a polypropylene (PP) sheet as a flexible substrate.
The surface observation of the composite thin films was performed using a scanning probe microscope (Nanocute/NanoNavi IIe, SII Nanotechnology Inc., Tokyo, Japan) in the SFM mode. The instrument was equipped with a commercial silicon cantilever (OMCL-AC160TS-C3, Olympus Corp., Tokyo, Japan) with a spring constant and a resonant frequency of approximately 26 N/m and 300 KHz, respectively. Conductivity measurements were performed using a two-probe method in a vacuum below 10 −5 Torr using a source/measure unit (SMU; 6430, Keithley Instruments, Inc., Cleveland, OH, USA) in a cryogenic probing station (LIPS, Nagase Techno-Engineering Co. Ltd., Tokyo, Japan). Pt electrodes were sputter-deposited through a metal mask by reactive ion-beam etching (EIS-200ER, Elionix Inc., Tokyo, Japan), and the width W and gap L of the electrodes were 40 µm and 600 µm, respectively. The electrodes were deposited on the substrate in the case of the thin film, while they were deposited on the film in the case of the self-standing and flexible films for bending deformation.
The FET measurements were performed by the two-probe method in a vacuum below 10 −5 Torr at 300 K using a system combining the cryogenic probing station LIPS, SMU 6430 to measure the source-drain characteristics, and a Keithley 2400 digital source meter (Keithley Instruments, Inc., Cleveland, OH, USA) for applying the gate field. For thin-film measurement, two electrodes on the substrate were used as the source and drain (bottom contact), and the backside of Si was used as a back gate. For FET measurements under the bending deformation, after sputter-deposition of the electrodes on the sample film (top contact), the PMMA solution in acetone (20 wt%) was spin-casted (1000 rpm, 90 s) as a gate insulator. Further, the gate electrodes were sputter-deposited using a metal mask as the top gate. The field-effect mobility, µ, was estimated using the following relationship: where L is the spacing between the electrodes, W is the width of the electrodes, and C ox (=13.8 nm cm −2 ) is the capacitance of the insulation layer of SiO 2 (255 nm thick). I SD is the drain current and V G is the gate voltage.  Figure 2 shows the SFM images of the thin film obtained by spin-casting the suspension of P3HT (0.05 wt%) and SBS (0.5 wt%) in a mixture of chloroform and anisole (70:30 (v/v)). The fingerprint pattern of the microphase separation of SBS was observed in addition to the nanofiber formation of P3HT. From this result, it can be indicated that the SBS polymers in the suspension did not affect the P3HT nanofiber formation. Furthermore, because the microdomain was interrupted at the interface of the P3HT nanofibers, many P3HT nanofibers observed in the SFM image were embedded in the matrix. In addition, the P3HT molecules, which did not participate in the nanofiber formation, also scarcely affected the microphase separation of SBS because the domain spacing apart from the nanofibers was almost the same as that of the cast film of the pristine SBS solution.

Microscopic Structure of the SBS Film Loaded with a P3HT Nanofiber
From the magnified image of Figure 2b, no selective location of either component of SBS could be observed around the P3HT nanofiber. No specific component of the styrene or butadiene block was unevenly distributed around the interface between the SBS matrix and the nanofibers, which was embedded in a matrix for interrupting the microdomain. If there is a preferential interaction between a specific component and nanofibers, nanofibers should be surrounded by this component or aggregated each other. So, it is suggested that there is no preferential interaction between the P3HT nanofibers and each component of SBS.   Figure 2 shows the SFM images of the thin film obtained by spin-casting the suspension of P3HT (0.05 wt%) and SBS (0.5 wt%) in a mixture of chloroform and anisole (70:30 (v/v)). The fingerprint pattern of the microphase separation of SBS was observed in addition to the nanofiber formation of P3HT. From this result, it can be indicated that the SBS polymers in the suspension did not affect the P3HT nanofiber formation. Furthermore, because the microdomain was interrupted at the interface of the P3HT nanofibers, many P3HT nanofibers observed in the SFM image were embedded in the matrix. In addition, the P3HT molecules, which did not participate in the nanofiber formation, also scarcely affected the microphase separation of SBS because the domain spacing apart from the nanofibers was almost the same as that of the cast film of the pristine SBS solution.  Figure 2 shows the SFM images of the thin film obtained by spin-casting the suspension of P3HT (0.05 wt%) and SBS (0.5 wt%) in a mixture of chloroform and anisole (70:30 (v/v)). The fingerprint pattern of the microphase separation of SBS was observed in addition to the nanofiber formation of P3HT. From this result, it can be indicated that the SBS polymers in the suspension did not affect the P3HT nanofiber formation. Furthermore, because the microdomain was interrupted at the interface of the P3HT nanofibers, many P3HT nanofibers observed in the SFM image were embedded in the matrix. In addition, the P3HT molecules, which did not participate in the nanofiber formation, also scarcely affected the microphase separation of SBS because the domain spacing apart from the nanofibers was almost the same as that of the cast film of the pristine SBS solution.
From the magnified image of Figure 2b, no selective location of either component of SBS could be observed around the P3HT nanofiber. No specific component of the styrene or butadiene block was unevenly distributed around the interface between the SBS matrix and the nanofibers, which was embedded in a matrix for interrupting the microdomain. If there is a preferential interaction between a specific component and nanofibers, nanofibers should be surrounded by this component or aggregated each other. So, it is suggested that there is no preferential interaction between the P3HT nanofibers and each component of SBS.  From the magnified image of Figure 2b, no selective location of either component of SBS could be observed around the P3HT nanofiber. No specific component of the styrene or butadiene block was unevenly distributed around the interface between the SBS matrix and the nanofibers, which was embedded in a matrix for interrupting the microdomain. If there is a preferential interaction between a specific component and nanofibers, nanofibers should be surrounded by this component or aggregated each other. So, it is suggested that there is no preferential interaction between the P3HT nanofibers and each component of SBS. Figure 3 shows the I-V characteristics of the thin film obtained by spin-casting the suspension of P3HT (0.05 wt%) and SBS (0.5-5 wt%) in the mixture of chloroform and anisole (70:30 (v/v)). On the polymer composite, because the P3HT molecules were exposed to a small amount of water or oxygen adsorbed in the matrix polymer, the film was difficult to be undoped completely even under the vacuum atmosphere. Therefore, the film had low conductivity even without doping. Increasing the ratio of SBS decreased conductivity, and then the conductivity was too small to be measured in the weight ratio of P3HT less than 0.99 wt% (P3HT: 0.05 wt%, SBS: 5 wt%). Generally, polymer composites loading anisotropic fillers with small diameters and high aspect ratios, such as CNTs, are reported to exhibit a low percolation threshold from 0.0021 to 8 wt% [49]. Furthermore, in the CNT/P3HT system, the percolation threshold was reported to be 1.0 wt% [50]. In the composite films loaded with P3HT, the percolation threshold was reported to be less than 1 wt% [31]. The small percolation threshold of our study was consistent with the previous studies. From the slope, the conductivity of SBS of 0.5 wt% was estimated to be 4.43 × 10 −4 S cm −1 .

FET Properties of SBS Film Loaded with a P3HT Nanofiber
Polymers 2020, 12, x FOR PEER REVIEW 5 of 11 Figure 3 shows the I-V characteristics of the thin film obtained by spin-casting the suspension of P3HT (0.05 wt%) and SBS (0.5-5 wt%) in the mixture of chloroform and anisole (70:30 (v/v)). On the polymer composite, because the P3HT molecules were exposed to a small amount of water or oxygen adsorbed in the matrix polymer, the film was difficult to be undoped completely even under the vacuum atmosphere. Therefore, the film had low conductivity even without doping. Increasing the ratio of SBS decreased conductivity, and then the conductivity was too small to be measured in the weight ratio of P3HT less than 0.99 wt% (P3HT: 0.05 wt%, SBS: 5 wt%). Generally, polymer composites loading anisotropic fillers with small diameters and high aspect ratios, such as CNTs, are reported to exhibit a low percolation threshold from 0.0021 to 8 wt% [49]. Furthermore, in the CNT/P3HT system, the percolation threshold was reported to be 1.0 wt% [50]. In the composite films loaded with P3HT, the percolation threshold was reported to be less than 1 wt% [31]. The small percolation threshold of our study was consistent with the previous studies. From the slope, the conductivity of SBS of 0.5 wt% was estimated to be 4.43 × 10 −4 S cm −1 . We performed the FET measurements of the SBS films loaded with the P3HT nanofibers (P3HT: 0.05 wt%, SBS: 0.5 wt%). Figure 4a shows the output characteristics of the thin films by changing the gate voltage VG from −20 V to −50 V. The drain current (ISD) vs. drain voltage (VSD) deviated from the Ohmic law to saturate at VSD~−10 V. Further, ISD showed significant amplification with increasing negative VG, which is a typical property of p-type semiconductors. Figure 4b shows the transfer characteristic at VSD = −30 V. As mentioned above, an apparent current could be detected at VG = 0; therefore, the characteristics were regarded as normally on state. A typical p-type semiconductor property was observed, where the marked amplification of ISD with respect to the negative VG led to an ISD of approximately −400 nA at a VG of −50 V. Initially, ISD increased in the low-negative-VG region below −40 V; further, it tended to saturate. Here, μ was estimated to be 6.96 × 10 −3 cm 2 V −1 s −1 , which was consistent with the previous studies on P3HT nanofibers composited in PMMA or PS [30,31,36]. Moreover, the on/off ratio was 4.90 × 10 3 . From the results of the electrical measurements, we found that the P3HT nanofiber network was connected in the SBS bulk matrix, and the SBS film loaded with the P3HT nanofiber had a p-type semiconducting property, which was expected to be applicable to the sheet transistor. We performed the FET measurements of the SBS films loaded with the P3HT nanofibers (P3HT: 0.05 wt%, SBS: 0.5 wt%). Figure 4a shows the output characteristics of the thin films by changing the gate voltage V G from −20 V to −50 V. The drain current (I SD ) vs. drain voltage (V SD ) deviated from the Ohmic law to saturate at V SD~− 10 V. Further, I SD showed significant amplification with increasing negative V G , which is a typical property of p-type semiconductors. Figure 4b shows the transfer characteristic at V SD = −30 V. As mentioned above, an apparent current could be detected at V G = 0; therefore, the characteristics were regarded as normally on state. A typical p-type semiconductor property was observed, where the marked amplification of I SD with respect to the negative V G led to an I SD of approximately −400 nA at a V G of −50 V. Initially, I SD increased in the low-negative-V G region below −40 V; further, it tended to saturate. Here, µ was estimated to be 6.96 × 10 −3 cm 2 V −1 s −1 , which was consistent with the previous studies on P3HT nanofibers composited in PMMA or PS [30,31,36]. Moreover, the on/off ratio was 4.90 × 10 3 . From the results of the electrical measurements, we found that the P3HT nanofiber network was connected in the SBS bulk matrix, and the SBS film loaded with the P3HT nanofiber had a p-type semiconducting property, which was expected to be applicable to the sheet transistor.

Electrical Properties of SBS Film Loaded with P3HT Nanofibers under Elongation and Bending Deformation
With increasing P3HT ratio, the conductivity increased but the mechanical strength decreased apparently. So, we measured the conductivity of the self-standing film containing P3HT (0.05 wt%) and SBS (5 wt%), which was the ratio obtaining self-standing film with a sufficient mechanical strength, after an elongation treatment. SFM was performed after the film was stretched by two times, and the SFM phase images of both the unstretched and stretched parts are shown in Figure 5. In the unstretched part, the P3HT nanofibers were observed frequently, while in the stretched part, these nanofibers were not observed at all. However, dark tracks, which were suggested to be the tracks of the nanofibers and existed before the elongation, could be observed. From this result, it was found that the P3HT nanofibers could not follow the elongation of the SBS matrix and were retained in the less-deformed part. As no specific component of the styrene or butadiene block was unevenly distributed around the interface between the SBS matrix and the nanofibers from the SFM images and no specific interaction was suggested to exist at the nanofiber interface, the results were consistent with this suggestion.

Electrical Properties of SBS Film Loaded with P3HT Nanofibers under Elongation and Bending Deformation
With increasing P3HT ratio, the conductivity increased but the mechanical strength decreased apparently. So, we measured the conductivity of the self-standing film containing P3HT (0.05 wt%) and SBS (5 wt%), which was the ratio obtaining self-standing film with a sufficient mechanical strength, after an elongation treatment. SFM was performed after the film was stretched by two times, and the SFM phase images of both the unstretched and stretched parts are shown in Figure 5. In the unstretched part, the P3HT nanofibers were observed frequently, while in the stretched part, these nanofibers were not observed at all. However, dark tracks, which were suggested to be the tracks of the nanofibers and existed before the elongation, could be observed. From this result, it was found that the P3HT nanofibers could not follow the elongation of the SBS matrix and were retained in the less-deformed part. As no specific component of the styrene or butadiene block was unevenly distributed around the interface between the SBS matrix and the nanofibers from the SFM images and no specific interaction was suggested to exist at the nanofiber interface, the results were consistent with this suggestion.

Electrical Properties of SBS Film Loaded with P3HT Nanofibers under Elongation and Bending Deformation
With increasing P3HT ratio, the conductivity increased but the mechanical strength decreased apparently. So, we measured the conductivity of the self-standing film containing P3HT (0.05 wt%) and SBS (5 wt%), which was the ratio obtaining self-standing film with a sufficient mechanical strength, after an elongation treatment. SFM was performed after the film was stretched by two times, and the SFM phase images of both the unstretched and stretched parts are shown in Figure 5. In the unstretched part, the P3HT nanofibers were observed frequently, while in the stretched part, these nanofibers were not observed at all. However, dark tracks, which were suggested to be the tracks of the nanofibers and existed before the elongation, could be observed. From this result, it was found that the P3HT nanofibers could not follow the elongation of the SBS matrix and were retained in the less-deformed part. As no specific component of the styrene or butadiene block was unevenly distributed around the interface between the SBS matrix and the nanofibers from the SFM images and no specific interaction was suggested to exist at the nanofiber interface, the results were consistent with this suggestion.   Figure 6a shows I-V characteristics of the self-standing film in the unstretched and stretched parts after the elongation. In the stretched part, the conductivity decreased by two orders of magnitude, and the conductive network was fatally broken. This result was consistent with the SFM observations. Although the SBS matrix has sufficient elasticity, the conductive nanofiber network could not follow this bulk elongation. Figure 6a shows I-V characteristics of the self-standing film in the unstretched and stretched parts after the elongation. In the stretched part, the conductivity decreased by two orders of magnitude, and the conductive network was fatally broken. This result was consistent with the SFM observations. Although the SBS matrix has sufficient elasticity, the conductive nanofiber network could not follow this bulk elongation.  Figure 6b shows the conductance ratio of the stretched part G to the unstretched part G0 with changing a strain ε. In the SBS film loaded with P3HT nanofibers, the conductance decreased apparently at ε > 0.2, and the conductive property was no longer observed at ε = 1.0 (stretching by two times). In the previous study, the electrical property was maintained at ε of 0.5-1.0 [43][44][45][46], therefore the SBS and P3HT nanofibers had low resistance to the elongation deformation. From this result, it was found that the modification of the interface between each component of SBS and the P3HT nanofiber should be needed.
For the FET measurements of the bending deformation, a flexible film comprising the P3HT nanofibers (0.05 wt%) and SBS (5 wt%) on a PP substrate with a top gate was fabricated. The flexible SBS film loaded with the P3HT nanofibers with the electrodes was bent along a cylindrical mold with a radius of curvature of 1.75 cm, as shown in Figure 7.  Figure 8 shows the transfer characteristics of the flexible SBS film loaded with the P3HT nanofibers before and after the bending deformation at VSD = −30 V. An apparent current could be detected at VG = 0. Furthermore, the amplification with respect to negative VG was scarcely observed in this case, whereas ISD was depressed by positive VG. In this case, impurities could not be removed from the film comprising various components, and we could not obtain an off-state and a proper gate-controlled channel. As a result, the device operated in a normally-on state during the FET operation.  Figure 6b shows the conductance ratio of the stretched part G to the unstretched part G 0 with changing a strain ε. In the SBS film loaded with P3HT nanofibers, the conductance decreased apparently at ε > 0.2, and the conductive property was no longer observed at ε = 1.0 (stretching by two times). In the previous study, the electrical property was maintained at ε of 0.5-1.0 [43][44][45][46], therefore the SBS and P3HT nanofibers had low resistance to the elongation deformation. From this result, it was found that the modification of the interface between each component of SBS and the P3HT nanofiber should be needed.
For the FET measurements of the bending deformation, a flexible film comprising the P3HT nanofibers (0.05 wt%) and SBS (5 wt%) on a PP substrate with a top gate was fabricated. The flexible SBS film loaded with the P3HT nanofibers with the electrodes was bent along a cylindrical mold with a radius of curvature of 1.75 cm, as shown in Figure 7.
Polymers 2020, 12, x FOR PEER REVIEW 7 of 11 Figure 6a shows I-V characteristics of the self-standing film in the unstretched and stretched parts after the elongation. In the stretched part, the conductivity decreased by two orders of magnitude, and the conductive network was fatally broken. This result was consistent with the SFM observations. Although the SBS matrix has sufficient elasticity, the conductive nanofiber network could not follow this bulk elongation.  Figure 6b shows the conductance ratio of the stretched part G to the unstretched part G0 with changing a strain ε. In the SBS film loaded with P3HT nanofibers, the conductance decreased apparently at ε > 0.2, and the conductive property was no longer observed at ε = 1.0 (stretching by two times). In the previous study, the electrical property was maintained at ε of 0.5-1.0 [43][44][45][46], therefore the SBS and P3HT nanofibers had low resistance to the elongation deformation. From this result, it was found that the modification of the interface between each component of SBS and the P3HT nanofiber should be needed.
For the FET measurements of the bending deformation, a flexible film comprising the P3HT nanofibers (0.05 wt%) and SBS (5 wt%) on a PP substrate with a top gate was fabricated. The flexible SBS film loaded with the P3HT nanofibers with the electrodes was bent along a cylindrical mold with a radius of curvature of 1.75 cm, as shown in Figure 7.  Figure 8 shows the transfer characteristics of the flexible SBS film loaded with the P3HT nanofibers before and after the bending deformation at VSD = −30 V. An apparent current could be detected at VG = 0. Furthermore, the amplification with respect to negative VG was scarcely observed in this case, whereas ISD was depressed by positive VG. In this case, impurities could not be removed from the film comprising various components, and we could not obtain an off-state and a proper gate-controlled channel. As a result, the device operated in a normally-on state during the FET operation.  Figure 8 shows the transfer characteristics of the flexible SBS film loaded with the P3HT nanofibers before and after the bending deformation at V SD = −30 V. An apparent current could be detected at V G = 0. Furthermore, the amplification with respect to negative V G was scarcely observed in this case, whereas I SD was depressed by positive V G . In this case, impurities could not be removed from the film comprising various components, and we could not obtain an off-state and a proper gate-controlled channel. As a result, the device operated in a normally-on state during the FET operation. The field effect mobility before and after the bending deformation was estimated to be 1.64 × 10 −5 cm 2 V −1 s −1 and 5.30 × 10 −5 cm 2 V −1 s −1 , respectively, and the mobility at the returning state from the bending deformation was estimated to be 1.35 × 10 −5 cm 2 V −1 s −1 . The value was a considerably small value reported previously, such as the PDMS stretchable composite loaded with P3HT (the order of 10 −2 cm 2 V −1 s −1 ) [46]. This small value suggests that an optimization of the gate and gate insulator was not sufficient. However, the FET operation, that is, the depression of the drain current by VG was hardly affected by the bending deformation, and we can show the possibility of fabrication of flexible devices using the SBS film loaded with the P3HT nanofibers.

Conclusions
We investigated the electrical properties of SBS composite films loaded with P3HT nanofibers. The P3HT nanofibers were embedded in the fingerprint pattern of the microphase separation of SBS, as noticed by SFM observation. A nanofiber network was formed in the SBS matrix, and the conductivity and FET properties were observed. The field-effect mobility, μ, was estimated to be 6.96 × 10 −3 cm 2 V −1 s −1 , which was consistent with the previous study on the P3HT nanofibers composited in PMMA or PS. This film was stretchable, but after elongation by two times, the nanofibers could not follow the elongation of the SBS matrix; hence, the conductivity decreased drastically. The FET of this film was operated by bending deformation with a radius of curvature of 1.75 cm, though we could not obtain an off-state and the device operated in a normally-on state. The elastomer-based semiconducting sheet was one of the candidates for elastic and flexible semiconductors, which have the possibility for applying to biosensors as well as energy devices such as the electrodes of a flexible battery and capacitor.  Acknowledgments: This work was partially supported by a Grant-in-Aid for Challenging Research (Exploratory) 18K19106 from the Japan Society for the Promotion of Science (JSPS).

Conflicts of Interest:
The authors declare no conflicts of interest. The funders had no role in the design of the study; in the collection, analyses, or interpretation of data; in the writing of the manuscript, or in the decision to publish the results. The field effect mobility before and after the bending deformation was estimated to be 1.64 × 10 −5 cm 2 V −1 s −1 and 5.30 × 10 −5 cm 2 V −1 s −1 , respectively, and the mobility at the returning state from the bending deformation was estimated to be 1.35 × 10 −5 cm 2 V −1 s −1 . The value was a considerably small value reported previously, such as the PDMS stretchable composite loaded with P3HT (the order of 10 −2 cm 2 V −1 s −1 ) [46]. This small value suggests that an optimization of the gate and gate insulator was not sufficient. However, the FET operation, that is, the depression of the drain current by V G was hardly affected by the bending deformation, and we can show the possibility of fabrication of flexible devices using the SBS film loaded with the P3HT nanofibers.

Conclusions
We investigated the electrical properties of SBS composite films loaded with P3HT nanofibers. The P3HT nanofibers were embedded in the fingerprint pattern of the microphase separation of SBS, as noticed by SFM observation. A nanofiber network was formed in the SBS matrix, and the conductivity and FET properties were observed. The field-effect mobility, µ, was estimated to be 6.96 × 10 −3 cm 2 V −1 s −1 , which was consistent with the previous study on the P3HT nanofibers composited in PMMA or PS. This film was stretchable, but after elongation by two times, the nanofibers could not follow the elongation of the SBS matrix; hence, the conductivity decreased drastically. The FET of this film was operated by bending deformation with a radius of curvature of 1.75 cm, though we could not obtain an off-state and the device operated in a normally-on state. The elastomer-based semiconducting sheet was one of the candidates for elastic and flexible semiconductors, which have the possibility for applying to biosensors as well as energy devices such as the electrodes of a flexible battery and capacitor.