*3.1. Analysis of Optical and Thermal Properties*

All of the prepared hybrid films have optical transmittances greater than 90% with the film thickness about 200 nm. Figure 2a shows the UV-vis spectra of the optical transmittance of A0, A30, B30, and C30 hybrid thin films in the visible light region of 400–700 nm, the optical transmittance is greater than 90%. This result shows that the composite dielectric film has good transparency (as listed in Table 1). Supplementary Figure S1 shows the TEM image of inorganic TiO2-SiO<sup>2</sup> nanoparticles. It shows that the size of the particles of the as-prepared TiO2-SiO<sup>2</sup> is about 30–40 nm with a spherical morphology. When the particle size is less than 50 nm, light scattering can be negligible [42]. Moreover, Supplementary Figure S2 shows the optical transmittance of A0, A30, B30, and C30 films as the dielectric layer of OTFTs device in the visible light region of 400–700 nm. This indicates that the optical transmittances of all samples are greater than 75%. The thermal properties of the prepared polyimide-TiO2-SiO<sup>2</sup> composite dielectric films were analyzed by thermogravimetric analysis (TGA). Figure 2b shows the TGA curves undertaken in a nitrogen atmosphere. It reveals that the decomposition temperature (Td) of A0, A30, B30, and C30 hybrid thin films are 418, 450, 461, and 443 ◦C, respectively. The relative parameters for thermal properties are listed in Table 1. This indicates that the thermal decomposition temperature increases with the content of TiO2-SiO<sup>2</sup> nanoparticles due to the formation

of chemical bonding between polyimide and TiO2-SiO2, which can restrict the polyimide chain reaction, and the T<sup>d</sup> and thermal stability for the hybrid films thus increases as TiO2-SiO<sup>2</sup> content increases [22]. In addition, the addition of Jeffamine D2000 and polyurethane also increase the T<sup>d</sup> from 426 ◦C to 477 ◦C for B0–B40 and 405 ◦C to 454 ◦C for C0–C40. The increase in T<sup>d</sup> for B0–B40 is due to the hydrogen bonding between the N atom in the Jeffamine D2000 and the composite dielectric material. However, the polyurethane is a softer polymer, so the T<sup>d</sup> of B0–B40 is expected to be lower than that for the other two series of hybrid films. However, the T<sup>d</sup> for all of hybrid films nonetheless exceed 400 ◦C, indicating good thermal stability. In addition, none of the hybrid films exhibit weight loss at temperatures lower than 300 ◦C, and the residual quantity of A0–A40 increased with increasing quantities of TiO2-SiO<sup>2</sup> added when the temperature increased to 900 ◦C. At 900 ◦C most of the polyimide has completely decomposed, and the remaining residual quantity is an inorganic oxide forming a cross-linked stable network. This result demonstrates that inorganic TiO2-SiO<sup>2</sup> nanoparticles have been successfully incorporated into organic materials. Figure 2c shows the differential scanning calorimeter analysis (DSC) measured in a nitrogen atmosphere. It reveals that the glass transition temperatures (Tg) of A0 (PI), B0 (PI:D2000), and C0 (PI:PU) are 266 ◦C, 286 ◦C, and 270 ◦C, respectively. In addition, no T<sup>g</sup> point of all samples can be observed in Figure 2c in the temperature range of 25–350 ◦C, showing the T<sup>g</sup> of all hybrid materials (PI/TiO2-SiO2) prepared in this study exceeds 350 ◦C (as listed in Table 1). It is known that the inorganic TiO2-SiO<sup>2</sup> nanoparticles can be uniformly distributed in the polyimide matrix, and form a crosslinking structure between the polyimide and nanoparticles, which restricts the chain motion and strengthens the polyimide strength, thereby causing an increase in T<sup>g</sup> and Td. The results of thermal analysis suggest that all of the hybrid films prepared in this study exhibit good heat resistance and no phase separation between the polyimide and TiO2-SiO<sup>2</sup> nanoparticles [43]. *Polymers* **2020**, *12*, x FOR PEER REVIEW 6 of 16

**Figure 2.** (**a**) UV-vis spectra of the optical transmittance, (**b**)TGA curves, and (**c**) DSC curves of hybrid thin films. **Figure 2.** (**a**) UV-vis spectra of the optical transmittance, (**b**)TGA curves, and (**c**) DSC curves of hybrid thin films.

when subjected to a stretching ratio of 30%, and numerous cracks and wrinkles are produced when the stretching ratio reaches 50%. The B0 film exhibits only wrinkles under the stretching ratio of 30%, but numerous cracks are also present as the stretching ratio increases to 50%. Compared with the result for A0, the addition of Jeffamine D2000 (B0) is seen to improve the film's stretchability. For the C0, the film shows no cracks or wrinkles subject to stretching ratios of 30% and 50%. The results reveal that the addition of polyurethane is more effective than the addition of Jeffamine D2000 for improving the tensile properties of the thin films in the absence of inorganic particles in the polyimide matrix. Moreover, the effect of nanoparticles TiO2-SiO2 on the tensile properties is seen in Figure 3b. Adding TiO2-SiO2 is seen to cause the tensile properties of the A30 films to decrease obviously because more cracks are observed for a stretching ratio of 30%. For the case of B30 films, wrinkles continue to be generated at a stretching ratio of 30%, but no cracks are observed. The C30 films' stretchability is optimal at the stretching ratios of 30% and 50%. No cracks or wrinkles are observed on the C30 films. Therefore, from the optical microscopy diagram of these dielectric hybrid films, the addition of Jeffamine D2000 and polyurethane polymers is seen to increase the film stretchability and the addition of polyurethane produces tensile properties superior to those obtained from the addition

*3.2. Analysis of Stretching Properties*

of Jeffamine D2000.


**Table 1.** Summary of properties of the prepared dielectric hybrid film.

<sup>a</sup> Thickness of the prepared thin film. <sup>b</sup> Ra is the average roughness of the prepared thin films, respectively.

#### *3.2. Analysis of Stretching Properties*

Figure 3 shows the optical microscopy images of (a) A0, B0, and C0 and of (b) A30, B30, and C30 thin films subject to various strain levels. Figure 3a shows that bare polyimide film generates cracks when subjected to a stretching ratio of 30%, and numerous cracks and wrinkles are produced when the stretching ratio reaches 50%. The B0 film exhibits only wrinkles under the stretching ratio of 30%, but numerous cracks are also present as the stretching ratio increases to 50%. Compared with the result for A0, the addition of Jeffamine D2000 (B0) is seen to improve the film's stretchability. For the C0, the film shows no cracks or wrinkles subject to stretching ratios of 30% and 50%. The results reveal that the addition of polyurethane is more effective than the addition of Jeffamine D2000 for improving the tensile properties of the thin films in the absence of inorganic particles in the polyimide matrix. Moreover, the effect of nanoparticles TiO2-SiO<sup>2</sup> on the tensile properties is seen in Figure 3b. Adding TiO2-SiO<sup>2</sup> is seen to cause the tensile properties of the A30 films to decrease obviously because more cracks are observed for a stretching ratio of 30%. For the case of B30 films, wrinkles continue to be generated at a stretching ratio of 30%, but no cracks are observed. The C30 films' stretchability is optimal at the stretching ratios of 30% and 50%. No cracks or wrinkles are observed on the C30 films. Therefore, from the optical microscopy diagram of these dielectric hybrid films, the addition of Jeffamine D2000 and polyurethane polymers is seen to increase the film stretchability and the addition of polyurethane produces tensile properties superior to those obtained from the addition of Jeffamine D2000.

**Figure 3.** Optical microscopy images of (**a**) A0, B0, and C0 and of (**b**) A30, B30, and C30 thin films subject to various strain levels. **Figure 3.** Optical microscopy images of (**a**) A0, B0, and C0 and of (**b**) A30, B30, and C30 thin films subject to various strain levels.

The surface flatness of the hybrid dielectric film s was measured using an atomic force microscope (AFM). The AFM result demonstrates that the surface roughness (Ra) of the three series of A0–A40, B0–B40, and C0–C40 are 0.44–0.75, 0.31–0.64, and 0.43–0.69 nm, respectively. Ra increases

*3.3. Analysis of Surface Morphology and Surface Energy*

#### *3.3. Analysis of Surface Morphology and Surface Energy*

The surface flatness of the hybrid dielectric film s was measured using an atomic force microscope (AFM). The AFM result demonstrates that the surface roughness (Ra) of the three series of A0–A40, B0–B40, and C0–C40 are 0.44–0.75, 0.31–0.64, and 0.43–0.69 nm, respectively. Ra increases with the increase in TiO2-SiO<sup>2</sup> content. However, all hybrid dielectric films were produced without pinholes, and the surface flatness (the ratio of Ra to film thickness, Ra/h) for all hybrid films was less than 0.35% (Table 1), indicating that all prepared hybrid dielectric films in this study had a good surface flatness. In the previous studies, it has been confirmed that, when the ratio of surface roughness to thickness is less than 0.5%, the material has a good flatness. The prepared dielectric thin film in this study has a better surface flatness than those of studies in literature [39,42,43]. According to the aforementioned results, the three series of hybrid dielectric films have good light transmission, thermal stability, and surface flatness, and no phase separation was observed. Therefore, the prepared hybrid dielectric films can be effectively applied as the gate dielectric materials for the OTFT application.

Typically, thin films show a light scattering behavior due to the surfaces roughness. An innovative hybrid thin film with a lower-than-usual surface roughness can reduce the light loss on the waveguide surface. This result also confirms the potential for the use of polyimide-TiO2-SiO<sup>2</sup> hybrid material in OTFT as the dielectric film. The surface flatness of the dielectric layer greatly influences the characteristics of the OTFT. When the dielectric layer has a low surface roughness, it effectively reduces the leakage current of OTFT and promotes the order growth of crystals in the active layer. Figure 4 shows the AFM images of the semiconductor layer (BffBT4T-2OD) coated on the various dielectric composite films, namely A0, B0, C0, A30, B30, and C30. This indicates that island-like aggregation was produced from the BffBT4T-2OD on the semiconductor layer (A30) after the addition of the inorganic nanoparticles, and the degree of aggregation became more obvious after the addition of the Jeffamine D2000 (B30) and polyurethane (C30). These dense aggregates of BffBT4T-2OD can help to increase the tensile properties of these composite films and the stretchability of OTFT [41]. BffBT4T-2OD is hydrophobic in nature, and we observed B30 to have lower surface energy (42.07 mJ·m−<sup>2</sup> ) than A30 and C30 did, which enables the growth of BffBT4T-2OD. As the adding ratio of the TiO2-SiO<sup>2</sup> nanoparticles increases, the size of BffBT4T-2OD crystal grains in the semiconductor layer also increases, resulting in better characteristics for the OTFT. This may be related to the affinity of the dielectric surface for BffBT4T-2OD. As the TiO2-SiO<sup>2</sup> content increases from 0% (A0) to 30 wt.% (A30), the surface energy of the dielectric layer decreases, which causes the grain size of BffBT4T-2OD in semiconductor layer to increase. The well-connected domain of the A30 provides an efficient channel for charge transport and increases the charge carrier density at the interface between dielectric and semiconductor, which can prevent the charge defects from occurring at the interface and improve the performance of the OTFTs [38–40].

The contact angles of the gate dielectric films were measured using deionized water and diiodomethane as the test drops, respectively, due to their different polarities. The surface energies of the polyimide-TiO2-SiO<sup>2</sup> hybrid films could then be calculated from the values of the contact angles obtained from water and diiodomethane drops, respectively. The results are listed in Table 2. If the surface of a hybrid film has a small water contact angle, this indicates that the surface is hydrophilic and has a large surface energy. Conversely, a large water contact angle indicates that the surface is hydrophobic and has a low surface energy. As shown in Table 2, whether water or diiodomethane is used as the test drop, the contact angles for the hybrid films (A, B, and C) increase first and then decrease with the addition of inorganic particles. For A0–A40 hybrid films, the water contact angles increase from 79.78 for A0 to 83.99 for A30 and then decrease to 78.30 for A40.

semiconductor chains.

**Figure 4.** Tapping-mode AFM (1 × 1 μm) images (left: topographic images, right: phase images) of blend films deposited with various TiO2-SiO2 ratios and addition of Jeffamine D2000 or polyurethane; (**a**) A0, (**b**) B0, (**c**) C0, (**d**) A30, (**e**) B30, and (**f**) C30. **Figure 4.** Tapping-mode AFM (1 × 1 µm) images (left: topographic images, right: phase images) of blend films deposited with various TiO<sup>2</sup> -SiO<sup>2</sup> ratios and addition of Jeffamine D2000 or polyurethane; (**a**) A0, (**b**) B0, (**c**) C0, (**d**) A30, (**e**) B30, and (**f**) C30.


The contact angles of the gate dielectric films were measured using deionized water and **Table 2.** Summary of dielectric constant and surface energy for various hybrid dielectric films.

the addition of high dielectric TiO2-SiO2 in a low dielectric PI matrix can change the surface roughness of the PI/TiO2-SiO2 hybrid film, which in turn affects the surface energy of the hybrid film. In addition, due to the inherent hydrophobic nature of the polymer, the addition of Jeffamine D2000 and polyurethane additives can produce a highly hydrophobic surface, which further reduces the surface energy. The results show that the lowest surface energy obtained from B30 is 42.07 mJ·m−2 [31]. Typically, dielectric surfaces with low surface energy can provide a venue for the growth of organic The increase in water contact angle is mainly due to the change in surface roughness of hybrid films. In addition, the PI/SiO2-TiO<sup>2</sup> hybrid films in this study have a polarizable and weakly hydrophobic surface, resulting in this dielectric layer having a low surface energy. This is a very important property for wetting of the latter deposited organic semiconductor layer, and can improve the performance of the device [44]. Therefore, when 30 wt.% of TiO2-SiO<sup>2</sup> was added, the surface energy of the hybrid film was lowered from 51.02 mJ·m−<sup>2</sup> (A0) to 44.17 mJ·m−<sup>2</sup> (A30), indicating that the addition of high

energy of the hybrid film was lowered from 51.02 mJ·m−2 (A0) to 44.17 mJ·m−2 (A30), indicating that

dielectric TiO2-SiO<sup>2</sup> in a low dielectric PI matrix can change the surface roughness of the PI/TiO2-SiO<sup>2</sup> hybrid film, which in turn affects the surface energy of the hybrid film. In addition, due to the inherent hydrophobic nature of the polymer, the addition of Jeffamine D2000 and polyurethane additives can produce a highly hydrophobic surface, which further reduces the surface energy. The results show that the lowest surface energy obtained from B30 is 42.07 mJ·m−<sup>2</sup> [31]. Typically, dielectric surfaces with low surface energy can provide a venue for the growth of organic semiconductor chains.

#### *3.4. Analysis of Electrical Properties*

The result of volumetric capacity measurement shows that the capacitance (at 1 kHz–1 MHz) increases as the TiO2-SiO<sup>2</sup> ratio increases, and the relationship is linear. At lower frequencies, the capacitance may increase slightly due to the increased response time available for polarization. The dielectric constant (k) is evaluated using the following equation:

$$\mathbf{C} = \frac{\mathbf{k}\varepsilon\_0 \mathbf{A}}{\mathbf{d}} \tag{1}$$

where C is the measured capacitance, ε<sup>0</sup> is the vacuum dielectric constant, A is the area of the capacitor, and d is the thickness of the dielectric layer. As shown in Table 2, the dielectric constants obtained at 1 kHz were 4.53 for A0, 9.51 for A40, 4.47 for B0, 8.58 for B40, 4.22 for A0, and 7.87 for A40. When a higher concentration of TiO2-SiO<sup>2</sup> was used in a film's fabrication, its dielectric constant was higher. Moreover, the electrical data of OTFTs fabricated by various hybrid dielectrics are shown in Table 3. The results show that the values of mobility (µ) and switch current ratio (on-off current ratios, Ion-Ioff) increase with increasing the TiO2-SiO<sup>2</sup> content. Moreover, the leakage current density (LCD) measured at <sup>−</sup>2 MV·cm−<sup>1</sup> also increases as the content of TiO2-SiO<sup>2</sup> nanoparticles increases. Figure S3. shows the transfer curves of OTFTs prepared by different dielectric materials, A0, A30, B30, and C30. This indicates that the mobility and Ion/Ioff of the device prepared by the polyimide dielectric layer without TiO2-SiO<sup>2</sup> nanoparticles (A0) are 0.0181 cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 1.13 <sup>×</sup> <sup>10</sup><sup>3</sup> , respectively. When the PI/TiO2-SiO<sup>2</sup> hybrid material (A30) was used as a dielectric layer, the mobility and Ion/Ioff of device increased to 0.242 cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 9.04 <sup>×</sup> <sup>10</sup><sup>3</sup> . When adding Jeffamine D2000 (B30) and polyurethane (C30) additives into the dielectric layer, the mobility and Ion/Ioff were further increased to 0.817 cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 4.27 <sup>×</sup> <sup>10</sup><sup>5</sup> for B30 and 0.562 cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 2.04 <sup>×</sup> <sup>10</sup><sup>5</sup> for C30, respectively, which shows that the proper amount of TiO2-SiO<sup>2</sup> nanoparticles and additives can effectively improve the device performance. The larger the Ion/Ioff ratio, the better the switch characteristics of OTFTs. It is known that high-k dielectric layer could cause a low operation voltage and low power consumption. The LCD value is related to the thickness of the hybrid dielectric layer and the pinholes density, because the chemical bonding between the inorganic and polyimide can make the dielectric layer structure more dense, and the high-k dielectric can improve the capacitive coupling effect between the gate and active channel layer, which can increase the driving current and reduce the operating voltage. In addition, the surface morphology of the dielectric layer affects the structure of the deposited organic semiconductor layer, which in turn affects the performance of the device. A smooth and pinhole-free surface of dielectric layer is important for the interfacial connection during the deposition of organic semiconductor layers, because a smooth interface reduces the charge scattering sites in the channel. Reducing the current leakage from the dielectric interface has a great influence on the electrical performance of the OTFTs. For high-performance OTFTs, the gate dielectric should have a low LCD and a high-k, which can provide greater surface charge accumulation and simultaneously reduce the operating voltage. It should be noted that the thickness of the dielectric layer must be carefully controlled to minimize the current leakage without greatly reducing the capacitance [44]. An increase in the LCD value means that the effect of the insulating layer is reduced. As shown in Table 3, the LCD values of all dielectric layers were less than 10−<sup>8</sup> <sup>A</sup>·cm−<sup>2</sup> . Therefore, these hybrid dielectric layers are suitable for OTFT applications. The gate-current behavior is usually similar to the capacitor leakage current. In this work, we used a metal-insulator-metal capacitor to study the

dielectric leakage current. Moreover, as the surface energy decreases, the particle size and alignment of the semiconductor layer become denser, and the carrier mobility of the OTFT increases. Namely, more hydrophobic material increases the carrier mobility of the OTFT. Therefore, the increase in inorganic content helps to form a good organic polymer film, reducing the structural defects in the film and increasing compactness, thus improving carrier mobility. However, the device mobility decreases when the TiO2-SiO<sup>2</sup> content is more than 30 wt.%, which may be attributed to the coarser surface and the aggregation of the TiO2-SiO<sup>2</sup> particles, disturbing the formation of BffBT4T-2OD crystal structure in the semiconductor layer. Supplementary Figure S4 shows the output characteristics of the OTFTs using (a) (A0), (b) A30, (c) B30 and (d) C30 as the dielectric layer, respectively. The threshold voltages (Vt) of OTFTs based on hybrid films are small, so only a small gate voltage is needed to turn on the gate. Surface polarization may result in smaller threshold voltages, which can lead to the filling defects of local carrier. Most of the V<sup>t</sup> displacement is affected by three factors, which are the charge defect trapping, surface polarization, and ions. In this study, the variation of V<sup>t</sup> displacement might be attributed to the addition of different proportions of inorganic nanoparticles at the interface between the dielectric and the semiconductor layers [45,46].


**Table 3.** The electrical data of OTFTs fabricated by various hybrid dielectrics.

Figure 5a shows the mobility values of A0, B0,C0, A30, B30, and C30 at various strain values. These results prove that devices with Jeffamine D2000 (B0, B30) and polyurethane (C0, C30) as additives can be stretched to 20% and 50%, respectively. Figure 5b shows the mobility of A0, B0, C0, A30, B30, and C30 at various stretch cycles, indicating that the devices with Jeffamine D2000 (B0, B30) and polyurethane (C0, C30) as additives can be stretched up to 150. The aforementioned results show that the devices with polyurethane additive can achieve superior stretching properties of 50% for stretching 150 cycles. The mobility has almost no change, which is because the polyurethane additive is a softer chain polymer. AFM analysis revealed that the hybrid films with polyurethane always exhibit a denser and more concentrated film structure that is advantageous for the stretching propertes of the stretchable devices. In addition, the devices with Jeffamine D2000 can also achieve a good stretching properties of 50% for stretching 150 cycles. Although the mobility is reduced by approximately 10%. However, the A0 and A30 samples without added any additives have a significant problem in that the mobility decreases sharply and does not have stretchability.

significant problem in that the mobility decreases sharply and does not have stretchability.

Figure 5a shows the mobility values of A0, B0,C0, A30, B30, and C30 at various strain values. These results prove that devices with Jeffamine D2000 (B0, B30) and polyurethane (C0, C30) as additives can be stretched to 20% and 50%, respectively. Figure 5b shows the mobility of A0, B0, C0, A30, B30, and C30 at various stretch cycles, indicating that the devices with Jeffamine D2000 (B0, B30) and polyurethane (C0, C30) as additives can be stretched up to 150. The aforementioned results show that the devices with polyurethane additive can achieve superior stretching properties of 50% for stretching 150 cycles. The mobility has almost no change,which is because the polyurethane additive is a softer chain polymer. AFM analysis revealed that the hybrid films with polyurethane always exhibit a denser and more concentrated film structure that is advantageous for the stretching propertes of the stretchable devices. In addition, the devices with Jeffamine D2000 can also achieve a good stretching properties of 50% for stretching 150 cycles. Although the mobility is reduced by

**Figure 5.** (**a**) mobility of the strained percentage, (**b**) the strained cycles and (**c**) leakage characteristics of hybrid thin films. **Figure 5.** (**a**) mobility of the strained percentage, (**b**) the strained cycles and (**c**) leakage characteristics of hybrid thin films.

Finally, we applied three series of dielectric materials (A, B, C) in the OTFT device as gate materials. Table 3 summarizes the electrical characteristics of these OTFTs, including the LCD, mobility, and Ion-Ioff. As mentioned, the electrical properties of the fabricated OTFT devices are identical to those obtained using AFM and surface energy. In the upstretched case, the LCD becomes larger with the increase in the content of TiO2-SiO2 inorganic nanoparticles, but the LCD value is less than 10−8 A·cm−2 (−2 MV·cm−1) (Figure 5c). The addition of Jeffamine D2000 and polyurethane additives reduces the LCD values. The mobility and Ion-Ioff of the dielectric layers of pure polyimide without inorganic nanoparticles and polymer additives (A0, B0, and C0) are 1.81 × 10−2 cm2·V−1·s−1 and 1.13 × 103 for A0, 5.04 × 10−2 cm2·V−1·s−1 and 1.51× 104 for B0, and 4.81 × 10−2 cm2·V−1·s−1 and 8.13 × 103 for C0, respectively. The mobility and Ion-Ioff increase obviously with the content of TiO2-SiO2 inorganic nanoparticles. The mobility and Ion-Ioff of A30 hybrid film reach 2.42 × 10−1 cm2·V−1·s−1 and 9.04 × 103, respectively. Moreover, after the addition of Jeffamine D2000 (B30) and polyurethane (C30), the mobility and Ion-Ioff improve to 8.17 × 10−1 cm2·V−1·s−1 and 4.27 × 105, respectively, for B30 and to 5.62 ×10−1 cm2·V−1·s−1 and 2.04 × 105, respectively, for C30. However, when the content of SiO2-TiO2 increases Finally, we applied three series of dielectric materials (A, B, C) in the OTFT device as gate materials. Table 3 summarizes the electrical characteristics of these OTFTs, including the LCD, mobility, and Ion-Ioff. As mentioned, the electrical properties of the fabricated OTFT devices are identical to those obtained using AFM and surface energy. In the upstretched case, the LCD becomes larger with the increase in the content of TiO2-SiO<sup>2</sup> inorganic nanoparticles, but the LCD value is less than <sup>10</sup>−<sup>8</sup> <sup>A</sup>·cm−<sup>2</sup> (−2 MV·cm−<sup>1</sup> ) (Figure 5c). The addition of Jeffamine D2000 and polyurethane additives reduces the LCD values. The mobility and Ion-Ioff of the dielectric layers of pure polyimide without inorganic nanoparticles and polymer additives (A0, B0, and C0) are 1.81 <sup>×</sup> <sup>10</sup>−<sup>2</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 1.13 <sup>×</sup> <sup>10</sup><sup>3</sup> for A0, 5.04 <sup>×</sup> <sup>10</sup>−<sup>2</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 1.51 <sup>×</sup> <sup>10</sup><sup>4</sup> for B0, and 4.81 <sup>×</sup> <sup>10</sup>−<sup>2</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 8.13 <sup>×</sup> <sup>10</sup><sup>3</sup> for C0, respectively. The mobility and Ion-Ioff increase obviously with the content of TiO2-SiO<sup>2</sup> inorganic nanoparticles. The mobility and Ion-Ioff of A30 hybrid film reach 2.42 <sup>×</sup> <sup>10</sup>−<sup>1</sup> cm<sup>2</sup> ·V −1 ·s −1 and 9.04 <sup>×</sup> <sup>10</sup><sup>3</sup> , respectively. Moreover, after the addition of Jeffamine D2000 (B30) and polyurethane (C30), the mobility and Ion-Ioff improve to 8.17 <sup>×</sup> <sup>10</sup>−<sup>1</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 4.27 <sup>×</sup> <sup>10</sup><sup>5</sup> , respectively, for B30 and to 5.62 <sup>×</sup> <sup>10</sup>−<sup>1</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 2.04 <sup>×</sup> <sup>10</sup><sup>5</sup> , respectively, for C30. However, when the content of SiO2-TiO<sup>2</sup> increases to 40 wt.% (A40, B40, and C40), the mobility and switching current ratio decrease to 1.07 <sup>×</sup> <sup>10</sup>−<sup>2</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 1.16 <sup>×</sup> <sup>10</sup><sup>3</sup> , respectively, for A40 and to 5.51 <sup>×</sup> <sup>10</sup>−<sup>1</sup> cm<sup>2</sup> ·V −1 ·s −1 , and 8.50 <sup>×</sup> <sup>10</sup><sup>4</sup> , respectively, for B40, and to 2.07 <sup>×</sup> <sup>10</sup>−<sup>1</sup> cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 2.16 <sup>×</sup> <sup>10</sup><sup>3</sup> , respectively, for C40.

The decreases in mobility and switching current ratio are attributed to the phase separation of the mixed solution when the content of inorganic particles of TiO2-SiO<sup>2</sup> is too high. The results show that the use of TiO2-SiO<sup>2</sup> inorganic nanoparticles and Jeffamine D2000 and polyurethane additives can improve the mobility and Ion-Ioff. However, when the content of TiO2-SiO<sup>2</sup> inorganic nanoparticles reaches 40 wt.%, precipitation and subsequent phase separation occurs in the precursor solution, resulting in poor film properties and thus poor electrical properties for A40, B40, and C40 samples. Therefore, the optimal mass ratio of polyimide and TiO2-SiO<sup>2</sup> inorganic nanoparticles is 70:30 wt.%. The aforementioned results demonstrate that the content of TiO2-SiO<sup>2</sup> nanoparticles exert an obvious influence on the electrical performance of OTFTs. In summary, the mobility and current-switching ratio

of B30- and C30-based OTFT after being stretched 150 cycles at 50% of strain are 0.29 cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 8.17 <sup>×</sup> <sup>10</sup><sup>4</sup> for B30-based OTFT and 0.38 cm<sup>2</sup> ·V −1 ·s <sup>−</sup><sup>1</sup> and 1.34 <sup>×</sup> <sup>10</sup><sup>5</sup> for C30-based OTFT, respectively, which is higher than those obtained from other hybrid dielectrics-based devices. These results show that Jeffamine D2000 additives (B30) and polyurethane additives (C30) improve the properties of stretchable OTFE devices, of which C30 exerts the better effect. This result is consistent with the optical microscopy result of the tensile test for the hybrid dielectric films.
