Facile Fabrication of N-Type Flexible CoSb3-xTex Skutterudite/PEDOT:PSS Hybrid Thermoelectric Films

Alongiside the growing demand for wearable and implantable electronics, the development of flexible thermoelectric (FTE) materials holds great promise and has recently become a highly necessitated and efficient method for converting heat to electricity. Conductive polymers were widely used in previous research; however, n-type polymers suffer from instability compared to the p-type polymers, which results in a deficiency in the n-type TE leg for FTE devices. The development of the n-type FTE is still at a relatively early stage with limited applicable materials, insufficient conversion efficiency, and issues such as an undesirably high cost or toxic element consumption. In this work, as a prototype, a flexible n-type rare-earth free skutterudite (CoSb3)/poly(3,4-ethylenedioxythiophene)-polystyrene sulfonate (PEDOT:PSS) binary thermoelectric film was fabricated based on ball-milled skutterudite via a facile top-down method, which is promising to be widely applicable to the hybridization of conventional bulk TE materials. The polymers bridge the separated thermoelectric particles and provide a conducting pathway for carriers, leading to an enhancement in electrical conductivity and a competitive Seebeck coefficient. The current work proposes a rational design towards FTE devices and provides a perspective for the exploration of conventional thermoelectric materials for wearable electronics.


Introduction
Out of the primary energy sources such as feedstocks, oil, natural gas, etc., there has been an increasing demand for the development of renewable and sustainable sources of energy [1][2][3]. Heat conversion via thermoelectric (TE) devices represents a promising avenue for generating electricity and clean energy in a renewable and sustainable way for future energy development [4][5][6]. Various ongoing efforts in experiments and theories have been attempting to improve the TE properties and conversion efficiency of relevant materials [7][8][9][10]. The efficiency of TE materials is described by a dimensionless figure of merit ZT = S 2 σTκ −1 , where S represents the Seebeck coefficient, σ represents electrical conductivity, κ represents thermal conductivity, and T represents absolute temperature. To improve the figure of merit, the majority of recent research is focused on two aspects: the enhancement of the power factor (S 2 σ) [11][12][13][14][15][16][17] and the reduction in thermal conductivity κ [18][19][20][21][22][23][24][25][26][27].
In recent years, a variety of novel flexible electronic devices, ranging from wearable smart electronics to printable circuit boards, have steadily been developed in line with the concept of the Internet of things (IoT) society [28,29]. The growing demand for wearable and implantable electronics and sensors that use body heat advances the development of flexible thermoelectric (FTE) devices [30][31][32][33][34][35]. Polymers are one of the promising candidates for FTE conversion materials. Most of the advances achieved in FTE materials so far have been focused on conductive polymer-based TE materials. Typical conductive polymers including Polyaniline (PANI) [36], poly (3,4-ethylenedioxythiophene) (PEDOT) [37], Polypyrrole (PPy) [38], etc., show p-type TE performance. Benzodifurandione-based polyphenylene vinylene (BDPPV) [39] and poly(nickel-1,1,2,2-ethenetetrathiolate) (poly(Kx(Ni-ett)) [40] as conductive polymers exhibit n-type TE performance. However, the n-type conductive polymers have a lower TE performance and stability in air compared to p-type polymers due to their unstable dopants [33]. Therefore, p-type polymers are still the mainstream in current FTE development. Among the various polymers, poly (3,4-ethylenedioxythiophene) polystyrene sulfonate (PEDOT:PSS) stands out in particular because of its high electrical conductivity of up to 4839 S/cm [41], and the possibility of further increasing its TE property via post-treatment with acids or reducing agents [42,43]. Despite its high electrical conductivity and flexibility to be easily tailored into various shapes, the Seebeck coefficient of PEDOT:PSS has remained limited with a value lying in the 10.35-67 µV/K range [41,44], which is far from satisfactory when compared to conventional inorganic TE materials. To overcome the rigidity of the conventional inorganic TE materials and the low performance of polymers, the polymers and inorganic TE materials have been hybridized into an assembly.
Various methods have been conducted to build a hybrid composed of inorganic TE materials and polymers. For example, polyethyleneimine (PEI) has been used as a dopant in carbon nanotube yarn (CNTY) by donating electrons to fabricate an n-type FTE film [45]. Furthermore, depositing the specific n-type inorganic TE materials on flexible substrates such as nylon and/or PI substrates by suction filtration [46] or magnetron sputtering [47] could also effectively provide flexibility comparable to that of organic materials. However, TE materials that exhibit high performance usually contain relatively expensive and rare elements such as Ag and Te, or toxic elements such as Se. In addition, to produce uniform films, most inorganic materials are synthesized into nanoparticles using chemical processing, but the number of inorganic materials that can be obtained using the same method is limited. Recently, the hybridized FTE films between the ballmilled chalcopyrite (Cu x Zn 1-x FeS 2 ) and PEDOT:PSS on the polytetrafluoroethylene (PTFE) membrane have been reported and exhibit outstanding flexibility and performance [48]. This versatile and promising approach to obtaining FTE film could be extended to various inorganic TE materials that present natively attractive TE performance.
Skutterudite, with a general formula of CoSb 3 , is another family of promising TE candidates which shows high TE performance in the medium to high-temperature range due to its high electrical conductivity [49]. By doping CoSb 3 with Te to form a ternary solid solution alloy, Te provides electrons as a donor, and the electrical conductivity increases rapidly due to the increase in the carrier concentration [50]. Since CoSb 3-x Te x has been mainly studied as a bulk TE material, the study of CoSb 3-x Te x as an FTE film will provide new insights and is expected to broaden the selection of inorganic materials used in the development of FTE materials in the future.
In this study, an n-type flexible CoSb 3-x Te x /PEDOT:PSS TE film was produced using a facile method. CoSb 3-x Te x ingots were prepared using a top-down method by breaking down the size of the bulk counterpart via ball-milling that does not require chemical treatment, and the powder was mechanically mixed with PEDOT:PSS, followed by suction filtering onto a membrane. The TE properties (electric conductivity, Seebeck coefficient, power factor, etc.) with different compositions and Te doping of the hybrid films were evaluated and discussed, which demonstrated the potential for CoSb 3-x Te x to be developed into an FTE component.

Preparation of CoSb 3-x Te x Skutterudite
CoSb 3-x Te x (x = 0.05, 0.10, 0.15) was synthesized by a solid-state reaction. Co pieces, Sb grains, and Te grains were well-mixed in a stoichiometric ratio and added into quartz tubes that were subsequently sealed under vacuum conditions (1 × 10 −3 mbar). The tubes were put into a muffle furnace, which was heated to 1423 K with a ramping rate of 0.8 K/min and kept for 24 h. The samples were quenched in water and annealed at 873 K for 96 h. The as-prepared ingot samples were ground with a mortar to obtain the powder, and the powder was ball-milled for 1 h by the 8000D Mixer/Mill.

Fabrication of the CoSb 3-x Te x Skutterudite/PEDOT:PSS Composite Films
The fabrication process for the CoSb 3-x Te x skutterudite/PEDOT:PSS film is shown in Scheme 1. An aqueous solution of PEDOT:PSS and 5 vol% DMSO was mixed for 2 h using a stirrer, and the mixture was filtered through a polyvinylidene difluoride (PVDF) syringe filter (0.45 µm). Subsequently, the ball-milled CoSb 3-x Te x powders were added to ethanol and sonicated for 30 min. A CoSb 3-x Te x dispersion with various skutterudite contents (20,40,60,70,80,85,90,95,97, and 98 wt%) was added to the PEDOT:PSS/DMSO solution and sonicated for 30 min. The mixture was vacuum-filtrated with an MCE membrane filter. After the film was dried in a vacuum oven at 60 • C for 10 h, the film was cold-pressed for 5 min at 20MPa. All of the TE properties were measured using MCE membrane-based hybrid films.

Preparation of CoSb3-xTex Skutterudite
CoSb3-xTex (x = 0.05, 0.10, 0.15) was synthesized by a solid-state reaction. Co pieces, Sb grains, and Te grains were well-mixed in a stoichiometric ratio and added into quartz tubes that were subsequently sealed under vacuum conditions (1 × 10 −3 mbar). The tubes were put into a muffle furnace, which was heated to 1423 K with a ramping rate of 0.8 K/min and kept for 24 h. The samples were quenched in water and annealed at 873 K for 96 h. The as-prepared ingot samples were ground with a mortar to obtain the powder, and the powder was ball-milled for 1 h by the 8000D Mixer/Mill.

Fabrication of the CoSb3-xTex Skutterudite/PEDOT:PSS Composite Films
The fabrication process for the CoSb3-xTex skutterudite/PEDOT:PSS film is shown in Scheme 1. An aqueous solution of PEDOT:PSS and 5 vol% DMSO was mixed for 2 h using a stirrer, and the mixture was filtered through a polyvinylidene difluoride (PVDF) syringe filter (0.45 µ m). Subsequently, the ball-milled CoSb3-xTex powders were added to ethanol and sonicated for 30 min. A CoSb3-xTex dispersion with various skutterudite contents (20,40,60,70,80,85,90,95,97, and 98 wt%) was added to the PEDOT:PSS/DMSO solution and sonicated for 30 min. The mixture was vacuum-filtrated with an MCE membrane filter. After the film was dried in a vacuum oven at 60 °C for 10 h, the film was cold-pressed for 5 min at 20MPa. All of the TE properties were measured using MCE membrane-based hybrid films.

Characterization
The morphology and elemental mapping was obtained from a field-emission scanning electron microscope (FE-SEM, Hitachi S-4800, Tokyo, Japan) with an energy-dispersive X-ray spectrometer (EDX, Horiba EMAX Evolution X-Max 80, Kyoto, Japan). In the SEM observation, a small piece of as-prepared film was pasted onto the SEM stage with carbon conductive tape. The accelerating voltage was 10.0 kV. The phase structural information was acquired from the X-ray diffractometer (Smart Lab3, Rigaku Co., Tokyo, Japan) with Cu Kα radiation (λ = 0.154 nm). The measurement was conducted under a voltage of 40 kV and a current of 40 mA (scan speed: 3°/min; scan step: 0.02°) in the Theta-2 Theta geometry. X-ray powder diffraction patterns were refined via Rietveld analysis

Characterization
The morphology and elemental mapping was obtained from a field-emission scanning electron microscope (FE-SEM, Hitachi S-4800, Tokyo, Japan) with an energy-dispersive X-ray spectrometer (EDX, Horiba EMAX Evolution X-Max 80, Kyoto, Japan). In the SEM observation, a small piece of as-prepared film was pasted onto the SEM stage with carbon conductive tape. The accelerating voltage was 10.0 kV. The phase structural information was acquired from the X-ray diffractometer (Smart Lab3, Rigaku Co., Tokyo, Japan) with Cu Kα radiation (λ = 0.154 nm). The measurement was conducted under a voltage of 40 kV and a current of 40 mA (scan speed: 3 • /min; scan step: 0.02 • ) in the Theta-2 Theta geometry. X-ray powder diffraction patterns were refined via Rietveld analysis using the FullProf and WinPLOTR software packages [51,52]. The shape of the diffraction peaks was modeled using a pseudo-Voigt profile function. Zero-point shift, asymmetry parameters, and lattice parameters were systematically refined, and the background contribution was manually estimated. The structure of the organic compounds was characterized by Fourier transform infrared spectroscopy (FT-IR, IRAffinity-1S, Shimadzu, Kyoto, Japan). Thermogravimetric analysis (TGA) was conducted using an STA449 F1 Jupiter (NETZSCH, Selb, Germany) at a heating rate of 10 K/min under a N 2 atmosphere. The calibration was performed with an empty aluminum crucible. The evaluation of the thermoelectric properties including the electrical conductivity (σ), the Seebeck coefficient (S), and the power factor (PF) was carried out on a ZEM-3 (Advance Riko, Yokohama, Japan). The measurement was performed in a standard four-probe configuration under a partial helium atmosphere (0.1 MPa) at RT. Figure S1a shows the morphology of the representative as-synthesized CoSb 2.95 Te 0.05 powder with the corresponding EDX spectrum presenting the elemental Co, Sb, and Te distribution in Figure S1b. The corresponding XRD patterns of the as-synthesized CoSb 3-x Te x powders with different amounts of Te dopants are shown in Figure S2. The ballmilled powder is consistent with the CoSb 3 composition, which confirms the purity of the CoSb 2.95 Te 0.05 prepared in this study. All the patterns can be indexed to the skutterudite structure (JCPDS no.01-083-0055) with a space group of Im-3 (No.204). The Rietveld refinement results are summarized in Table S1 and exhibit low-reliability factors demonstrating evidence of how the CoSb 3 structure purity is exempt from structural defects. Moreover, the lattice size varied linearly with the Te content attesting to the successful substitution of the Sb by the Te within the structure. Figure 1 shows the morphology and microstructural information of the CoSb 2.95 Te 0.05 /PEDOT:PSS hybrid film. According to the digital photo image of the 98 wt% CoSb 2.95 Te 0.05 /PEDOT:PSS hybrid film shown in Figure 1a, the color of the hybrid film is black, similar to the color of CoSb 2.95 Te 0.05 powder. As displayed in Figure 1b Figure 1i, the uniform distribution of the elements Co, Sb, and Te, which constitute CoSb 2.95 Te 0.05 , and the C, O, and S contained in PEDOT:PSS reveal how the TE materials and PEDOT:PSS are evenly dispersed within each other. The cross-sectional image in Figure 1k indicates that the typical film in our experiment has a thickness of 53.0 ± 7 µm.

Results and Discussion
According to the TGA results shown in Figure 2a, even in the hybrid film with 98 wt% CoSb 2.95 Te 0.05 where the ratio of the PEDOT:PSS is extremely small, it is evident that a mass loss occurrs corresponding to the decomposition of the PEDOT:PSS when increasing the measurement temperature, confirming the successful assembly of the PEDOT:PSS and the CoSb 2.95 Te 0.05 powders . Figure 2b shows the FT-IR spectra of the CoSb 2.95 Te 0.05 /PEDOT:PSS hybrid films. It is known that PEDOT:PSS has several distinct absorption bands between 800 cm −1 and 1600 cm −1 [53,54], and a similar spectrum was observed for the PEDOT:PSS used in this study. As the amount of CoSb 2.95 Te 0.05 increases, the signature peaks of PEDOT:PSS are weakened, but the peak position of C-S at wavenumber 977 cm −1 and S-O at wavenumber 1141 cm −1 are not shifted, indicating that the structure of the PEDOT:PSS has not changed. According to the TGA results shown in Figure 2a, even in the hybrid film with 98 wt% CoSb2.95Te0.05 where the ratio of the PEDOT:PSS is extremely small, it is evident that a mass loss occurrs corresponding to the decomposition of the PEDOT:PSS when increasing the measurement temperature, confirming the successful assembly of the PEDOT:PSS and the CoSb2.95Te0.05 powders. Figure 2b shows the FT-IR spectra of the CoSb2.95Te0.05/PE-DOT:PSS hybrid films. It is known that PEDOT:PSS has several distinct absorption bands between 800 cm −1 and 1600 cm −1 [53,54], and a similar spectrum was observed for the PE-DOT:PSS used in this study. As the amount of CoSb2.95Te0.05 increases, the signature peaks of PEDOT:PSS are weakened, but the peak position of C-S at wavenumber 977 cm −1 and S-O at wavenumber 1141 cm −1 are not shifted, indicating that the structure of the PE-DOT:PSS has not changed. The properties of the hybrid films in Figure 3 containing a lower content (<95 wt%) of CoSb2.95Te0.05 show much lower TE properties than the hybrid films containing a CoSb2.95Te0.05 content above 95 wt%. Our experiments in the later section are mainly focused on the hybrid films with the CoSb3-xTex weight fraction over 95 wt%. The XRD patterns of the hybrid films with 95 wt%, 97 wt%, and 98 wt% of CoSb2.95Te0.05 are shown here in Figure 2c, which are very consistent with the XRD patterns of the original powders in Figure S2. The structure of CoSb2.95Te0.05 did not change, indicating that no mutual interference on the microstructure occurred between the CoSb2.95Te0.05 and the PEDOT:PSS dur- focused on the hybrid films with the CoSb 3-x Te x weight fraction over 95 wt%. The XRD patterns of the hybrid films with 95 wt%, 97 wt%, and 98 wt% of CoSb 2.95 Te 0.05 are shown here in Figure 2c, which are very consistent with the XRD patterns of the original powders in Figure S2. The structure of CoSb 2.95 Te 0.05 did not change, indicating that no mutual interference on the microstructure occurred between the CoSb 2.95 Te 0.05 and the PEDOT:PSS during the hybridization of the two materials. The lattice sizes of all the CoSb 2.95 Te 0.05 films are comparable to the reference powder, attesting to the non-degradation of the powder during the hybridization with PEDOT:PSS. The same trend was also observed when the doping concentration of CoSb 3-x Te x in the hybrid film was varied (Figure 2d). which only showed 0.031 S/cm as displayed in Table S2. The very low electrical conductivity can be attributed to the skutterudite particles aggregating in a random way to form a loose structure on the film where there is no effective bonding between the CoSb2.95Te0.05 particles ( Figure S3). While improving the amount of PEDOT:PSS to bridge the particles, the electrical conductivity shows a drastic upward trend. According to the previous method [55], we analyzed the composite method between CoSb2.95Te0.05 and PEDOT:PSS. As shown in Figure 3a, the red line is fitted in a parallel-connected model with S and σ as in the follow the Equation: where Sparallel and σparallel are the Seebeck coefficient and the electrical conductivity of the parallel-connected composite; Ss and Sp are the Seebeck coefficients of CoSb2.95Te0.05 and PEDOT:PSS, respectively; σs and σp are the electrical conductivities of CoSb2.95Te0.05 and PEDOT:PSS, respectively; and xs is the volume fraction of CoSb2.95Te0.05. The blue line is fitted in a series-connected model with S and σ as in the following equation: where Sseries and σseries are the Seebeck coefficient and the electrical conductivity of the series-connected composite, and κs and κp are the thermal conductivities of CoSb2.95Te0.05 and PEDOT:PSS, respectively. The experimental values of the Seebeck coefficient and electrical conductivity show properties closer to those of the series-connected model. To optimize the CoSb3-based FTE film, the doping level of the native inorganic powder was modulated to promote a larger negative Seebeck coefficient. Different doping ratios of CoSb3-xTex (x = 0.05, 0.10, 0.15) and of skutterudite hybridized with different mass ratios of X CoSb3-xTex/1-X PEDOT:PSS (X = 95, 97, 98 wt%) have been developed, and the influence on the FTE properties was investigated as shown in Figure 4. With the same fraction of skutterudite, the Seebeck coefficient of the hybrid film increases with a decreasing CoSb3-xTex doping ratio and obtained a largest negative value of −161.7 μV/K at 98 wt%, considering an uncertainty of 6% from the measurement [56]. This trend is also observed in the CoSb3-xTex bulk sample, where the Seebeck coefficient increases with a decreasing doping rate due to the charge carrier tuning (Table S3). In other words, a larger Seebeck coefficient in the native powder likely helps to reach a higher Seebeck coefficient in the hybrid FTE film. The contribution of CoSb3-xTex to the Seebeck coefficient is In order to fabricate the n-type film, it is necessary to increase the fraction of skutterudite to above 95 wt%. The electrical conductivity decreases gradually while increasing the amount of CoSb 3-x Te x powder. In comparison, the CoSb 2.95 Te 0.05 film was also fabricated using the same method for the hybrid film without the addition of PEDOT:PSS, which only showed 0.031 S/cm as displayed in Table S2. The very low electrical conductivity can be attributed to the skutterudite particles aggregating in a random way to form a loose structure on the film where there is no effective bonding between the CoSb 2.95 Te 0.05 particles ( Figure S3). While improving the amount of PEDOT:PSS to bridge the particles, the electrical conductivity shows a drastic upward trend. According to the previous method [55], we analyzed the composite method between CoSb 2.95 Te 0.05 and PEDOT:PSS. As shown in Figure 3a, the red line is fitted in a parallel-connected model with S and σ as in the follow the Equation: The blue line is fitted in a series-connected model with S and σ as in the following equation: where S series and σ series are the Seebeck coefficient and the electrical conductivity of the series-connected composite, and κ s and κ p are the thermal conductivities of CoSb 2.95 Te 0.05 and PEDOT:PSS, respectively. The experimental values of the Seebeck coefficient and electrical conductivity show properties closer to those of the series-connected model. To optimize the CoSb 3 -based FTE film, the doping level of the native inorganic powder was modulated to promote a larger negative Seebeck coefficient. Different doping ratios of CoSb 3-x Te x (x = 0.05, 0.10, 0.15) and of skutterudite hybridized with different mass ratios of X CoSb 3-x Te x /1-X PEDOT:PSS (X = 95, 97, 98 wt%) have been developed, and the influence on the FTE properties was investigated as shown in Figure 4. With the same fraction of skutterudite, the Seebeck coefficient of the hybrid film increases with a decreasing CoSb 3-x Te x doping ratio and obtained a largest negative value of −161.7 µV/K at 98 wt%, considering an uncertainty of 6% from the measurement [56]. This trend is also observed in the CoSb 3-x Te x bulk sample, where the Seebeck coefficient increases with a decreasing doping rate due to the charge carrier tuning (Table S3). In other words, a larger Seebeck coefficient in the native powder likely helps to reach a higher Seebeck coefficient in the hybrid FTE film. The contribution of CoSb 3-x Te x to the Seebeck coefficient is dominant in the n-type film with a high CoSb 3-x Te x content. However, there is only a small variation in the electrical conductivity of the hybrid film when decreasing the CoSb 3-x Te x doping ratio, and the electrical conductivity generates a different trend with the variation in the Te doping ratio in the CoSb 3-x Te x . The skutterudite grains of micrometer size synthesized under high vacuum are very stable with a negligible effect from the surface oxidation; this is thought to be due to the electrical conduction of the hybrid film being modulated by the interaction of the PEDOT:PSS and the bulk CoSb 3-x Te x particles. The electrical conductivity at various doping levels of Te showed a decreasing trend when the weight fraction increased from 90 wt% to 97 wt%. However, at 98 wt%, the electrical conductivity slightly increased compared to the 97 wt%, which might be due to the slightly larger compacity of CoSb 3-x Te x powders within the film. In addition, we compared the electrical conductivity with different doping levels at the same weight fraction. The CoSb 2.85 Te 0.15 /PEDOT:PSS film shows a much higher electrical conductivity than the CoSb 2.90 Te 0.10 /PEDOT:PSS and CoSb 2.95 Te 0.05 /PEDOT:PSS at 95 wt%, but it becomes the lowest at 98 wt%. At the same time, CoSb 2.95 Te 0.05 /PEDOT:PSS becomes the best hybrid film when improving the weight fraction above 97 wt%, while CoSb 2.85 Te 0.15 /PEDOT:PSS and CoSb 2.90 Te 0.10 /PEDOT:PSS generate similar electrical conductivities. The exact mechanism is quite complex but might be related to the drastic decrease of the carrier mobility with doped Te incremented as indicated previously in the reference. As a result, the hybrid film with the smallest doping ratio (x = 0.05) of Te, CoSb 2.95 Te 0.05 , at 98 wt% shows the largest power factor of 6.47 µW/m K 2 at room temperature. Table 1 shows the Seebeck coefficient, electrical conductivity, and power factor of the ntype flexible thermoelectric materials reported so far. In this study, CoSb 2.95 Te 0.05 /PEDOT:PSS hybrid film records the largest negative Seebeck coefficient value of −161.7 µV/K at ambient temperature. However, the electrical conductivity and the power factor are much lower compared to the previous work. We will improve our efforts in the future by downsizing the skutterudites and uniformizing the grain size. In addition, we measured the temperature-dependent TE properties of the 98wt% CoSb 2.95 Te 0.05 hybrid film as shown in Figure S4. Both the electrical conductivity and the absolute value of Seebeck coefficient increased with an increase in temperature. This is a typical metallic behavior dependence observed in Te-doped CoSb 3 , which agrees with a large carrier concentration and supports the idea that the inorganic component led the electrical transport properties rather than the organic component.
DOT:PSS film shows a much higher electrical conductivity than the CoSb2.90Te0.10/PE-DOT:PSS and CoSb2.95Te0.05/PEDOT:PSS at 95 wt%, but it becomes the lowest at 98 wt%. At the same time, CoSb2.95Te0.05/PEDOT:PSS becomes the best hybrid film when improving the weight fraction above 97 wt%, while CoSb2.85Te0.15/PEDOT:PSS and CoSb2.90Te0.10/PE-DOT:PSS generate similar electrical conductivities. The exact mechanism is quite complex but might be related to the drastic decrease of the carrier mobility with doped Te incremented as indicated previously in the reference. As a result, the hybrid film with the smallest doping ratio (x = 0.05) of Te, CoSb2.95Te0.05, at 98 wt% shows the largest power factor of 6.47 µ W/m K 2 at room temperature.  Table 1 shows the Seebeck coefficient, electrical conductivity, and power factor of the n-type flexible thermoelectric materials reported so far. In this study, CoSb2.95Te0.05/PE-DOT:PSS hybrid film records the largest negative Seebeck coefficient value of −161.7 µ V/K at ambient temperature. However, the electrical conductivity and the power factor are much lower compared to the previous work. We will improve our efforts in the future by downsizing the skutterudites and uniformizing the grain size. In addition, we measured the temperature-dependent TE properties of the 98wt% CoSb2.95Te0.05 hybrid film as shown in Figure S4. Both the electrical conductivity and the absolute value of Seebeck coefficient increased with an increase in temperature. This is a typical metallic behavior dependence observed in Te-doped CoSb3, which agrees with a large carrier concentration and supports the idea that the inorganic component led the electrical transport properties rather than the organic component.  The 98 wt% CoSb 2.95 Te 0.05 /PEDOT:PSS hybrid film, which has the highest thermoelectric performance, was subjected to a bending test to measure its flexibility as shown in Figure 5. The Seebeck coefficient and the electrical conductivity decreased from the original value promptly in the first 250 bending cycles along a glass rod with a 4 mm radius, but the rate of decrease became much slower after 250 bending cycles, demonstrating the film's flexibility to a certain degree considering that the film contains a large weight of powder and the facile method for breaking down the size of rigid TE materials.  The 98 wt% CoSb2.95Te0.05/PEDOT:PSS hybrid film, which has the highest thermoelectric performance, was subjected to a bending test to measure its flexibility as shown in Figure 5. The Seebeck coefficient and the electrical conductivity decreased from the original value promptly in the first 250 bending cycles along a glass rod with a 4 mm radius, but the rate of decrease became much slower after 250 bending cycles, demonstrating the film's flexibility to a certain degree considering that the film contains a large weight of powder and the facile method for breaking down the size of rigid TE materials.

Conclusions
In this study, a CoSb3-xTex/PEDOT:PSS hybrid film was produced using a simple method. First, we succeeded in our preliminary step to obtain a submicron to several micron particle size suitable for hybridization with the organic counterpart. Then, by suction-filtering the mixed solution with the PEDOT:PSS aqueous dispersion to an MCE membrane, we achieved the production of a uniform and flexible n-type FTE film. As for the TE performance, the Seebeck coefficient of the hybrid film increased as the amount of CoSb3-xTex in the hybrid film increased and the doping rate of CoSb3-xTex decreased. As a result, the CoSb2.95Te0.05/PEDOT:PSS hybrid film obtained the largest negative Seebeck co-

Conclusions
In this study, a CoSb 3-x Te x /PEDOT:PSS hybrid film was produced using a simple method. First, we succeeded in our preliminary step to obtain a submicron to several micron particle size suitable for hybridization with the organic counterpart. Then, by suction-filtering the mixed solution with the PEDOT:PSS aqueous dispersion to an MCE Polymers 2022, 14,1986 9 of 11 membrane, we achieved the production of a uniform and flexible n-type FTE film. As for the TE performance, the Seebeck coefficient of the hybrid film increased as the amount of CoSb 3-x Te x in the hybrid film increased and the doping rate of CoSb 3-x Te x decreased. As a result, the CoSb 2.95 Te 0.05 /PEDOT:PSS hybrid film obtained the largest negative Seebeck coefficient of −161.7 µV/K at 98 wt% at room temperature. As it is more challenging to obtain a large negative Seebeck coefficient in the hybrid thin films than improving the electrical conductivity of these type of films, wherein few approaches have been attempted, our work established a useful method of improving the power factor by raising the Seebeck coefficient. In addition, the 98 wt% hybrid film retained the flexibility to maintain a certain degree of electrical conductivity even after being bent 1000 times. It was proved that it is relatively easy to fabricate a flexible film with a very small amount of PEDOT:PSS and obtain moderate properties by finely tuning the composition of the TE films. The same method in this study can be applied to other inorganic materials. Therefore, it is expected that the selection of inorganic TE materials used for the development of n-type flexible thermoelectric materials will be expanded in the future.

Conflicts of Interest:
The authors declare no conflict of interest.