Structure and Thermoelectric Properties of Bi2−xSbxTe3 Nanowires Grown in Flexible Nanoporous Polycarbonate Templates

We report the room-temperature growth of vertically aligned ternary Bi2−xSbxTe3 nanowires of diameter ~200 nm and length ~12 µm, within flexible track-etched nanoporous polycarbonate (PC) templates via a one-step electrodeposition process. Bi2−xSbxTe3 nanowires with compositions spanning the entire range from pure Bi2Te3 (x = 0) to pure Sb2Te3 (x = 2) were systematically grown within the nanoporous channels of PC templates from a tartaric–nitric acid based electrolyte, at the end of which highly crystalline nanowires of uniform composition were obtained. Compositional analysis showed that the Sb concentration could be tuned by simply varying the electrolyte composition without any need for further annealing of the samples. Thermoelectric properties of the Bi2−xSbxTe3 nanowires were measured using a standardized bespoke setup while they were still embedded within the flexible PC templates.


Introduction
The rise of wireless sensing and communication technology in consumer electronics, health care and industry has led to an increased demand for wireless devices that are able to sustain themselves using ambient energy sources such as heat and vibrations.Thermoelectric generators (TEGs), without requiring any moving parts, can convert a temperature difference directly into an electrical current, and are therefore attracting widespread interest in generating power by recovering waste heat energy [1].Thermoelectric (TE) materials therefore hold a lot of promise in power generation, via the Seebeck effect, as well as solid-state cooling via the converse Peltier effect [2].The TE dimensionless figure-of-merit of a material at a temperature T, defined as ZT = S 2 σT/κ (where S is the Seebeck coefficient, σ is the electrical conductivity κ is the thermal conductivity), is essentially dependent on the material's intrinsic electrical and thermal properties.So far, considerable efforts have been made toward enhancing the figure-of-merit values in other existing TE material classes, including tellurides [3][4][5][6], half-Heuslers [7,8], and silicides [9,10].Also ZT can be often largely improved by nanostructuring [11][12][13].In this respect, TE nanomaterials offer the scope for higher ZT values and simultaneously allow for miniaturization of TE devices required for small-scale energy harvesting technologies.Additionally, there is a considerable interest in developing flexible and lightweight TE materials and devices for thermal energy harvesting for a range of different applications.Here we have employed a simple and cost-effective one-step electrodeposition growth process to fabricate vertically aligned nanowires of the ternary compound, Bi 2−x Sb x Te 3 , embedded within a flexible nanoporous PC template, where the effect of composition variation on the Seebeck coefficient is investigated.
Mixed ternary compounds of isostructural Bi 2 Te 3 and Sb 2 Te 3 (Bi 2−x Sb x Te 3 where x = 0 to 2) are among the most widely studied TE materials with a room temperature ZT value of ~1 [14][15][16].A large variation in this alloy composition is possible without greatly affecting ZT when a precise doping is maintained, and hence this has been a focus for TE research.The crystal structures of Bi 2−x Sb x Te 3 TE alloys show anisotropy originating from the rhombohedral structure composed of quintuple atomic layer series along the c-axis, and therefore one-dimensional nano-confinement in this material may significantly affect the electronic and thermal properties [11][12][13].Significant progress in enhancing ZT in Bi 2 Te 3 -based materials has been made through utilizing scalable processing techniques that can lead to nanostructuring [16][17][18][19], in order to achieve the desired shape, size, and other physical attributes that are useful controlling factors for enhanced TE performance.To this end, Bi 2−x Sb x Te 3 nanowires (NWs) have been extensively investigated, and TE performance of these alloy NWs are found to be improved due to the phonon scattering effects across the grain boundaries, and by manipulation of the band structure due to dimensional confinement [20][21][22][23].In this regard, a solution-based synthesis processes such as electrodeposition is a widely used protocol for preparing NWs within porous templates and has been reported as a cost-effective and scalable method to grow Bi 2 Te 3 based NWs with high density and large aspect ratios [24][25][26][27].These NWs have been predominantly synthesized by a number of template-assisted methods using track-etched membranes [28,29], diblock copolymers [30,31], or anodized aluminum oxide (AAO) templates [24].However, high thermal conductivities of the template matrices have been known to induce large thermal leakages [32,33].Therefore, it is crucial to prepare TE NWs in flexible and robust polymer templates that have very low thermal conductivities themselves, and that provide additional mechanical support and protection to the embedded NWs.
Our work therefore focuses on optimizing the growth parameters for different stoichiometries of ternary Bi 2−x Sb x Te 3 (x = 0, 0.5, 1, 1.5, 2) NWs of diameter ~200 nm and length ~12 µm in track-etched nanoporous polycarbonate (PC) membranes at room temperature, which was previously not been systematically studied.Controlling the doping concentration in the deposition solution leads to the variation in the stoichiometry in these high aspect ratio NWs.The resulting NWs were found to be highly crystalline and preferentially aligned with uniform compositional homogeneity.Furthermore, the high mechanical stability of the lightweight PC templates enabled the in-situ measurement of the thermoelectric properties of Bi 2−x Sb x Te 3 NWs, while they were still embedded and vertically aligned within the template.The work is of interest in the context of research toward fabricating flexible inorganic-organic hybrid TEGs.The synthesis process may be modified and extended to design NWs of other relevant Bi-based TE materials such as Bi and Bi x Sb y alloys with related crystal structures.

Template Preparation
Nanoporous polycarbonate (PC) templates of thickness ~12 µm thick and having pore diameters ~200 nm with a pore density of ~25% (Whatman ® Cyclopore ® , GE Healthcare, Wilkes-Barre, PA, USA) were used for growing the Bi 2−x Sb x Te 3 NWs (Panel A in Figure 1a).Prior to electrodeposition, the templates were coated on one-side with a layer of 100 nm thick Au layer by sputtering (Emitech ® K550, Quorum Technologies Limited, Lewes, UK) (Panel B in Figure 1a).The Au layer serves as both nucleation sites and electrode contact for the growth of NWs inside the porous template during electrodeposition [34].A glass slide coated with Au was then used to attach the Au-coated template secured with Kapton tape, and a copper wire was soldered to the template for electrical contact to the template during the electrodeposition process (Panel C in Figure 1a).

Electrolyte Preparation
All the chemicals obtained from Sigma Aldrich (Cheshire, UK) were of 99.99 % purity, ACS grade and were used without further purification.To grow Bi2−xSbxTe3 NWs, acidic aqueous electrolyte solutions were prepared.To achieve well-dispersed electrolytes, initially 1.5 mmol ground tellurium

Electrolyte Preparation
All the chemicals obtained from Sigma Aldrich (Cheshire, UK) were of 99.99 % purity, ACS grade and were used without further purification.To grow Bi 2−x Sb x Te 3 NWs, acidic aqueous electrolyte solutions were prepared.To achieve well-dispersed electrolytes, initially 1.5 mmol ground tellurium (Te) powder was dissolved in 6.4 mL 70% HNO 3 at 60 • C and the solution was stirred using a magnetic stirrer, followed by addition of 10 mL DI-water.When Te was fully dissolved, required molar ratios (for x = 0.25, 0.5 and 0.75) of hydrated bismuth nitrate (Bi(NO 3 ) 3 •5H 2 O)) was added at 60 • C.After bismuth nitrate was dissolved, 100 mL H 2 O was added and the solution was cooled down to room temperature.1-5 gm of tartaric acid was added depending on the molar ratio of Sb required, which was dissolved at room temperature.The tartaric acid served to dissolve the antimony acetate added in the next step and prevented formation of unwanted Sb 2 O 3 from antimony (III) acetate (Sb(CH 3 CO 2 ) 3 ) that was added in the end and dissolved at room temperature.The final solution was stirred at room temperature until a clear electrolyte mixture of Bi, Sb and Te precursors were obtained without any visible precipitants at pH ≈ 2.

Electrodepositon Process
The electrodeposition rig was set up in a three-probe configuration, where a Pt foil (20 mm × 20 mm) electrode was used as the cathode, while the electrode PC template and a Sigma Aldrich Ag/AgCl reference electrode served as the anode (Panel C in Figure 1a).A Versastat4 ® from Princeton Applied Sciences was used to set up the potential difference and the data was recorded in VersaStudio ® [34,35].Chronoamperometric electrodeposition (potentiostatic) was used where the potential difference and deposition time were varied and optimized to reach the optimum growth of the NWs and achieve maximum fill within the nanoporous PC templates (Panel D in Figure 1a).Under optimized conditions, −0.5 V was applied between the working electrode and the double junction Ag/AgCl reference electrode for ~90 min.The deposition was paused in the middle and the template surface was treated with stream of DI water to remove the powdery deposition on the template surface and the process was continued thereafter.When this intermediate cleaning step was not undertaken, the deposition residue blocked the nano-pores and incomplete growth of nanowires was observed (see Supporting Information).The solution was stirred throughout the deposition to avoid precipitation during the electrodeposition process.Finally, Bi 2−x Sb x Te 3 NW-filled PC templates were obtained (Panel E in Figure 1a).The PC template filled up with the NWs appeared to be black due to the presence of Bi 2−x Sb x Te 3 NWs inside, as shown in Panel E in Figure 1a).

Characterization
The phase and crystallinity of the Bi 2−x Sb x Te 3 NWs were characterized by X-ray diffraction (XRD) with a Bruker D8 diffractometer (Bruker AXS, Madison, WI, USA) equipped with Lynx Eye position-sensitive detector using Cu Kα radiation (λ = 1.5418Åu) at room temperature.Peak shifts due to sample misalignment were adjusted while performing the XRD scans and background correction was taken care of by using a zero diffraction silicon substrate for mounting.Microstructural studies were carried out by field-emission scanning electron microscopy (FE-SEM, FEI Nova NanoSEM, FEI, USA) and transmission electron microscopy (HRTEM, JEOL 4000EXII, JEOL, Tokyo, Japan).For TEM analysis Bi 2−x Sb x Te 3 NWs were released and collected by dissolving the PC templates in chlorobenzene (99%, Sigma Aldrich) followed by centrifugation.The NWs were then dispersed in anhydrous ethanol and drop-cast onto TEM grids (Ted Pella Inc., Redding, CA, USA).Energy Dispersive X-ray Analysis (EDX, Oxford Instruments, Oxfordshire, UK) was carried out to map the elemental distribution and to scan the elemental distribution along individual Bi 2−x Sb x Te 3 NWs.Structural studies such as XRD and SEM were also carried out on the NWs freed from the template.

Thermoelectric Property Measurements
The electrical conductivities and Seebeck coefficients (relative to the electrodes and contacts) of the samples were measured by a bespoke measurement setup (see Supporting Information).It consisted of a pair of commercial Peltier cooler/heater elements (Multicomp ® , 4.5 W, Farnell, UK) connected in series but with reverse polarity.A DC source was used to power the Peltier elements so that when one was heated the other was cooled and vice-versa.Both the Peltier elements were connected to heat reservoirs in the form of metallic blocks to ensure steady temperatures at a given DC bias powering the Peltier elements.The sample to be measured was sandwiched between the two Peltier elements to create a stable thermal gradient across the sample.Enamelled copper conducting wires were attached using Ag paint to the top and bottom faces of the sample in a pseudo four probe configuration.The Seebeck voltage and the electrical resistance of the sample were measured using a Keithley digital multimeter.The temperatures of the two Peltier elements were monitored by using an aerosol-jet printed Ag-track resistance thermometer [36], and sputter-coated Pd thin-film resistance thermometer, which were both calibrated against a commercial (Pt-100) platinum resistance thermometer (see Supporting information).A thermal grease (Servisol ® heat sink compound, Farnell, UK) was used to ensure good thermal contact between the Peltier elements and the sample.

Results and Discussion
The step by step reactions (inequilibrium) responsible for electrolytic deposition of Bi 2−x Sb x Te 3 NWs in acidic solutions can be described as: However, the actual mechanisms of reaction are far more complex [37], as the pH value of the electrolytic solution as well as the electrochemical potential has an influence on the crystallinity and stoichiometry of the NWs grown.The actual composition of Bi 2−x Sb x Te 3 NWs grown in PC controls their microstructure, crystallinity, and eventually thermoelectric behavior as shown in Figure 1b-g.Figure 1b shows the SEM image of the bare PC template indicating ~20% porosity, while Figure 1c) shows the Bi 2−x Sb x Te 3 NW-filled template.The representative cross sectional image of a torn-up PC template shown in Figure 1c reveals the growth of Bi 2−x Sb x Te 3 NWs, filling the template all through.Typical top surface of the Bi 2−x Sb x Te 3 NW-filled PC template is indicated by a square in Figure 1c and shown in Figure 1d).Profuse growth of NWs with protruding tips are clearly evident after the electrodeposition of Bi 2−x Sb x Te 3 NWs showing almost 100 % coverage.Bi 2−x Sb x Te 3 NWs of Sb-rich and Bi-rich compositions (nominal at %) were also released after dissolving the PC template (see experimental details) which are shown in Figure 1f,g, respectively.In the case of NWs, which are Sb-rich in composition, rough surface morphology in the NWs was observed.These NWs appeared to be rough, consisting of many nano-sized grains indicating poor crystallinity, while the Bi-rich NWs appear to have smooth, well-defined facets and hence, better crystallinity.This is further confirmed from XRD studies.
EDX analyses of all the samples were conducted in order to investigate the actual compositional variation within the NWs which are shown in Figure 2. In general, all the Bi 2−x Sb x Te 3 NWs did show presence of Bi, Sb and Te elements suggesting the formation of Bi 2−x Sb x Te 3 (Figure 2a).EDX mapping on the template-freed NWs also indicated uniform distribution of all the three elements in the samples revealing successful growth of Bi 2−x Sb x Te 3 alloy compositions.EDX analyses performed for each nominal composition of Bi 2−x Sb x Te 3 NWs as performed on over 50 different NWs indicated the actual at % of Bi and Sb elements present in each sample as shown in Figure 2c.It is to be noted that with increasing Bi/Sb ratio in the electrolyte (nominal wt %), the Bi/Sb ratio increased in the as-grown NWs (actual wt %) without any post-treatment such as annealing.Figure 3 shows the XRD spectra for different compositions of Bi2−xSbxTe3 NWs grown in PC templates.The sharp peak around 2θ = 28° corresponds to the (015) crystallographic direction and there were also relatively strong peaks observed at 2θ = 27° from (110) direction.As the Bi2-xSbxTe3 NWs have relatively larger diameters (~200 nm), polycrystalline orientations were more prevalent as revealed from the XRD spectra, and are in agreement with other reports [28,29,38].Contributions from the amorphous PC template also added to the background at lower angle 2θ between 10° and 50°.Several reports have focused on pore diameter as being one of the most influential factors in the physical properties of template-grown NWs [28,29,39].It is to be noted that as the Sb content increased in the samples, the crystallinity in the sample was found to significantly decrease.While the peaks for pure Bi2Te3 NWs prepared under similar deposition conditions are relatively sharp indicating highly crystalline grain domains, alloy compositions rich in Sb show broad XRD peaks indicating either low crystallinity or small crystallite sizes commensurate with our SEM observation in Figure 1f.showing the nominal atomic % of Bi, Sb and Te elements and the actual atomic % of the same elements present in the samples, which reveal that the samples are slightly rich in tellurium.Tellurium may be present in metallic form within the samples.
Figure 3 shows the XRD spectra for different compositions of Bi 2−x Sb x Te 3 NWs grown in PC templates.The sharp peak around 2θ = 28 • corresponds to the (015) crystallographic direction and there were also relatively strong peaks observed at 2θ = 27 • from (110) direction.As the Bi 2−x Sb x Te 3 NWs have relatively larger diameters (~200 nm), polycrystalline orientations were more prevalent as revealed from the XRD spectra, and are in agreement with other reports [28,29,38].Contributions from the amorphous PC template also added to the background at lower angle 2θ between 10 • and 50 • .Several reports have focused on pore diameter as being one of the most influential factors in the physical properties of template-grown NWs [28,29,39].It is to be noted that as the Sb content increased in the samples, the crystallinity in the sample was found to significantly decrease.While the peaks for pure Bi 2 Te 3 NWs prepared under similar deposition conditions are relatively sharp indicating highly crystalline grain domains, alloy compositions rich in Sb show broad XRD peaks indicating either low crystallinity or small crystallite sizes commensurate with our SEM observation in Figure 1f.In order to understand the observed peak broadening with increasing Sb content in the NWs, TEM and HRTEM was carried out on both Bi-rich and Sb-rich Bi2-xSbxTe3 compositions as shown in Figure 4.As expected Bi-rich Bi2-xSbxTe3 NWs showed uniform thickness along the length due to the presence of large spherical particulate crystallites (Figure 4a,b).The polycrystalline NWs have a crystallite size of ~30 nm and show well-defined crystalline behavior with preferential development of (015) plane (d spacing ~0.32 nm).Fast Fourier Transform (FFT) patterns of the (015) lattice plane showed crystalline spots depicting plausible hexagonal crystal structure of the constituent nano-sized grains, corresponding to the rhombohedral crystal system of Bi2−xSbxTe3 alloys.On the contrary, Sb-rich Bi2−xSbxTe3 NWs have rough surfaces as shown in Figure 4c, due to the clear hexagonal/rhombohedral crystallites of ~5-10 nm in size.These nanocrystallites are also highly crystalline, and show major development of (015) planes.FFT patterns similarly showed rhombohedral disposition of the nanocrystallites.Hence the broadness of the XRD peaks in Sb-rich compositions can be accounted for due to small crystallite sizes in the polycrystalline NWs, and not due to low crystallinity.The formation of polycrystalline Bi2-xSbxTe3 NWs can be explained by considering a competitive growth mechanism during the electrochemical growth of the Bi2-xSbxTe3 NWs: (i) rapid nucleation on the conducting gold layer and (ii) nucleation followed by formation of new grains.While single crystalline NWs are expected with the formation of larger nuclei and subsequent fast growth along the template pores, polycrystalline NWs may form if small nuclei are formed at the first instance followed by slow and steady growth of the nuclei.The two processes compete with each other and depend on several parameters including the potential difference, nature of the electrodes from which the nucleation start, the particle size of the sputtered back electrode, as well as the electrolyte composition [40].We argue that profuse availability of Bi ions from aqueous ionic Bi-nitrate during the growth of Bi-rich compositions might have led to rapid growth of the nuclei and hence larger crystallites.On the other hand, low availability of Sb ions due In order to understand the observed peak broadening with increasing Sb content in the NWs, TEM and HRTEM was carried out on both Bi-rich and Sb-rich Bi 2−x Sb x Te 3 compositions as shown in Figure 4.As expected Bi-rich Bi 2−x Sb x Te 3 NWs showed uniform thickness along the length due to the presence of large spherical particulate crystallites (Figure 4a,b).The polycrystalline NWs have a crystallite size of ~30 nm and show well-defined crystalline behavior with preferential development of (015) plane (d spacing ~0.32 nm).Fast Fourier Transform (FFT) patterns of the (015) lattice plane showed crystalline spots depicting plausible hexagonal crystal structure of the constituent nano-sized grains, corresponding to the rhombohedral crystal system of Bi 2−x Sb x Te 3 alloys.On the contrary, Sb-rich Bi 2−x Sb x Te 3 NWs have rough surfaces as shown in Figure 4c, due to the clear hexagonal/rhombohedral crystallites of ~5-10 nm in size.These nanocrystallites are also highly crystalline, and show major development of (015) planes.FFT patterns similarly showed rhombohedral disposition of the nanocrystallites.Hence the broadness of the XRD peaks in Sb-rich compositions can be accounted for due to small crystallite sizes in the polycrystalline NWs, and not due to low crystallinity.The formation of polycrystalline Bi 2−x Sb x Te 3 NWs can be explained by considering a competitive growth mechanism during the electrochemical growth of the Bi 2−x Sb x Te 3 NWs: (i) rapid nucleation on the conducting gold layer and (ii) nucleation followed by formation of new grains.While single crystalline NWs are expected with the formation of larger nuclei and subsequent fast growth along the template pores, polycrystalline NWs may form if small nuclei are formed at the first instance followed by slow and steady growth of the nuclei.The two processes compete with each other and depend on several parameters including the potential difference, nature of the electrodes from which the nucleation start, the particle size of the sputtered back electrode, as well as the electrolyte composition [40].We argue that profuse availability of Bi ions from aqueous ionic Bi-nitrate during the growth of Bi-rich compositions might have led to rapid growth of the nuclei and hence larger crystallites.On the other hand, low availability of Sb ions due to slow release of Sb ions from the Sb-tartaric acid complex might cause a steady and slow growth of nuclei and hence this resulted in finer grain sizes in Sb-rich compositions [41].While high temperature annealing might lead to enhanced crystallinity of the NWs, this could also potentially lead to the fractionalization of ternary alloy composition and formation of sub-oxide impurities leading to high resistivity in the sample.Therefore, our electrochemical growth process at room temperature is a step forward in growing the complex Bi 2−x Sb x Te 3 composition as pure and highly crystalline NWs. to slow release of Sb ions from the Sb-tartaric acid complex might cause a steady and slow growth of nuclei and hence this resulted in finer grain sizes in Sb-rich compositions [41].While high temperature annealing might lead to enhanced crystallinity of the NWs, this could also potentially lead to the fractionalization of ternary alloy composition and formation of sub-oxide impurities leading to high resistivity in the sample.Therefore, our electrochemical growth process at room temperature is a step forward in growing the complex Bi2-xSbxTe3 composition as pure and highly crystalline NWs.Our Bi2-xSbxTe3 NWs encapsulated within a PC matrix may serve as a lightweight flexible TEG as can be demonstrated from the measured relative Seebeck coefficients of the above samples.For each measurement, NW-filled PC template were cut into pieces having cross-sectional area of ~0.15-0.20 cm 2 , and sputter-coated with Au electrodes on the top surface.The results of these measurements are depicted in Figure 5 (electrical conductivity data is shown in the Supporting Information).From Figure 5, we can clearly see that the relative Seebeck coefficient increased with increasing Sb content, peaking at 100 at % (nominal at %).The samples show p-type behavior over the entire composition range.The power factor, calculated as S 2 σ, is also shown in the figure.From these results we can see that although the power factor obtained is less than what has been reported in the literature [16][17][18][19] for Bi and Sb tellurides (see also Supporting Information), it is worth noting that this performance has been achieved by using a much cheaper processing technique, which utilises only a small amount of material, and the final product can be used in applications where flexibility of the devices is needed in order to conformally wrap them around complex-shaped  Our Bi 2−x Sb x Te 3 NWs encapsulated within a PC matrix may serve as a lightweight flexible TEG as can be demonstrated from the measured relative Seebeck coefficients of the above samples.For each measurement, NW-filled PC template were cut into pieces having cross-sectional area of ~0.15-0.20 cm 2 , and sputter-coated with Au electrodes on the top surface.The results of these measurements are depicted in Figure 5 (electrical conductivity data is shown in the Supporting Information).From Figure 5, we can clearly see that the relative Seebeck coefficient increased with increasing Sb content, peaking at 100 at % (nominal at %).The samples show p-type behavior over the entire composition range.The power factor, calculated as S 2 σ, is also shown in the figure.From these results we can see that although the power factor obtained is less than what has been reported in the literature [16][17][18][19] for Bi and Sb tellurides (see also Supporting Information), it is worth noting that this performance has been achieved by using a much cheaper processing technique, which utilises only a small amount of material, and the final product can be used in applications where flexibility of the devices is needed in order to conformally wrap them around complex-shaped objects.On the other hand, we also continue to improve our measurement procedure as sensing the precise temperature on either sides of such a thin sample is very challenging and potentially, can result in overestimation the temperature difference (and hence, underestimating the relative Seebeck coefficient and power factor).It should also be noted here that the thermoelectric properties of arrays of template-grown nanowires of Bi 2−x Sb x Te 3 still embedded in the template are rarely found in the literature.Most of the reported measurements relate to individual nanowires freed from the template.Such single nanowires exhibit better thermoelectric properties than that reported here because of fewer defects, better crystallinity and better preserved structure of the individual nanowire being tested (see Supporting Information).However, isolated nanowires would prove difficult to implement in actual thermoelectric device applications.Instead, in this work, we have presented measurements of the thermoelectric performance of embedded nanowire arrays which can be directly incorporated in real life applications.The thermoelectric parameters evaluated in this way are lower than the literature reports of single nanowires (see Supporting Information), due to higher probability of encountering a small fraction of defective nanowires containing imperfections such as anti-site defects, Te-rich nano-nuggets, accidental Au doped regions, etc., which affect the Seebeck coefficient and thermoelectric power factor [42][43][44][45][46][47][48][49].Nevertheless, evaluation of thermoelectric performance of the as-grown template-embedded nanowires offers valuable insight into their applicability in thermoelectric devices.
Materials 2017, 10, 553 9 of 12 objects.On the other hand, we also continue to improve our measurement procedure as sensing the precise temperature on either sides of such a thin sample is very challenging and potentially, can result in overestimation the temperature difference (and hence, underestimating the relative Seebeck coefficient and power factor).It should also be noted here that the thermoelectric properties of arrays of template-grown nanowires of Bi2−xSbxTe3 still embedded in the template are rarely found in the literature.Most of the reported measurements relate to individual nanowires freed from the template.Such single nanowires exhibit better thermoelectric properties than that reported here because of fewer defects, better crystallinity and better preserved structure of the individual nanowire being tested (see Supporting Information).However, isolated nanowires would prove difficult to implement in actual thermoelectric device applications.Instead, in this work, we have presented measurements of the thermoelectric performance of embedded nanowire arrays which can be directly incorporated in real life applications.The thermoelectric parameters evaluated in this way are lower than the literature reports of single nanowires (see Supporting Information), due to higher probability of encountering a small fraction of defective nanowires containing imperfections such as anti-site defects, Te-rich nano-nuggets, accidental Au doped regions, etc., which affect the Seebeck coefficient and thermoelectric power factor [42][43][44][45][46][47][48][49].Nevertheless, evaluation of thermoelectric performance of the as-grown template-embedded nanowires offers valuable insight into their applicability in thermoelectric devices.

Conclusions
In conclusion, we have successfully prepared Bi2−xSbxTe3 NWs of different compositions with varying Sb/Bi ratios (both Bi-rich and Sb-rich) in flexible PC templates, via a one-step room temperature electrodeposition process.The process involves simple tuning of tartaric acid and nitric acid electrolyte composition at an optimized voltage condition of −0.5 V between the two electrodes for ~90 min.The structure and crystallinity of the NWs studied by SEM, XRD and TEM indicates that the NWs are polycrystalline with high order of crystallinity.NWs of Sb-rich compositions formed small crystallites with dimensions of the order of 5 nm, as compared to ~30 nm in Bi-rich compositions, possibly due to the difference in the rate of growth after nucleation as a result of slow dissociation of Sb ions from tartaric acid complex.We measured TE properties of our as-grown NWs using a bespoke thermoelectric set-up.Our high crystalline ternary Bi2−xSbxTe3 NWs encapsulated within flexible and lightweight PC matrix showed reasonably good TE properties with Sb2Te3 NWs sample showing a relative Seebeck coefficient of ~6.5 µV/K.

Conclusions
In conclusion, we have successfully prepared Bi 2−x Sb x Te 3 NWs of different compositions with varying Sb/Bi ratios (both Bi-rich and Sb-rich) in flexible PC templates, via a one-step room temperature electrodeposition process.The process involves simple tuning of tartaric acid and nitric acid electrolyte composition at an optimized voltage condition of −0.5 V between the two electrodes for ~90 min.The structure and crystallinity of the NWs studied by SEM, XRD and TEM indicates that the NWs are polycrystalline with high order of crystallinity.NWs of Sb-rich compositions formed small crystallites with dimensions of the order of 5 nm, as compared to ~30 nm in Bi-rich compositions, possibly due to the difference in the rate of growth after nucleation as a result of slow dissociation of Sb ions from tartaric acid complex.We measured TE properties of our as-grown NWs using a bespoke thermoelectric set-up.Our high crystalline ternary Bi 2−x Sb x Te 3 NWs encapsulated within flexible and lightweight PC matrix showed reasonably good TE properties with Sb 2 Te 3 NWs sample showing a relative Seebeck coefficient of ~6.5 µV/K.

Figure 1 .
Figure 1.(a) Schematic showing the electrodeposition growth process of Bi2−xSbxTe3 NWs inside polymer PC templates.Panel A is the original PC template and panel E is the template after deposition containing NWs; (b,c) are the SEM images of nanoporous PC templates before and after NW growth; (d) shows the surface of the NW filled template as indicated in (c) (white square); (e) Close-up view of the NW arrays inside the PC template; (f) Sb-rich Bi2−xSbxTe3 NWs after dissolving PC template which show rough surfaces as compared to the Bi-rich NWs as shown in (g) which are smooth textured.

Figure 1 .
Figure 1.(a) Schematic showing the electrodeposition growth process of Bi 2−x Sb x Te 3 NWs inside polymer PC templates.Panel A is the original PC template and panel E is the template after deposition containing NWs; (b,c) are the SEM images of nanoporous PC templates before and after NW growth; (d) shows the surface of the NW filled template as indicated in (c) (white square); (e) Close-up view of the NW arrays inside the PC template; (f) Sb-rich Bi 2−x Sb x Te 3 NWs after dissolving PC template which show rough surfaces as compared to the Bi-rich NWs as shown in (g) which are smooth textured.

Figure 2 .
Figure 2. (a) Representative EDX spectrum of Bi2−xSbxTe3 NWs; (b) Mapping of the Bi2−xSbxTe3 NWs reveal uniform presence of the constituent elements: bismuth (green), tellurium (blue) and antimony (pink).The scale bar in the mapping indicates 1 μm; (c) Tableshowingthe nominal atomic % of Bi, Sb and Te elements and the actual atomic % of the same elements present in the samples, which reveal that the samples are slightly rich in tellurium.Tellurium may be present in metallic form within the samples.

Figure 2 .
Figure 2. (a) Representative EDX spectrum of Bi 2−x Sb x Te 3 NWs; (b) Mapping of the Bi 2−x Sb x Te 3 NWs reveal uniform presence of the constituent elements: bismuth (green), tellurium (blue) and antimony (pink).The scale bar in the mapping indicates 1 µm; (c) Tableshowingthe nominal atomic % of Bi, Sb and Te elements and the actual atomic % of the same elements present in the samples, which reveal that the samples are slightly rich in tellurium.Tellurium may be present in metallic form within the samples.

Figure 3 .
Figure 3. Representative XRD patterns of Bi2-xSbxTe3 NWs of different nominal compositions; (a) for x = 0 i.e., pure Bi2Te3 (b) for x = 2 i.e., Sb2Te3 (c) Bi-rich and (d) Sb-rich Bi2-xSbxTe3 NWs.The NWs show a noticeable peak broadening with increasing Sb, due to the grain size difference between the Bi-rich and Sb-rich compositions, showing polycrystalline signature for all of the types of NWS.

Figure 3 .
Figure 3. Representative XRD patterns of Bi 2−x Sb x Te 3 NWs of different nominal compositions; (a) for x = 0 i.e., pure Bi 2 Te 3 (b) for x = 2 i.e., Sb 2 Te 3 (c) Bi-rich and (d) Sb-rich Bi 2−x Sb x Te 3 NWs.The NWs show a noticeable peak broadening with increasing Sb, due to the grain size difference between the Bi-rich and Sb-rich compositions, showing polycrystalline signature for all of the types of NWS.

Figure 4 .
Figure 4. TEM and HRTEM images of (a,b) of Bi-rich Bi2-xSbxTe3 NWs showing uniform and smooth surface texture composed of well crystalline spherical grains; (c,d) Sb-rich Bi2-xSbxTe3 NWs with rough surface that are composed of highly crystalline faceted grains.

Figure 4 .
Figure 4. TEM and HRTEM images of (a,b) of Bi-rich Bi 2−x Sb x Te 3 NWs showing uniform and smooth surface texture composed of well crystalline spherical grains; (c,d) Sb-rich Bi 2−x Sb x Te 3 NWs with rough surface that are composed of highly crystalline faceted grains.

Figure 5 .
Figure 5. Relative Seebeck coefficient and power factor of the Bi2−xSbxTe3 NWs plotted as a function of the nominal Sb content in the samples.

Figure 5 .
Figure 5. Relative Seebeck coefficient and power factor of the Bi 2−x Sb x Te 3 NWs plotted as a function of the nominal Sb content in the samples.
Figure S1: (a) Large crystals grown on top of the template surface blocking the pores in uncleaned template during deposition and (b) Unfilled template with incomplete NW growth as a result as shown in the cross section; Figure S2: (a) A representative sample used for characterization; (b) Peltier module used to heat or cool the sample surface; (c) the Peltier module-copper block assembly used to heat/cool top or bottom surfaces of the sample.