Enhanced Thermoelectric Cooling through Introduction of Material Anisotropy in Transverse Thermoelectric Composites

Transverse thermoelectric materials can achieve appreciable cooling power with minimal space requirement. Among all types of material candidates for transverse thermoelectric applications, composite materials have the best cooling performance. In this study, anisotropic material properties were applied to the component phase of transverse thermoelectric composites. A mathematical model was established for predicting the performance of fibrous transverse thermoelectric composites with anisotropic components. The mathematical model was then validated by finite element analysis. The thermoelectric performance of three types of composites are presented, each with the same set of component materials. For each type of component, both anisotropic single-crystal and isotropic polycrystal material properties were applied. The results showed that the cooling capacity of the system was improved by introducing material anisotropy in the component phase of composite. The results also indicated that the orientation of the anisotropic component’s property axis, the anisotropic characteristic of a material, will significantly influence the thermoelectric performance of the composite. For a composite material consisting of Copper fiber and Bi2Te3 matrix, the maximum cooling capacity can vary as much as 50% at 300 K depending on the property axis alignment of Bi2Te3 in the composite. The composite with Copper and anisotropic SnSe single crystal had a 51% improvement in the maximum cooling capacity compared to the composite made of Copper and isotropic SnSe polycrystals.


Introduction
Thermoelectric material can transform thermal energy into electrical energy and vice versa. Its applications can be found in various fields such as temperature measurement, power generation, temperature control, etc. Conventional thermoelectric devices consist of both n-type and p-type thermoelectric legs. Within each leg, the heat flux and electrical current flow are parallel to each other [1,2]. Transverse thermoelectric devices make use of the transverse Seebeck effect so that the electrical current and heat flux flow perpendicular to each other [3]. There are four main types of transverse thermoelectric materials, which are anisotropic single-crystal material, polycrystal material with engineered anisotropy, anisotropic organic thin-film thermoelectrics, and anisotropic

Mathematical Model for Fibrous Thermoelectric Composites with Anisotropic Components
In this section, analytical equations are derived for the effective properties of a transverse thermoelectric composite. In the mathematical model, unit cell structure is used to reduce the complexity of this problem. This unit cell model has been proven to be a convenient tool in studies on the effective properties of a material with periodical structures [16,22]. The schematic of a fibrous thermoelectric composite unit cell is shown in Figure 1, where a fiber (F) with a square cross-section was placed at the corner of a cubic matrix (M). The square fiber was used in the unit cell model for mathematical simplicity. The contact between the matrix and fibrous material was assumed to be ideal so that electrical and thermal contact resistance were not considered.
axis system "uvw" to describe the anisotropic material properties (Figure 1b). There are four sets of coordinate systems in Figure 1, which are the local material coordinate system of the fibrous and matrix phase, the coordinate system of composite C1(F + M1), and the coordinate system of unit cell C2(F + M1 + M2). In Figure 1, the coordinate axes u, x1, and x2 align parallel to each other; v, y1, and y2 align parallel to each other, and a, w, z1, and z2 align parallel to each other. The cross-sectional plane of fiber (p-p) is parallel with the u-v plane of the matrix material. The effective properties of the unit cell can be derived in two steps as illustrated in Figure 1c. In the first step, the square fiber (F) is combined with part of the matrix phase (M1) to form a rectangular composite C1, where the matrix block has the same width and height as the fibrous phase. In the second step, the composite C1 is combined with the rest of the matrix to form the unit cell. The effective thermal and electrical conducting properties of the unit cell can be calculated using Kirchhoff's law, and the effective Seebeck coefficient can be calculated using Thevenin's theorem [25]. The material properties of the composite C1 can be derived according to Equation (1): The symbols ρ, λ, S, and f stand for electrical resistivity, thermal conductivity, Seebeck coefficient, and fiber volume fraction. The subscripts p, a, u, v, w, xi, yi, and zi stand for component material's properties along each material's local coordinate systems. The material properties of the unit cell can be derived according to Equation (2): When anisotropic material properties are introduced into the component phase (i.e., fibrous phase and matrix phase) of a composite material, the alignment of the material local property axis with respect to the composite material coordinate system plays a key role in the effective properties of the composite. Many 1D inclusions, such as carbon nanotubes [23,24], have different material properties along and perpendicular to the fiber axis direction. Therefore, in this study, we used the subscript "p" to represent the properties on the cross-sectional plane of the fiber and subscript "a" to represent properties along fiber axis ( Figure 1a). As for the matrix phase, we used the material local axis system "uvw" to describe the anisotropic material properties (Figure 1b). There are four sets of coordinate systems in Figure 1, which are the local material coordinate system of the fibrous and matrix phase, the coordinate system of composite C 1 (F + M 1 ), and the coordinate system of unit cell C 2 (F + M 1 + M 2 ). In Figure 1, the coordinate axes u, x 1 , and x 2 align parallel to each other; v, y 1 , and y 2 align parallel to each other, and a, w, z 1 , and z 2 align parallel to each other. The cross-sectional plane of fiber (p-p) is parallel with the u-v plane of the matrix material.
The effective properties of the unit cell can be derived in two steps as illustrated in Figure 1c. In the first step, the square fiber (F) is combined with part of the matrix phase (M 1 ) to form a rectangular composite C 1 , where the matrix block has the same width and height as the fibrous phase. In the second step, the composite C 1 is combined with the rest of the matrix to form the unit cell. The effective thermal and electrical conducting properties of the unit cell can be calculated using Kirchhoff's law, and the effective Seebeck coefficient can be calculated using Thevenin's theorem [25]. The material properties of the composite C 1 can be derived according to Equation (1): The symbols ρ, λ, S, and f stand for electrical resistivity, thermal conductivity, Seebeck coefficient, and fiber volume fraction. The subscripts p, a, u, v, w, x i , y i , and z i stand for component material's properties along each material's local coordinate systems. The material properties of the unit cell can be derived according to Equation (2): In Figure 1, the fiber axis aligns parallel to the z 2 -axis of the composite. When fibers are tilted aligned in the composite, the effective properties of the composite can be calculated through matrix transformation. For example, if the fibers in Figure 1 are rotated by an angle of θ around x 2 -axis into the configuration in Figure 2, the effective properties of the composite can be calculated as [26]: In Figure 1, the fiber axis aligns parallel to the z2-axis of the composite. When fibers are tilted aligned in the composite, the effective properties of the composite can be calculated through matrix transformation. For example, if the fibers in Figure 1 are rotated by an angle of θ around x2-axis into the configuration in Figure 2, the effective properties of the composite can be calculated as [26]: In a transverse thermoelectric material, heat flux and electrical current flow perpendicular to each other. Based on Figure 2, we assume the electrical current flows in the y-direction and heat flux flows in the z-direction. The transverse thermoelectric figure of merit is defined as Z T = [10,27], where Szy is the transverse Seebeck coefficient, ρyy is electrical resistivity in the y-direction, λzz is thermal conductivity in the z-direction, T is the operating temperature. The term Szy, ρyy, and λzz values can be calculated using Equation (1) to Equation (3). Figure 2 can also represent a fibrous transverse thermoelectric device operating under cooling mode, where the top surface serves as a cooling surface with a temperature of Tc and the bottom surface serves as a heat sink with a temperature of Th. When the electrical current flows in the ydirection, the transverse Peltier effect will trigger heat flux along the z-direction. The maximum cooling capacity of the system is related to the ZtransT value, according to previous studies [10,28]. In this study, the Th was set to be the measuring temperature of material properties, which are shown in Table 1. ρ yy λ zz [10,27], where S zy is the transverse Seebeck coefficient, ρ yy is electrical resistivity in the y-direction, λ zz is thermal conductivity in the z-direction, T is the operating temperature. The term S zy , ρ yy , and λ zz values can be calculated using Equation (1) to Equation (3). Figure 2 can also represent a fibrous transverse thermoelectric device operating under cooling mode, where the top surface serves as a cooling surface with a temperature of T c and the bottom surface serves as a heat sink with a temperature of T h . When the electrical current flows in the y-direction, the transverse Peltier effect will trigger heat flux along the z-direction. The maximum cooling capacity of the system is related to the Z trans T value, according to previous studies [10,28]. In this study, the T h was set to be the measuring temperature of material properties, which are shown in Table 1.  In the next step, experimentally measured material properties are implemented into the derived equations. Previous studies [9] have shown that high-performance transverse thermoelectric composites usually consist of one semiconducting thermoelectric phase and one highly conductive phase, where the thermoelectric phase provides high Seebeck coefficient and low thermal conductivity, the conducting phase provides low electrical resistivity. Therefore, we chose anisotropic Bi 2 Te 3 polycrystal as the matrix phase and Copper as the fibrous phase for the composite. The properties of these materials are shown in Table 1. According to Table 1, the Copper phase was isotropic and Bi 2 Te 3 was anisotropic with planar (u-v plane) isotropy.
When anisotropic material properties are implemented in the component phase of a composite, the alignment of component material's local property coordinate system, with respect to the composite coordinate system, will affect the effective properties of the composite. In Figure 1, the u-v plane of the matrix material aligns perpendicular to the fiber axis. If the material property coordinate in Figure 1b is rotated around the u-axis 90 degrees, the anisotropy plane of Bi 2 Te 3 will be parallel to the fiber axis direction. For the convenience of analysis, we shall refer to the two configurations mentioned above as configuration I and configuration II. In configuration I, the material property axes u, v, and w are parallel to the composite axes x 2 , y 2 , and z 2 , respectively. In configuration II, the material property axes u, v, and w are parallel to the composite axes x 2 , z 2 , and y 2 , respectively. The corresponding Z trans T and maximum cooling capacities (∆T max ) based on these two configurations were calculated using the derived mathematical model with respect to fiber rotation angle, θ, and fiber volume fraction, f. The results are shown in Figure 3. When anisotropic material properties are implemented in the component phase of a composite, the alignment of component material's local property coordinate system, with respect to the composite coordinate system, will affect the effective properties of the composite. In Figure 1, the uv plane of the matrix material aligns perpendicular to the fiber axis. If the material property coordinate in Figure 1b is rotated around the u-axis 90 degrees, the anisotropy plane of Bi2Te3 will be parallel to the fiber axis direction. For the convenience of analysis, we shall refer to the two configurations mentioned above as configuration I and configuration II. In configuration I, the material property axes u, v, and w are parallel to the composite axes x2, y2, and z2, respectively. In configuration II, the material property axes u, v, and w are parallel to the composite axes x2, z2, and y2, respectively. The corresponding ZtransT and maximum cooling capacities (∆Tmax) based on these two configurations were calculated using the derived mathematical model with respect to fiber rotation angle, θ, and fiber volume fraction, f. The results are shown in Figure 3.   volume fraction under a constant rotation angle had a minor influence on the Z trans T and ∆T max values. The maximum Z trans T and ∆T max values in configuration I were 0.29 and 34 K, while the values of maximum Z trans T and ∆T max in configuration II were 0.22 and 27 K. These results indicate a 26% difference in the peak thermoelectric performance among the two configurations. Hence, the alignment of the material's local property coordinates with respect to the composite coordinate system had significant influence on the composite's cooling performance.
Many thermoelectric materials are polycrystals. These polycrystals may exhibit certain degrees of texture, and thus, anisotropic properties as a result of the fabrication processes. There exists theoretical models that can correlate the aggregate properties of polycrystals with its single-crystal material property. Among these theoretical models, the Voigt model and Reuss model can provide upper and lower bounds for the aggregate properties of polycrystals, respectively [32][33][34]. In this study, we take experimentally measured values from a single-crystal Bi 2 Te 3 ( Table 1) and calculate possible aggregate material properties using Reuss and Voigt models. The Bi 2 Te 3 polycrystal has isotropic Seebeck coefficients and exhibits planar isotropy (u-v plane) in electrical resistivity and thermal conductivity based on existing experimental results [5,18,35,36]. The anisotropy ratio terms r λ and r ρ are used to relate the material properties in different axis directions, such that r λ = λ u /λ w , r ρ = ρ w /ρ u . By importing these hypothetical aggregate properties into the Bi 2 Te 3 phase, the maximum cooling capacities were calculated for the Bi 2 Te 3 matrix/Cu fiber composite. The results are shown in Figure 4. According to the definition of r λ and r ρ , the bottom-left corner of Figure 4a,b represents the maximum cooling capacity of a polycrystal Bi 2 Te 3 with isotropic material properties. The results in Figure 4 show that by introducing material anisotropy in a fibrous transverse thermoelectric composite, the cooling capacity of the composite can be improved by 7% (Figure 4b

Finite Element Simulation for Fibrous Thermoelectric Composite with Anisotropic Components
In order to validate the effectiveness of the mathematical model, finite element simulations were carried out using COMSOL (COMSOL Multiphysics, COMSOL Inc., Burlington, MA, USA). A unit cell model based on Figure 1c was constructed using polycrystal Bi2Te3 as the matrix phase and Copper as the fiber phase assuming the isotropy plane of Bi2Te3 was perpendicular to the fiber axis. For all finite element models involved in this study, mesh convergence studies were carried out and the convergence error was limited to below 3%.
According to the unit cell model shown in Figure 1c, square fiber was used for mathematical simplicity. In the finite element simulations, both cylindrical fiber and square fiber were investigated so as to explore the effect of fiber shapes. The effective properties of the unit cells are shown in Figure  5.

Finite Element Simulation for Fibrous Thermoelectric Composite with Anisotropic Components
In order to validate the effectiveness of the mathematical model, finite element simulations were carried out using COMSOL (COMSOL Multiphysics, COMSOL Inc., Burlington, MA, USA). A unit cell model based on Figure 1c was constructed using polycrystal Bi 2 Te 3 as the matrix phase and Copper as the fiber phase assuming the isotropy plane of Bi 2 Te 3 was perpendicular to the fiber axis. For all finite element models involved in this study, mesh convergence studies were carried out and the convergence error was limited to below 3%.
According to the unit cell model shown in Figure 1c, square fiber was used for mathematical simplicity. In the finite element simulations, both cylindrical fiber and square fiber were investigated so as to explore the effect of fiber shapes. The effective properties of the unit cells are shown in Figure 5.
carried out using COMSOL (COMSOL Multiphysics, COMSOL Inc., Burlington, MA, USA). A unit cell model based on Figure 1c was constructed using polycrystal Bi2Te3 as the matrix phase and Copper as the fiber phase assuming the isotropy plane of Bi2Te3 was perpendicular to the fiber axis. For all finite element models involved in this study, mesh convergence studies were carried out and the convergence error was limited to below 3%.
According to the unit cell model shown in Figure 1c, square fiber was used for mathematical simplicity. In the finite element simulations, both cylindrical fiber and square fiber were investigated so as to explore the effect of fiber shapes. The effective properties of the unit cells are shown in Figure  5. According to Figure 5, the finite element simulation results and mathematical model agreed well with each other. The conductivities of the unit cell increased as the volume fraction of the fibers increased, since the fiber was more conductive than the matrix material. In Figure 5f, the effective Seebeck coefficient had negative values at a low fiber volume fraction, but became positive as the fiber volume fraction increased. This was because the Bi2Te3 phase had a negative Seebeck coefficient and Copper had a positive Seebeck coefficient. The effective Seebeck coefficient was dominated by the matrix phase at low fiber volume fractions, and by the fibrous phase at high fiber volume increased, since the fiber was more conductive than the matrix material. In Figure 5f, the effective Seebeck coefficient had negative values at a low fiber volume fraction, but became positive as the fiber volume fraction increased. This was because the Bi 2 Te 3 phase had a negative Seebeck coefficient and Copper had a positive Seebeck coefficient. The effective Seebeck coefficient was dominated by the matrix phase at low fiber volume fractions, and by the fibrous phase at high fiber volume fractions.
Some minor deviations were observed between the mathematical model and the finite element simulation model. This was because the mathematical model assumes a one-dimensional flux flow, i.e., the electrical and heat flux only flow along the applied field, whereas fluxes in other directions are not considered. These fluxes are caused by the material inhomogeneity and the shape feature of fibers. When the fiber volume fraction is very small or very large, homogeneity of the composite will inevitably be compromised. Moreover, when the direction of the applied potential is not perpendicular to the interface between the matrix and fibrous phase, the secondary dimensional flux will occur. Both situations above are the cause of deviation between the mathematical model and finite element simulation results.
Finite element models with tilted aligned fibers in a matrix were also constructed to study the cooling capacity of the composite. The properties of polycrystal Bi 2 Te 3 and Copper were applied. The fiber rotation angle was fixed at 80 degrees. According to Figure 2, the composite can be seen as fiber arrays periodically aligned in the x-direction. Therefore, to simplify the finite element model, only one fiber array was constructed inside the matrix block, and periodic boundary conditions were applied on the surfaces parallel to the y-z plane. The geometry of the model was 2 mm × 500 mm × 10 mm, while the fiber diameter was adjusted to suit different fiber volume fractions. The bottom surface of the device was fixed at 300 K to serve as a heat sink, while the top surface was subjected to natural convective heat transfer. Two 1 mm thick Copper blocks were added on both ends of the y-direction of the composite to serve as electrodes. Twenty cases were studied with different fiber volume fractions, fiber shapes, and with respect to the two configurations mentioned above. Within each case, the input electrical current density was adjusted until the maximum temperature difference between the top and bottom surface was reached. Figure 6 provides temperature distributions on the y-z plane for both cylindrical fiber model and square fiber model at 30% fiber volume fraction. Enlarged views of the top surface are shown in the insets. For both composites in Figure 6, a temperature gradient caused by the transverse Peltier effect can be clearly observed in the vertical direction. In the horizontal direction, the temperature was uniformly distributed except at the ends of the electrodes. In the insets of Figure 6, the abrupt temperature change at the interfaces of the fiber and matrix phases was the result of the Peltier effect. arrays periodically aligned in the x-direction. Therefore, to simplify the finite element model, only one fiber array was constructed inside the matrix block, and periodic boundary conditions were applied on the surfaces parallel to the y-z plane. The geometry of the model was 2 mm × 500 mm × 10 mm, while the fiber diameter was adjusted to suit different fiber volume fractions. The bottom surface of the device was fixed at 300 K to serve as a heat sink, while the top surface was subjected to natural convective heat transfer. Two 1 mm thick Copper blocks were added on both ends of the ydirection of the composite to serve as electrodes. Twenty cases were studied with different fiber volume fractions, fiber shapes, and with respect to the two configurations mentioned above. Within each case, the input electrical current density was adjusted until the maximum temperature difference between the top and bottom surface was reached. Figure 6 provides temperature distributions on the y-z plane for both cylindrical fiber model and square fiber model at 30% fiber volume fraction. Enlarged views of the top surface are shown in the insets. For both composites in Figure 6, a temperature gradient caused by the transverse Peltier effect can be clearly observed in the vertical direction. In the horizontal direction, the temperature was uniformly distributed except at the ends of the electrodes. In the insets of Figure 6, the abrupt temperature change at the interfaces of the fiber and matrix phases was the result of the Peltier effect. The surface temperature was averaged on the top surface of each finite element model. The maximum temperature difference in each case was calculated by subtracting the heat sink temperature by the averaged cooling surface temperature. The results are presented in Table 2. In general, the mathematical model results agreed well with the finite element simulation results with at most a 10% difference. These small discrepancies were mainly caused by the secondary The surface temperature was averaged on the top surface of each finite element model. The maximum temperature difference in each case was calculated by subtracting the heat sink temperature by the averaged cooling surface temperature. The results are presented in Table 2. In general, the mathematical model results agreed well with the finite element simulation results with at most a 10% difference. These small discrepancies were mainly caused by the secondary dimensional flux that was previously discussed. The only exception in Table 2 was the case for the cylindrical fiber with f = 0.1 under configuration I, where the ∆T max calculated using the mathematical model was more than 10% higher than the finite element simulation result. This was because under small or large fiber volume fraction cases, the homogeneity of the composite was very poor, which conflicts with the assumption in the mathematical model. The differences between the two configurations also agreed with the results shown in Figure 3, which emphasized the significant effect of the component material's local property axes alignment in the composite coordinate system. During the finite element analysis, it was found that the size of the fibers has a slight influence on the TE performance. In anisotropic thermoelectric composites, smaller fibers provide the composite with better homogeneity. Although, under the same volume fraction of fibers the cooling capacity of the composite may not vary much with the size of the fibers, large fiber geometry is likely to cause higher temperature fluctuations in between the boundaries of the fibrous phase and the matrix phase.

Cooling Capacity Comparison for 1-Dimensional and 2-Demensional Inclusion Thermoelectric Composites with Anisotropic Components
The cooling performance of fibrous transverse thermoelectric composites were investigated with both a mathematical approach and a simulation approach. While the fibrous transverse thermoelectric composite can be treated as a 1D inclusion composite, the layered transverse thermoelectric composite can be treated as a 2D inclusion composite. The cooling capacity of the layered transverse thermoelectric composites with anisotropic components have been investigated thoroughly in previous studies [21]. Hence, it is informative to compare the cooling performances of transverse thermoelectric composites between 1D and 2D inclusion composites. In this section, three types of anisotropic thermoelectric crystals were chosen as the semiconducting phase of the composite, while Copper was chosen as the conducting phase of the composite. The material properties are listed in Table 1. The thermoelectric properties of Bi 2 Te 3 single crystal were measured at 300 K, the thermoelectric properties of In 4 Se 2.25 single crystal were measured at 600 K, and the thermoelectric properties of SnSe single crystal were measured at 700 K. The Copper served as the fibrous phase in the fibrous composite thermoelectric materials; its thermoelectric properties at 600 K and 700 K are also given in Table 1. It should be noticed that, in transverse thermoelectric composites, the transverse ZT matrix is anisotropic. The study made use of engineered anisotropy in composite materials and optimized the transverse ZT with respect to one specific element in the anisotropic ZT matrix. The anisotropic ZT values for other elements in the matrix are not discussed.
The semiconducting materials used in this comparison, i.e., Bi 2 Te 3 , In 4 Se 2.25 , and SnSe, all belong to planar isotropic material. Therefore, for both 1D and 2D inclusion composites consisting of semiconducting crystal and isotropic Copper, two representative configurations were used. Assuming the local material property axis as u i v i w i (where the subscript i differentiates the type of materials), and the isotropy plane of material lies in the u i v i plane. For fibrous composite materials, the definition of the two configurations were explained in previous sections of this study. For layered composite materials, in configuration III, the u i v i plane aligns parallel to the layered plane of materials; in configuration IV, the u i v i plane aligns perpendicular to the planar surface of the layers. Besides the four configurations, the conducting properties of isotropic polycrystal Bi 2 Te 3 and SnSe, listed in Table 1, can be calculated using Reuss and Voigt models. Since Bi 2 Te 3 and SnSe single crystals have isotropic Seebeck properties, their isotropic polycrystal Seebeck properties are the same as anisotropic single crystals. The conducting properties of the isotropic polycrystals are the average of the results calculated by the Reuss and Voigt models, which is referred as 'Average RV' in Table 3, respectively. The results in Table 3 present both maximum Z trans T as well as the maximum cooling capacity (∆T max ) for composites with different anisotropic components and configurations using the derived mathematical model. It can be seen that, for composites which consist of the same combination of component materials but under different configurations, the alignment of component material's property axis in the composite has a major influence on Z trans T as well as the ∆T max values. For Bi 2 Te 3 /Copper composite, the difference in thermoelectric performances caused by the alignment of the anisotropic component's property axis was 50%. For the SnSe/Copper composite, this difference exceeded 400%. This difference was caused by the variance of properties among different material property axes in the anisotropic component phase, where larger variance usually leads to bigger variance in the Z trans T and ∆T max values of a composite.
When the cooling performance of the transverse thermoelectric was compared under the same component combination but with different inclusion types, it was found that for the composite with the same component volume fraction, the fibrous and layered composites yielded very similar ∆T max as well as Z trans T values. However, it should be noted that the peak performances of the layered and fibrous composites under the same volume fraction were not identical to each other. The ∆T max values were rounded up to the nearest integer, and the maximum Z trans T values were rounded up to the second decimal in Table 3. Although according to Table 3, the Z trans T and ∆T max values in between different configurations have same values, it should be noted that none of the results in Table 3 are exactly identical to one another.
By comparing the results between the composite with anisotropic component material and isotropic component material, it was found that the anisotropic component in single-crystal form in both the layered transverse thermoelectric composite and the fibrous transverse thermoelectric composite can provide a better cooling performance compared to their isotropic polycrystal counterpart. For the Bi 2 Te 3 /Copper composite at 300 K, the composite with the anisotropic Bi 2 Te 3 single crystal improved the maximum Z trans T and ∆T max by as much as 15% compared to the composite with the isotropic Bi 2 Te 3 polycrystal. For the SnSe/Copper composite at 700 K, the improvement in the maximum Z trans T and ∆T max for composite with SnSe single crystal component was as much as 51% compared to composite with isotropic SnSe polycrystal components. For the In 4 Se 2.25 /Copper composite, the single-crystal form of In 4 Se 2.25 had anisotropic Seebeck properties, but there are no existing studies regarding the effective properties of polycrystals with anisotropic Seebeck properties. Therefore, the comparison on the cooling performances for the In 4 Se 2.25 /Copper composite between composites with isotropic and anisotropic In 4 Se 2.25 phase properties was not presented.

Conclusions
This study investigated the transverse thermoelectric properties of fibrous composites with anisotropic component materials. A mathematical model was built for predicting the transverse thermoelectric figure of merit (Z trans T) and maximum cooling capacity (∆T max ) of the composite. The effectiveness of the mathematical model was verified by finite element simulations. The agreement among the two approaches indicated that the mathematical model can serve as an efficient tool for selecting and screening prospecting candidates for fibrous transverse thermoelectric composites with anisotropic material components. A case study using anisotropic Bi 2 Te 3 polycrystal as the matrix and isotropic Copper as the fiber was performed and a ∆T max of 34 K was reached.
The variance in the maximum Z trans T and ∆T max values for both the layered and fibrous transverse thermoelectric composites was investigated with respect to the possible anisotropic properties of component phase. The results showed that by enhancing the anisotropic profile of polycrystal, the maximum Z trans T and ∆T max for both the layered and fibrous transverse thermoelectric composites can be improved. For the SnSe/Copper composite at 700 K, the improvement of maximum Z trans T and ∆T max values for the composite with anisotropic SnSe single-crystal components can be as much as 51% compared to the composites with isotropic SnSe polycrystals.
This study also showed that the alignment of the component's local property axes in the composite can lead to significant variance in the Z trans T and ∆T max values of the composite. For the Bi 2 Te 3 /Copper composite, the difference in the thermoelectric performance caused by the alignment of the anisotropic component's property axis was 50%. For the SnSe/Copper composite, this difference exceeded 400%. This discrepancy was mainly caused by the variance in the anisotropic properties among different material property axis directions in the component phase.