Temperature dependence of the Seebeck coefficient for mixed semiconducting and metallic single-wall carbon nanotube bundles

The temperature (T) dependence of the Seebeck coefficient (S) for single-wall carbon nanotube (SWCNT) bundles was systematically investigated as a function of the chemical potential (μ) through theoretical simulations employing non-equilibrium Green’s function theory. The bundles were modeled as laterally aligned parallel circuits of semiconducting and metallic SWCNTs. The T dependence of S varied substantially with μ and with metallic SWCNT content. The calculated results semi-quantitatively reproduced the typical behavior observed experimentally for SWCNT films with chemical doping reported previously.

S ingle-wall carbon nanotubes (SWCNTs) are flexible and lightweight thermoelectric materials that exhibit high thermoelectric performance. [1][2][3][4][5][6][7][8][9][10][11][12][13][14][15][16][17][18] In bulk SWCNTs, a thermoelectric power factor (P) of as much as 2000 μW m -1 K -2 has been reported, 4) which is almost the same magnitude as that for commercial Bi-Te systems. However, the non-dimensional figure of merit ZT values are much smaller than those for Bi-Te systems. The thermoelectric properties may be enhanced by improving the hierarchic structures of the SWCNT films because bulk SWCNT films are usually composed of many randomly entangled bundles. 1,2,19) Each bundle consists of many SWCNTs with different structures, characterized by the chiral index n m , ( ) with integers n and m. Therefore, the macroscopic thermoelectric properties of the bulk are expected to be determined not only by the intrinsic properties of individual SWCNTs but also by such hierarchic structures.
A previous study 18) has suggested that the Seebeck coefficient (S) for SWCNT films is almost entirely determined by the bundles in the films, where each bundle was modeled as laterally aligned parallel circuits of semiconducting (s-) and metallic (m-)SWCNTs. The absolute value of S obtained from experiments conducted at room temperature was reproduced well by calculations. In this study, we examined the temperature (T) dependence of S for bundles in order to obtain a deeper understanding of S in SWCNT films.
The intrinsic conductance (G) and S for individual SWCNTs were calculated for the same model as described in previous reports. 11,12,18) Rolled-up structures of graphene ribbons with a carbon-carbon bond length of 0.142 nm were used as SWCNT structures without any geometry optimization. As in previous studies, 18,20) we calculated the transmission function for carriers with an energy ε, z e , ( ) by the non-equilibrium Green's function method and extended Hückel theory, using the software Atomistix ToolKit (ATK) developed by Quantum Wise Ltd. (www.quantumwise.com). The empirical potentials, so-called Cerda.Carbon [graphite] in the ATK software (http://quantumwise.com/documents/manuals/ATK-2014/ReferenceManual/ index.html/), were used in the Hückel basis set with a 0 eV vacuum level. The calculations were carried out for several electron temperatures (T) between 50 K and 500 K.
It is known that S has two contributions: (i) a ballistic contribution, which is related to the energy dependence of the electron density of states (DOS) and (ii) a diffusive contribution, which is related to the energy dependence of the diffusion coefficient. 14,21,22) We assumed that in the present calculations the ballistic contribution dominates the observed values. This assumption may be suitably applied to s-SWCNTs at high temperatures because a relatively large contribution from the ballistic term is expected in the present doping regime. Indeed, the S values for SWCNT films at ∼300 K were well reproduced by the ballistic term. 18) In the Landauer theory of electronic transport, 23,24) G and S are given by Here, q, h, and f are charge of the carriers, Plank's constant, and the Fermi-Dirac distribution function, respectively μ, which is the chemical potential of the system, can be experimentally controlled by carrier doping. 6,7,[11][12][13] In the present paper, we focus on the "lightly hole-doped" regime of m -< < -0.8 0.2 eV. However, it should be noted that the behavior in the "lightly electron-doped" regime would be essentially the same owing to the nearly symmetric band structures of SWCNTs for hole and electron doping.
The power factor (P) is usually defined as where σ is the electrical conductivity. However, P in the present paper is defined instead as where S and G are the Seebeck coefficient and the electrical conductance G for individual SWCNTs, respectively. This is the power factor per SWCNT.
Next, using the results for the individual SWCNTs, laterally aligned parallel circuits of SWCNTs 18) as illustrated in Fig. 1, with an m-SWCNT content β, were calculated. When there are two channels in parallel due to s-SWCNTs and m-SWCNTs, the K n ( = n 0 or 1) value for the circuit is where the superscripts m and s denote the contributions from m-SWCNTs and s-SWCNTs, respectively. Thus, the corresponding Seebeck coefficient for the circuit can be expressed as where S m s ( ) and G m s ( ) are the Seebeck coefficient and the electrical conductance for the individual intrinsic m(s)-SWCNT, respectively. The power factor P for the circuit is defined by Eq. (4) in the present paper. β is given by where N m and N s are the numbers of mand s-SWCNTs in the circuit, respectively.
First, we present the T dependence of S and G for an s-SWCNT with a chiral index (8, 0) and for an m-SWCNT with a chiral index (5,5) in the lightly hole-doped region, m -< < -0.8 0.2 eV, for several temperatures between 50 K and 500 K.
The results for the individual (8, 0) s-SWCNT are shown in Fig. 2(a). The top of the valence band is located at m m = » -0.526 eV. 0 It is found that G and S exhibit metallic and semiconducting behavior for m m < 0 and m m > , 0 respectively. For example, S and G 1/ increase with decreasing T when μ is located in the semiconducting band gap, 0 This is a well-known behavior established in previous studies. 17,18,21,22) On the other hand, S and G become metallic when μ is located within the valence band, m m < ; 0 S decreases and G approaches the value for m-SWCNTs with decreasing temperature.
The results for the individual (5, 5) m-SWCNTs are shown in Fig. 2(b). G is almost independent of T because the present calculation was performed in the ballistic regime. G is also independent of μ in the present μ region because of the assumption of ballistic transport. S decreases monotonically with decreasing T, i.e., it shows metallic behavior. However, its magnitude is substantially smaller than that for s-SWCNTs. This is expected on the basis of the Mott formula, which can be applied to metals: Thus, in the case of m-SWCNTs, the diffusive contribution to S might be important.
As expected, G for b = 5% and 30% increases with decreasing temperature for m m < 0 within the valence bands and decreases for μ within the band gap m m -~> > k T B 0 ( ( ) ) because it is dominated by the T dependence for the s-SWCNTs. However, the values at the lowest temperatures remain finite in all cases because G is limited by the metallic value for the s-and m-SWCNTs.
On the other hand, the S T ( ) of the mixed parallel circuits is quite different from those of the pure s-SWCNT circuits. While the S T ( ) of individual s-SWCNTs monotonically increases with decreasing temperature for m m -~> > k T , B 0 ( ) as shown by the dashed lines in Fig. 2(a), those in the mixed circuits are seen to show different behaviors depending on μ, and to exhibit a peak. The S T ( ) of the mixed circuits monotonically decreases with decreasing temperature at low temperatures, as explained by Eq. 5 for S of the mixed circuits. Because G s steeply decreases with decreasing temperature while G m and S m are nearly constant, The peak seen in the S-T relationship moves to higher temperature as μ is reduced to the top of the valence band, m m = . 0 The peak also moves to higher temperature with increasing m-SWCNT content, β. Such behavior is easily deduced from Fig. 3(b), where S is plotted as a function of μ for T values of 100 K, 300 K, and 500 K, and is seen to exhibit a peak. This can be inferred from the approximate form for m S : / it is found that the m S ( ) peak moves to higher μ values with increasing T. Thus, for appropriate μ values, S T ( ) exhibits a peak in the specific T range we examine. In Fig. 3(b), for example, a peak appears around 300 K for m m = .
2 Figure 3(b) also shows the power factor, m P .
( ) It is seen that the m P ( ) and m S ( ) maxima are both independent of temperature. However, the μ values where the maxima appear increase with temperature.
The calculation results can be compared with the experimental results for SWCNT films with chemical doping. 6) Figure 4(a) shows the T dependence of S for films enriched with s-SWCNTs. The nominal m-SWCNT content, β, was lower than 5%. It is well known that pristine films are already p-type. Further p-type doping was achieved chemically using HCl, H 2 SO 3 , and HNO 3 , whereas annealing in vacuum led to de-doping, as shown in Fig. 4(d). Upon p-type doping, the film resistivity (ρ) decreases and S exhibits a peak corresponding to the change in μ. The S-ρ relationship has been well established in previous studies. 11,18) The calculation results are shown by solid lines in Fig. 4(b) for fixed μ values. We found that the typical behavior observed for the annealed and pristine films in the upper panels is semi-quantitatively reproduced by calculation with It is important to note that the μ value used in the calculations consistently decreases with additional p-type doping or decreasing r, as shown in Fig. 4(d). Similarly, the β dependence is reproduced well by the calculations (see Fig. 5). Therefore, the overall behaviors observed experimentally, such as the absolute values for S at room temperature and qualitative T dependence of S for different μ and β values, were reproduced well by the present calculations.
Recently, it was reported that S T ( ) decreases with decreasing temperature irrespective of the carrier density or the Fermi level examined in high purity s-SWCNT samples. 25) It might have failed to reproduce observations of the intrinsic behaviors for S T s ( ) as shown by the dashed lines in Fig. 2 6) With p-type doping or decreasing μ, ρ decreases monotonically while S exhibits a peak. In the calculations, (b) and (c), β was assumed to be 5%.