THERMOELECTRIC CONVERSION MATERIAL, THERMOELECTRIC CONVERSION ELEMENT, THERMOELECTRIC CONVERSION MODULE, METHOD OF POWER GENERATION, AND METHOD OF HEAT TRANSFER

BACKGROUND
1. Technical Field

The present disclosure relates to a thermoelectric conversion material, a thermoelectric conversion element, a thermoelectric conversion module, a method of power generation, and a method of heat transfer.

2. Description of the Related Art

A thermoelectric conversion material containing Mg is conventionally known. For example, Japanese Patent No. 6127281 (hereinafter referred to as PTL 1) discloses a thermoelectric conversion material represented by the chemical formula Mg_3+mA_aB_bD_2-eE_eand a method of producing the thermoelectric conversion material. In the formula, A represents at least one selected from the group consisting of Ca, Sr, Ba and Yb. B represents at least one selected from the group consisting of Mn and Zn. D represents at least one selected from the group consisting of Sb and Bi. E represents at least one selected from the group consisting of Se and Te. The value of m is greater than or equal to −0.39 and less than or equal to 0.42, the value of a is greater than or equal to 0 and less than or equal to 0.12, the value of b is greater than or equal to 0 and less than or equal to 0.48, and the value of e is greater than or equal to 0.001 and less than or equal to 0.06.

Japanese Unexamined Patent Application Publication No. 2018-190953 (hereinafter referred to as PTL 2) discloses a thermoelectric conversion material represented by the chemical formula Mg_3+m-aA_aB_2-c-eC_cE_eand a method of producing the thermoelectric conversion material. In the formula, the element A represents at least one selected from the group consisting of Ca, Sr, Ba, Nb, Zn, and Al. The element B represents at least one selected from the group consisting of Sb and Bi. The element C represents at least one selected from the group consisting of Mn, Si, and Cr. The element E represents at least one selected from the group consisting of Se and Te. The value of m is greater than or equal to −0.1 and less than or equal to 0.4, the value of a is greater than or equal to 0 and less than or equal to 0.1, the value of c is greater than or equal to 0 and less than or equal to 0.1, and the value of e is greater than or equal to 0.001 and less than or equal to 0.06.

H. Tamaki et al. disclose a polycrystalline thermoelectric conversion material represented by the chemical formula Mg_3+δSb_1.5Bi_0.49Te_0.01and a method of producing the polycrystalline thermoelectric conversion material in “Isotropic Conduction Network and Defect Chemistry in Mg_3+δSb₂-Based Layered Zintl Compounds with High Thermoelectric Performance”, Advanced Materials, (USA), 2016, Vol. 28, issue 46, p. 10182-10187 (hereinafter referred to as NPL 1). In this chemical formula, the value of δ is 0.1, 0.2, or 0.3.

K. Imasato et al. disclose a monocrystalline thermoelectric conversion material represented by the chemical formula Mg₃Sb₂and a method of producing the monocrystalline thermoelectric conversion material in “Metallic n-Type Mg₃Sb₂Single Crystals Demonstrate the Absence of Ionized Impurity Scattering and Enhanced Thermoelectric Performance”, Advanced Materials, (USA), 2020, Vol. 32, issue 16, p. 1908218 (hereinafter referred to as NPL 2).

J. Zhangetal discloses a thermoelectric conversion material represented by the chemical formula Mg₃Sb_1.5-0.5xBi_0.5-0.5xTe_xand a method of producing the thermoelectric conversion material in “Discovery of high-performance low-cost n-type Mg₃Sb₂-based thermoelectric materials with multi-valley conduction bands”, Nature Communications, (UK), 2017, Vol. 8, Article number 13901 (hereinafter referred to as NPL 3). In this chemical formula, the value of x is 0.04, 0.05, 0.08, or 0.20.

V. Ponnambalam et al. disclose a thermoelectric conversion material represented by the chemical formula Mg₃Bi_2-xPn_xin “On the Thermoelectric Properties of Zintl Compounds Mg₃Bi_2-xPn_x(Pn=P and Sb)”, Journal of Electronic Materials, (USA), 2013, Vol. 42, No. 7, p. 1307-1312 (hereinafter referred to as NPL 4). In this chemical formula, Pn is P or Sb.

S. Kim et al. disclose a thermoelectric conversion material represented by the chemical formula Mg_3-xMn_xSb₂and a method of producing the thermoelectric conversion material in “Thermoelectric properties of Mn-doped Mg—Sb single crystals”, Journal of Materials Chemistry A, (UK), 2014, Vol. 2, p. 12311-12316 (hereinafter referred to as NPL 5). In this chemical formula, x satisfies the condition of 0≤x≤0.4.

X. Shi et al. disclose a thermoelectric conversion material represented by the chemical formula Mg_3.05-xSc_xSbBi and a method of producing the thermoelectric conversion material in “Efficient Sc-doped Mg_3.05-xSc_xSbBi thermoelectrics near room temperature”, Chemistry of Materials, (USA), 2019, Vol. 31, No. 21, p. 8987-8994 (hereinafter referred to as NPL 6). In this chemical formula, the value of x is 0.001, 0.0015, 0.003, 0.005, 0.009, 0.012, 0.015, 0.018, 0.020, 0.025, or 0.030.

S. W. Song et al. disclose a thermoelectric conversion material represented by the chemical formula Mg₃₀₀Y_xSb_1.5Bi_0.5and a method of producing the thermoelectric conversion material in “Joint effect of magnesium and yttrium on enhancing thermoelectric properties of n-type Zintl Mg_3+δY_0.02Sb_1.5Bi_0.5”, Materials Today Physics, (Netherlands), 2019, Vol. 8, p. 25-33 (hereinafter referred to as NPL 7). In this chemical formula, the value of x is 0.03, 0.035, or 0.04.

K. Imasato et al. disclose a thermoelectric conversion material represented by the chemical formula Mg_3.05-xLa_xSb_1.5Bi_0.5and a method of producing the thermoelectric conversion material in “Improved stability and high thermoelectric performance through cation site doping in n-type La-doped Mg₃Sb_1.5Bi_0.5”, Journal of Materials Chemistry A, (UK), 2018, Vol. 6, p. 19941-19946 (hereinafter referred to as NPL 8). In this chemical formula, the value of x is 0.005, 0.01, or 0.03.

J. Li et al. disclose a thermoelectric conversion material represented by the chemical formula (Mg, Ce)₃Sb₂in “Defect Chemistry for N-Type Doping of Mg₃Sb₂-Based Thermoelectric Materials”, Journal of Physical Chemistry C, (USA), 2019, Vol. 123, p. 20781-20788 (hereinafter referred to as NPL 9).

K. Imasato et al. disclose the value of the lattice thermal conductivity of the material represented by the chemical formula Mg_3.05(Sb_1-xBi_x)_1.99Te_0.001in “Exceptional thermoelectric performance in Mg₃Sb_0.6Bi_1.4for low-grade waste heat recovery”, Energy & Environmental Science, (UK), 2019, Vol. 12, p. 965-971 (hereinafter referred to as NPL 10).

SUMMARY

One non-limiting and exemplary embodiment provides a novel thermoelectric conversion material.

In one general aspect, the techniques disclosed here feature a thermoelectric conversion material that has a La₂O₃-type crystal structure and is of n-type, and the thermoelectric conversion material has a composition represented by the following formula (1).

Mg_3+m-a-bA_aB_bD_2-e-fE_eF_f formula (1)

wherein D is at least one element selected from the group consisting of Sb and Bi, E is at least one element selected from the group consisting of P and As, m is a value of greater than or equal to −0.1 and less than or equal to 0.4, e is a value of greater than or equal to 0.001 and less than or equal to 0.25, A is at least one element selected from the group consisting of Y, Sc, La, and Ce, F is at least one element selected from the group consisting of Se and Te, a and f are values that satisfy a condition of 0.0001≤a+f≤0.06, B is at least one element selected from the group consisting of Mn and Zn, and b is a value of greater than or equal to 0 and less than or equal to 0.25.

According to the present disclosure, a novel thermoelectric conversion material can be provided.

It should be noted that general or specific embodiments may be implemented as a system, a method, an integrated circuit, a computer program, a storage medium, or any selective combination thereof.

Additional benefits and advantages of the disclosed embodiments will become apparent from the specification and drawings. The benefits and/or advantages may be individually obtained by the various embodiments and features of the specification and drawings, which need not all be provided in order to obtain one or more of such benefits and/or advantages.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic view of a La₂O₃-type crystal structure;

FIG. 2 is a graph indicating an example of simulation results for an X-ray diffraction pattern of a La₂O₃-type crystal structure;

FIG. 3 is a schematic view of a La₂O₃-type crystal structure of a thermoelectric conversion material according to the present disclosure; and

FIG. 4 is a schematic view illustrating an example of a thermoelectric conversion module according to the present disclosure.

DETAILED DESCRIPTIONS
Underlying Knowledge Forming Basis of the Present Disclosure

The performance of a thermoelectric conversion material is indicated by the thermoelectric figure of merit ZT. The thermoelectric figure of merit ZT is indicated as ZT=S²σT/κ by using the Seebeck coefficient S, the electrical conductivity σ, the thermal conductivity κ, and the absolute temperature T. Here, the thermal conductivity κ is indicted as κ=κ_e+κ_latby using the electron thermal conductivity κ_eand the lattice thermal conductivity κ_lat.

PTL 1 discloses an n-type thermoelectric conversion material represented by the chemical formula Mg_3+mA_aB_bD_2-eE_e, which is based on Mg₃(Sb,Bi)₂. In PTL 1, E in this chemical formula is represented by at least one selected from the group consisting of Se and Te. In addition, the value of e is greater than or equal to 0.001 and less than or equal to 0.06. Under these conditions, the thermoelectric figure of merit ZT of the n-type thermoelectric conversion material represented by this chemical formula is 0.5 at 300 K and 1.5 at 700 K. These values of the thermoelectric figure of merit ZT are higher than the values of the thermoelectric figure of merit ZT of a thermoelectric conversion material that is represented by the chemical formula in which E is not contained, in other words, the chemical formula in which the value of e is 0.

The present inventors developed a new method that can more reliably predict the thermoelectric figure of merit ZT than a conventional method. More specifically, the present inventors combined calculation of the electronic state using the first principles calculation called density-functional theory (DFT) and a unique prediction model of the thermoelectric figure of merit ZT developed by the present inventors. In the present disclosure, comparisons between the empirical outcomes and the prediction outcomes of the thermoelectric figure of merit ZT were made for the thermoelectric conversion materials having the composition represented by Mg_3.05Sb_xBi_1.99-xTe_0.01to confirm the validity of the prediction model of the thermoelectric figure of merit ZT developed by the present inventors. As a result, the prediction model of the thermoelectric figure of merit ZT developed by the present inventors accurately reproduced the physical property values such as the Seebeck coefficient S, the electrical conductivity σ, the thermal conductivity κ, and the thermoelectric figure of merit ZT of the n-type thermoelectric conversion material based on Mg₃(Sb,Bi)₂.

In view of the above, the present inventors calculated and predicted the thermoelectric figures of merit ZT of materials having unexamined compositions among crystalline materials based on Mg₃(Sb,Bi)₂by using a combination of the calculation of the electronic state and the prediction model of the thermoelectric figure of merit ZT. The results showed that, when the thermoelectric conversion material is of n-type, the presence of at least one of P and As in the thermoelectric conversion material allows ZT to be higher than that of the Mg₃(Sb,Bi)₂base itself. It is important to verify that a thermoelectric conversion material having a particular composition is actually synthesizable. Thus, the present inventors predicted, by using defect formation energy calculated with DFT, a range in which the composition of the thermoelectric conversion material having the calculated and predicted thermoelectric figure of merit ZT is stable. This resulted in new finding of a thermoelectric conversion material of the present disclosure that has an actually synthesizable composition.

DESCRIPTION OF EMBODIMENTS

Hereinafter, embodiments of the present disclosure will be described with reference to the drawings.

The thermoelectric conversion material of the present disclosure has a La₂O₃-type crystal structure and is of n-type. In addition, the thermoelectric conversion material of the present disclosure has a composition represented by the following formula (1). In the formula (1), D is at least one element selected from the group consisting of Sb and Bi. Furthermore, E is at least one element selected from the group consisting of P and As. The value of m is greater than or equal to −0.1 and less than or equal to 0.4. The value of e is greater than or equal to 0.001 and less than or equal to 0.25. A is at least one element selected from the group consisting of Y, Sc, La, and Ce. F is at least one element selected from the group consisting of Se and Te. The values of a and f satisfy the condition of 0.0001≤a+f≤0.06. B is at least one element selected from the group consisting of Mn and Zn. The value of b is greater than or equal to 0 and less than or equal to 0.25.

Mg_3+m-a-bA_aB_bD_2-e-fE_eF_f formula (1)

FIG. 1 schematically illustrates the La₂O₃-type crystal structure. For example, PTL 1 and PTL 2 state that a material based on Mg₃(Sb,Bi)₂may have a La₂O₃-type crystal structure or a CaAl₂Si₂-type crystal structure, which belong to the space group P-3m1. (Sb,Bi) refers to at least one selected from the group consisting of Sb and Bi. FIG. 2 shows an example of simulation results for an X-ray diffraction pattern of Mg₃(Sb,Bi)₂having a La₂O₃-type crystal structure. FIG. 2 shows simulation results for an X-ray diffraction pattern of a La₂O₃-type crystal structure or a CaAl₂Si₂-type crystal structure having a lattice constant in the a-axis direction of 0.457 nanometers, a lattice constant in the b-axis direction of 0.457 nanometers, and a lattice constant in the c-axis direction of 0.723 nanometers. The software VESTA available from https://jp-minerals.org/vesta/jp/download.html was used to provide the simulation results shown in FIG. 2. FIG. 2 has auxiliary lines, which indicate values of diffraction angles corresponding to the peaks of the X-ray diffraction pattern, between the X-ray diffraction pattern and the horizontal axis.

By checking the presence of diffraction peaks that characterize the La₂O₃-type crystal structure with an X-ray diffraction technique, it is possible to determine whether the thermoelectric conversion material has the La₂O₃-type crystal structure.

The thermoelectric conversion material of the present disclosure may be monocrystalline or polycrystalline. FIG. 3 schematically illustrates a La₂O₃-type crystal structure of the thermoelectric conversion material of the present disclosure. This crystal structure may have defects in which some of the Mg sites C1 are replaced by at least one element selected from the group consisting of Y, Sc, La, and Ce. Furthermore, this crystal structure may have defects in which some of the Mg sites C2 are replaced by at least one element selected from the group consisting of Mn and Zn. Furthermore, the crystal structure has defects in which some of the sites C3 composed of at least one element selected from the group consisting of Sb and Bi are replaced by at least one element selected from the group consisting of P and As. The crystal structure may have defects in which some other sites C3 are replaced by at least one element selected from the group consisting of Se and Te.

Such defects in the crystal structure of the thermoelectric conversion material may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material of the present disclosure relative to the intensity peaks of the X-ray diffraction pattern of Mg₃(Sb,Bi)₂indicated in FIG. 2. The shift in the intensity peaks of the X-ray diffraction pattern results from the change in the lattice constant of the crystal structure. The intensity peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant of the crystal structure increases, and the intensity peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases. For example, NPL 4 shows the X-ray diffraction pattern of the thermoelectric conversion material represented by the chemical formula Mg₃Bi_2-xPn_xand states that the peak positions shift depending on the compositions. In this chemical formula, Pn is P or Sb.

In the thermoelectric conversion material, E in the formula (1) may include P. In such a case, a thermoelectric conversion material having a thermoelectric figure of merit ZT higher than the thermoelectric figure of merit ZT of the material based on Mg₃(Sb,Bi)₂and not containing P or As is readily produced.

In the thermoelectric conversion material, E in the formula (1) may include As. In such a case, a thermoelectric conversion material having a thermoelectric figure of merit ZT higher than the thermoelectric figure of merit ZT of the material based on Mg₃(Sb,Bi)₂and not containing P or As is readily produced.

D in the formula (1) may include Sb and Bi, and the composition of the thermoelectric conversion material may be a composition represented by the following formula (2). The symbols representing the atoms and the symbols representing the number of atoms in the formula (2) have the same meanings as the symbols representing the atoms and the symbols representing the number of atoms in the formula (1). In the formula (2), the value of x is greater than or equal to 0.2 and less than or equal to 1.5. In this case, a thermoelectric conversion material having a thermoelectric figure of merit ZT higher than the thermoelectric figure of merit ZT of the material based on Mg₃(Sb,Bi)₂and not containing P or As is readily produced.

Mg_3+m-a-bA_aB_bSb_xBi_2-e-f-xE_eF_f formula (2)

In the formula (1) representing the composition of the thermoelectric conversion material, the value of a may be 0. In such a case, a thermoelectric conversion material having a thermoelectric figure of merit ZT higher than the thermoelectric figure of merit ZT of the material based on Mg₃(Sb,Bi)₂and not containing P or As is also readily produced. Furthermore, a thermoelectric conversion material can be produced without using a material containing Y, Sc, La, or Ce.

In the formula (1) representing the composition of the thermoelectric conversion material, the value of a may be greater than or equal to 0.0001 and less than or equal to 0.04, and the value of f may be 0. In such a case, a thermoelectric conversion material having a thermoelectric figure of merit ZT higher than the thermoelectric figure of merit ZT of the material based on Mg₃(Sb,Bi)₂and not containing P or As is also readily produced. Furthermore, a thermoelectric conversion material can be produced without using a material containing Se or Te.

The thermoelectric conversion material having the composition represented by the formula (1) is stable and has a single crystalline phase in which multiple kinds of crystalline phases are not formed, or a single phase. The composition represented by the formula (1) corresponds to a stable composition range of Mg_3+m-a-bA_aB_bD_2-e-fE_eF_f. The stable composition range is a composition range which allows generation of only a crystalline material having the composition of Mg_3+m-a-bA_aB_bD_2-e-fE_eF_f, in other words, a composition range which allows Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fto stably form a solid solution. Outside the stable composition range, a crystalline phase of a composition other than the crystalline material having the composition of Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fmay be precipitated, and it may be impossible to generate only a crystalline material having the composition of Mg_3+m-a-bA_aB_bD_2-e-fE_eF_f. In other words, this suggests that a solid solution is not stably formed outside the stable composition range.

The value of f, the value of b, the value of m, and the value of a in the formula (1) can be determined, for example, with reference to the above-listed PTLs and NPLs. It is understood from PTL 1 that, for the values of f and b, the ranges of 0.0≤b≤0.48 and 0.0≤f≤0.06 can fall in the stable composition range. It is understood from PTL 2 that, for the value of m, the range of −0.1≤m≤0.4 can fall in the stable composition range. It is understood from NPL 6 that, when A is Sc, for the value of a, the range of 0.0≤a≤0.03 can fall in the stable composition range. It is understood from NPL 7 that, when A is Y, for the value of a, the range of 0.0≤a≤0.04 can fall in the stable composition range. It is understood from NPL 8 that, when A is La, for the value of a, the range of 0.0≤a≤0.03 can fall in the stable composition range. It is understood from NPL 9 that a thermoelectric conversion material can be more stably synthesized when A is Ce than when A is La.

It is understood from NPL 4 that, when E is P in the formula (1), for the value of e, the range of 0.0≤e≤0.5 can fall in the stable composition range.

In addition, when E is As in the formula (1), the range of the value of e that corresponds to the stable composition range can be determined as follows. Specifically, the following calculation can be performed to determine the range of the value of e that allows the La₂O₃-type crystal structure to be stable in the crystalline material having the composition of Mg₃Bi_2-eAs_e, which is based on Mg₃(Sb,Bi)₂. This calculation method is based on the defect formation theory of semiconductors disclosed by C. G. Van de Walle et al. in “First-principles calculations for defects and impurities: Applications to III-nitrides”, Journal of Applied Physics, (USA), 2004, Vol. 95, p. 3581-3879.

First, in Mg₃Bi₂, the defect formation energy E_formin the case where Bi sites are replaced by As is estimated using the formula (3) below. In the formula (3), E_defectis the total energy in the presence of defects, and E_pureis the total energy of Mg₃Bi₂in the absence of defects. In addition, n_iis an increase or decrease in the content of the i-th constituent element caused by defects, μ_iis the chemical potential of the i-th element, q is the charge amount of the defects, and E_Fis the Fermi energy of an electron. These energy values can be estimated by using a calculation technique based on DFT within the generalized gradient approximation.

E
_form(μ_i,q,E_F)=E_defect−E_pure−Σn_iμ_i+qE_F formula (3)

The volume density N_Dof the defects can be estimated based on the following formula (4) according to a Boltzmann distribution by using the defect formation energy E_formobtained by the formula (3). In the formula (4), N_siteis the volume density of sites that possibly have a concerned defect, KB is the Boltzmann's constant, and T is the absolute temperature. The permissible range of a chemical potential μ_iof Bi atoms and As atoms was calculated by using the same method as the technique described in Journal of Materials Chemistry A, (UK), 2014, Vol. 2, p. 11235-11245. Furthermore, the defect density range in which Bi sites are replaced by As was estimated by using the relational expression (4).

N
_D(μ_i,q,E_F)=N_site×exp[−E_form(μ_i,q,E_F)/k_BT] formula (4)

The results of the calculations indicate that, for the crystalline material having the composition of Mg₃Bi_2-eAs_e, within the range of 0.0≤e≤0.70, a single-phase La₂O₃-type crystal is obtained. When e is in the range of 0.0≤e≤0.70, the Mg₃Bi_2-eAs_ecrystalline material can stably form a solid solution.

The Bi atom radius of 0.150 nm is closer to the As atom radius of 0.120 nm than to the P atom radius of 0.109 nm. Thus, the range of the value of e that corresponds to the stable composition range in the case where E is As is theoretically broader than the range of the value of e that corresponds to the stable composition range in the case where E is P. Thus, the validity of the calculation is indicated by the result obtained through the above calculation in which the range of the value of e, 0.0≤e≤0.70, which corresponds to the stable composition range in the case where E is As is broader than the range of the value of e, 0.0≤e≤0.5, which corresponds to the stable composition range in the case where E is P referred to in NPL 4. The method for calculating the stable composition range of Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fis considered as reliable.

Furthermore, it was determined that, by the same method for calculating the stable composition range, the defect formation energy in the case where A is Sc and in the case where A is La is lower than the defect formation energy in the case where A is Y and a thermoelectric conversion material having a single phase is stably synthesizable. Based on the result and the descriptions of NPL 6 to NPL 9, the desirable value of a in the composition represented by the formula (1) can be determined with reference to a case in which A is Y. Thus, the formula (1) may satisfy the condition of 0.0≤a≤0.04.

The thermoelectric performance of a material can be evaluated by the thermoelectric figure of merit ZT specific to the material. The thermoelectric figure of merit ZT is defined by the following formulas (5) and (6). In the formulas (5) and (6), S, σ, κ_e, and κ_latare the Seebeck coefficient, the electrical conductivity, the thermal conductivity of electrons, and the lattice thermal conductivity, respectively, of the overall material. T is the absolute temperature under the evaluation environment. The Vienna Ab initio Simulation Package (VASP) code, the parabolic band model, and the Kane band model were used in combination to predict S, σ, and κ_e. For the parabolic band model and the Kane band model, reference can be made to Chapters 3 and 4 of H. J. Goldsmid, “Introduction to Thermoelectricity”, Springer, 2010.

ZT=S
²
σT/κ formula (5)

κ=κ_e+κ_lat formula (6)

The formulas (7) to (11) are calculation formulas for calculating the characteristic values for the parabolic band model. The physical quantities in the formulas (7) to (11) are determined by providing an elementary quantity of the electric charge e, a band effective mass m_I, a degree of degeneracy at a band edge N_v, an average longitudinal elastic constant C_l, a deformation potential Ξ, a reduced Fermi energy η, and reduction energy at a band edge ΔE. The reduced Fermi energy ηequals to E_F/k_BT, and the reduction energy at a band edge ΔE equals to E/k_BT. The plus-minus sign and minus-plus sign in the formulas of S_p(η) and F_i(η) include the upper signs for the conduction band and the lower signs for the valence band.

S
_p(η)=−k_B/e×[F₂(η)/F₁(η)∓η±ΔE] formula (7)

σ_p=2e²ℏN_vC_l/3πm_lΞ²×F₁(η) formula (8)

κ_e,p=σ_p×T×(k_B/e)²×[F₃(η)/F₁(η)−(F₂(η)/F₁(η))²] formula (9)

F
_i(η)=∫_ΔE^±∞dx(±x∓ΔE)ⁱ×(−∂f_±(x,η)/∂x) formula (10)

f
₊(x,η)=1/(1+e^x-η),f₋(x,η)=1−f₊(x,η) formula (11)

The formulas (12) to (15) are calculation formulas for calculating the characteristic values for the Kane band model on the conduction band side.

S
_k
=−k
_B
/e×[¹G₋₂¹(η)/⁰G₋₂¹(η)−η+ΔE] formula (12)

σ_k=2e²ℏN_vC_l/3πm_IΞ²×⁰G₋₂¹(η) formula (13)

κ_e,k=σ_kT(k_B/e)²[²G₋₂¹(η)/⁰G₋₂¹(η)−(¹G₋₂¹(η)/⁰G₋₂¹(η))²] formula (14)

ⁱ
G
_k
^j(η)=3∫_ΔE^∞dx(x−ΔE)ⁱ{x−ΔE+α(x−ΔE)²}^j×[{1+2α(x−ΔE)}²+2]^k/2×(−∂f₊(x,η)/∂x) formula (15)

The above-described physical quantities are determined by providing a parameter α, which indicates displacement from a parabolic structure, to the physical quantities for the parabolic band model. S, σ, and κ_eof the overall material are determined by the following formulas (16), (17), and (18) using these physical quantities. In these formulas, i and j are indexes of the band obtained by the VASP code and include indexes of the parabolic band and the Kane band.

S=Σ
_i
S
_iσ_i/Σ_iσ_i formula (16)

σ=Σ_iσ_i formula (17)

κ_e=Σ_iκ_e,i+(T/2)×Σ_i,jσ_iσ_j(S_i−S_j)²/Σ_iσ_i formula (18)

The reduced Fermi energy is calculated by using a defect concentration of A and F in the formula (1), which will be described later. The reduction energy at a band edge ΔE=E/k_BT and a band effective mass m_Iof the parabolic band are calculated by DFT using the VASP code. The average longitudinal elastic constant C_land the deformation potential function Ξ, are determined so as to reproduce the electrical conductivity of the Mg₃(Sb,Bi)₂crystalline material, which is the base material.

The parameter α of the Kane band and the band effective mass m_Ican be calculated by fitting a band structure in three-directions (k₁=k_x, k_y, k_z) obtained by the VASP code according to the following formulas (19) and (20).

$\begin{matrix} ℏ^{2} k_{l}^{2} / 2 m_{e} = \frac{m_{k_{l}}}{m_{e}} E (k_{1}) (1 + \frac{k_{B} T}{α} E (k_{l})) & formula (19) \end{matrix}$

$\begin{matrix} 1 / m 1 = (1 / m_{k_{x}} + 1 / m_{k_{y}} + 1 / m_{k_{z}}) / 3 & formula (20) \end{matrix}$

The lattice thermal conductivity can be calculated by fitting according to the following formula (21). In the formula (21), x is a proportion of Bi that occupies the site C3 in FIG. 3. The values of A and B can be determined to reproduce the calculated lattice thermal conductivity of Mg_3.05(Sb_1-xBi_x)_1.99Te_0.01disclosed in NPL 10.

1/κ_lat=A+B×x(1−x) formula (21)

The reduced Fermi energy and the concentration of defects can be linked to each other by the following formulas (22) and (23).

n(η)=C_K×N_K (formula (22)

n(η)=n_CB(η)+n_kane(η)−n_VB(η) formula (23)

In the formulas (22) and (23), n (η) is a carrier concentration of electrons, C_Kis a carrier activation rate of the atom K contained in A or F in the formula (1) as dopant, and N_Kis a concentration of the atom K. In the formulas (22) and (23), n_CB(η) is a carrier concentration of electrons derived from the parabolic band in the conduction band, n_kane(η) is a carrier concentration of electrons derived from the Kane band in the conduction band, and n_VB(η) is a whole carrier concentration in the valance band. These are calculated by using the following formulas (24), (25), and (26).

n
_CB(η)=ΣN_v(2m_dk_BT)^3/2/2π²ℏ³×∫_ΔE^∞dx(x−ΔE)^1/2×f₊(x,η) formula (24)

n
_kane(η)=ΣN_v(2m_dk_BT)^3/2/2π²ℏ³×∫_ΔE^∞dx{x−ΔE+α(x−ΔE)²}^1/2×{1+2α(x−ΔE)}×f₊(x,η) formula (25)

n
_VB(η)=ΣN_v(2m_dk_BT)^3/2/2π²ℏ³×∫_−∞^ΔEdx(−x+ΔE)^1/2×f₋(x,η) formula (26)

The carrier activation rate can be estimated from relation between the starting concentration of the dopant and the measured value of the carrier concentration for each crystalline material. The combination of the formulas (12), (22), and (23) can be compared with the value of the Seebeck coefficient of the base material Mg₃(Sb,Bi)₂to calculate the reduced Fermi energy, which is the parameter to predict the thermoelectric properties of a target material.

The calculation in accordance with the above-described calculation procedure can determine the thermoelectric figure of merit ZT for the compositions of the Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. Here, the value of m in the formula (1) seems to have little influence on the calculation results of the physical property values and the thermoelectric figure of merit ZT when being in the range disclosed in NPL 1. It is understood that, when the value of m is within the range disclosed in NPL 1, in the actual synthesis evaluation, the Seebeck coefficient of the material is negative, in other words, n-type thermoelectric conversion properties are exhibited, and the absolute value of the Seebeck coefficient is not changed. As described above, when n-type thermoelectric properties are exhibited, the value of m seems to have little influence on ZT. Thus, when a value in the stable composition range used in the synthesis in PTL 2 is employed as the value of m, changes in the physical property values caused by the value of m are negligible in the calculation.

The method of producing a thermoelectric conversion material is not limited to a specific method. The thermoelectric conversion material may be produced as follows, for example. Mg, at least one of Sb and Bi, at least one of P and As, and an element that can be contained as A or F as needed in the formula (1) in elemental form are weighed to be in a desired stoichiometric proportion. The weighed materials in elemental form are sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere. Then, the materials are pulverized and mixed by a planetary ball milling technique. In this process, stearic acid may be added to prevent alloy powder derived from the materials from attaching to the stainless-steel container. The alloy powder generated in this way is put into a graphite mold and is subjected to, while being pressurized, spark plasma sintering including heating using a pulsed current, to provide a bulk polycrystalline sintered object. In this way, a thermoelectric conversion material is produced. Instead of the spark plasma sintering, a known sintering technique such as hot pressing may be used. Alternatively, after the pulverization and mixing of the materials, a heating process may be performed to prepare alloy powder as a precursor, and the alloy powder may be sintered to produce a thermoelectric conversion material. Further alternatively, a metal flux method may be employed to produce a monocrystalline material to obtain a thermoelectric conversion material.

The thermoelectric conversion material according to the present disclosure may contain multiple elements as indicated by the formula (1). According to PTL 2, when the material contains elements, such as Ca, Sr, Ba, Nb, Zn, Al, Mn, Si, Cr, and Se, a thermoelectric conversion material based on Mg₃(Sb,Bi)₂can be synthesized and produced by the same method as the above-described production method. As described above, the composition represented by the formula (1) is determined based on the stable composition range. Thus, a thermoelectric conversion material having the composition represented by the formula (1) can be stably synthesized and produced by the above-described production method.

NPL 4 indicates that p-type Mg₃Bi_1.5P_0.5can be stably synthesized. The Bi atom radius of 0.150 nm is closer to the As atom radius of 0.120 nm than to the P atom radius of 0.109 nm. It is understood from this that Bi of Mg₃Bi₂is more likely to be replaced by As than by P. The above suggests that the thermoelectric conversion material having the composition represented by the formula (1) can be produced with reference to the production methods described in NPLs 1 and 2 and PTLs 1 and 2.

A thermoelectric conversion element including the thermoelectric conversion material according to the present disclosure can be provided. The thermoelectric conversion element can function as an n-type thermoelectric conversion element.

FIG. 4 illustrates an example of a thermoelectric conversion module according to the present embodiment. A thermoelectric conversion module 100 includes an n-type thermoelectric conversion element 10, a p-type thermoelectric conversion element 20, a first electrode 31, a second electrode 32, and a third electrode 33. The n-type thermoelectric conversion element 10 contains the thermoelectric conversion material according to the present disclosure. The p-type thermoelectric conversion element 20 may be a known p-type thermoelectric conversion element. The first electrode 31 electrically connects a first end of the n-type thermoelectric conversion element 10 and a first end of the p-type thermoelectric conversion element 20 to each other. The second electrode 32 is electrically connected to a second end of the n-type thermoelectric conversion element 10. The third electrode 33 is electrically connected to a second end of the p-type thermoelectric conversion element.

The thermoelectric conversion material according to the present disclosure can be employed to provide, for example, a method of power generation including the following items (Ia) and (IIa):

(Ia) providing the thermoelectric conversion material with a temperature difference; and

(IIa) deriving electric power from thermoelectromotive force generated in the thermoelectric conversion material due to the temperature difference provided in (Ia).

For example, an electrode is disposed on each of one end and another end of the thermoelectric conversion material according to the present disclosure. A temperature difference is provided such that the temperature of the one end becomes high and the temperature of the other end becomes low. This moves n-type carriers from the one end of the thermoelectric conversion material to the other end of the thermoelectric conversion material, resulting in generation of electric power.

The thermoelectric conversion material according to the present disclosure can provide, for example, a method of heat transfer including the following items (Ib) and (IIb):

(Ib) allowing a current to flow through the thermoelectric conversion material; and

(IIa) transferring heat by the current flowing in (Ib).

For example, heat is transferred from one end to another end of the thermoelectric conversion material. In this case, when the direction of the current is reversed, the direction in which heat is transferred in the thermoelectric conversion material is reversed. Thus, heat can also be transferred from the other end to the one end of the thermoelectric conversion material.

EXAMPLES

Hereinafter, the present disclosure will be described in detail with reference to the examples. However, the thermoelectric conversion material according to the present disclosure is not limited to the specific aspects described below.

To verify the validity of the prediction model based on the calculation for the material having the composition represented by the formula (1), synthesis of the Mg_3.05Sb_xBi_1.99-xTe_0.01crystalline material based on Mg₃(Sb,Bi)₂and evaluation of the thermoelectric properties were performed by the following methods.

Elemental Mg, Sb, Bi, and Te as materials were weighed to be in a desired composition ratio, and the materials were sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere having a diameter of 10 mm. Then, the materials were pulverized and mixed for two hours by the 8000D mixer/mill available from SPEX to provide a powder mixture. The generated powder mixture was put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3.05Sb_xBi_1.99-xTe_0.01based on Mg₃(Sb,Bi)₂was produced.

The produced compact was cut into strips and pellets. The samples cut into strips were subjected to measurements of the Seebeck coefficient S and the electrical conductivity a using ZEM-3 available from ADVANCE RIKO, Inc. The samples cut into pellets were subjected to evaluation of the thermal conductivity κ using LFA-447 available from NETZSCH. In this way, the performance of the produced crystalline material as the thermoelectric conversion material was examined.

Table 1 indicates the empirical values obtained by using the samples actually synthesized for the physical property values and the thermoelectric figure of merit ZT of the materials each having the composition of Mg_3.05Sb_xBi_1.99-xTe_0.01as comparative examples 1, 3, 5, 7, 9, and 11. In addition, Table 1 indicates the calculated values obtained by using the above-described prediction model, which is a combination of the VASP code, the parabolic band model, and the Kane band model, as comparative examples 2, 4, 6, 8, 10, and 12. The empirical values and the calculated values are both values at 330 K.

TABLE 1

Mg_3.05Sb_xBi_1.99−xTe_0.01

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

x
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 1 (experiment)
0.0
−136
2174
2.80
0.47

Com. Ex. 2 (calculation)
0.0
−127
2188
2.06
0.56

Com. Ex. 3 (experiment)
0.2
−132
2051
2.29
0.51

Com. Ex. 4 (calculation)
0.2
−121
2045
1.94
0.51

Com. Ex. 5 (experiment)
0.3
−135
1865
2.05
0.55

Com. Ex. 6 (calculation)
0.3
−128
1719
1.71
0.55

Com. Ex. 7 (experiment)
0.4
−142
1649
1.83
0.60

Com. Ex. 8 (calculation)
0.4
−137
1396
1.44
0.60

Com. Ex. 9 (experiment)
0.6
−159
1066
1.37
0.65

Com. Ex. 10 (calculation)
0.6
−159
1004
1.13
0.74

Com. Ex. 11 (experiment)
1.5
−192
605
1.01
0.73

Com. Ex. 12 (calculation)
1.5
−187
602
0.84
0.83

The results of the comparative examples 2, 4, 6, 8, 10, and 12, which are based on the calculation, and the results of the comparative examples 1, 3, 5, 7, 9, and 11, which are actually synthesized and empirically estimated, are substantially the same as each other. The validity of the prediction model based on the calculation is confirmed over a broad stable composition range of Sb and Bi represented by the value of x. This indicates that the above-described prediction model can be used to explain the crystalline material based on Mg₃(Sb,Bi)₂, which will be described below.

A study was further conducted on materials to which P or As was added by using the above-described prediction model having the valid calculated values over a broad stable composition range of Sb and Bi.

Examples 1 to 22

A crystalline material having a composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01can be produced as follows, for example. First, elemental Mg, Sb, Bi, Te, and P (red phosphorus) as materials were weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere. Then, the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition represented by Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by P and Te. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01is represented by the formula (1) in which the value of each of a and b is 0, D is at least one of Sb and Bi, the value of x is 0.0≤x≤1.99-e, E is P, F is Te, and the value of f is 0.01. In this crystalline material, the value of a is within the stable composition range of 0.0≤a≤0.04. In this crystalline material, the values of b and f are within the stable composition ranges derived with reference to PTL 1. The value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. Furthermore, the value of e satisfies the condition of 0.0≤e≤0.5 with reference to NPL 4.

The thermoelectric figure of merit ZT of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01was calculated by using the same method as the method of calculating the thermoelectric figure of merit ZT of the above-described crystalline material of Mg_3+m-a-bA_aB_bD_2-e-fE_eF_f. The Seebeck coefficient S and the thermoelectric figure of merit ZT of the crystalline materials having the composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01were calculated in accordance with the above-described calculation procedure using the formulas (5) to (26), for example. Here, the value of m in Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01has little influence on the physical property values and the thermoelectric figure of merit ZT when being in the range disclosed in NPL 1. It is understood that, when the value of m is in the range disclosed in NPL 1, the Seebeck coefficient of the material is negative, in other words, n-type thermoelectric properties are exhibited, and the absolute value of the Seebeck coefficient does not change in the practical synthesis evaluation. As described above, it is understood that, when a material exhibits n-type thermoelectric properties, the value of m has little influence on ZT. In the evaluation of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01, the stable composition range in the synthesis in PTL 2 was employed as m, and the changes of the physical property values due to the value of m was ignored in the following calculations. Table 2 shows the calculated values of the thermoelectric conversion properties of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01at 330 K.

TABLE 2

Mg_3+mSb_xBi_1.99−x−ePeTe_0.01

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

x
e
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 2
0.0
0.0
−127
2188
2.06
0.56

Ex. 1
0.0
0.001
−127
2202
2.06
0.57

Ex. 2
0.0
0.05
−131
2161
1.94
0.63

Ex. 3
0.0
0.125
−127
2246
1.93
0.62

Ex. 4
0.0
0.25
−118
2545
2.09
0.56

Com. Ex. 13
0.0
0.5
−75
3909
3.39
0.22

Ex. 5
0.2
0.001
−122
2034
1.94
0.51

Ex. 6
0.2
0.05
−141
1566
1.60
0.64

Ex. 7
0.2
0.125
−166
1195
1.31
0.83

Ex. 8
0.2
0.25
−182
1231
1.23
1.09

Ex. 9
0.3
0.001
−129
1708
1.70
0.55

Ex. 10
0.3
0.05
−152
1280
1.38
0.71

Ex. 11
0.3
0.125
−173
1032
1.17
0.87

Ex. 12
0.3
0.25
−184
1032
1.14
1.02

Ex. 13
0.4
0.001
−138
1387
1.44
0.61

Ex. 14
0.4
0.05
−161
1067
1.19
0.77

Ex. 15
0.4
0.125
−176
938
1.07
0.90

Ex. 16
0.4
0.25
−181
937
1.06
0.96

Ex. 17
0.6
0.001
−160
999
1.12
0.75

Ex. 18
0.6
0.05
−173
876
1.00
0.87

Ex. 19
0.6
0.125
−178
846
0.97
0.91

Ex. 20
0.6
0.25
−180
848
0.96
0.94

Ex. 21
1.0
0.001
−182
725
0.87
0.91

Ex. 22
1.0
0.05
−182
726
0.87
0.91

Ex. 23
1.0
0.125
−182
728
0.87
0.91

Ex. 24
1.0
0.25
−182
730
0.88
0.91

Ex. 25
1.5
0.001
−187
602
0.84
0.83

Ex. 26
1.5
0.05
−187
603
0.85
0.82

Ex. 27
1.5
0.25
−187
605
0.90
0.77

Ex. 28
1.74
0.001
−189
550
0.87
0.74

Ex. 29
1.74
0.05
−189
551
0.89
0.73

Ex. 30
1.74
0.25
−189
552
0.99
0.66

As indicated in Table 2, the crystalline materials having the composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01exhibited n-type thermoelectric conversion properties in which the value of the Seebeck coefficient S is negative when the condition of 0.001≤e≤0.25 is satisfied with x being in the range of 0.0≤x≤1.74. In addition, the thermoelectric figures of merit ZT in this case were high enough to exceed the thermoelectric figure of merit ZT of the comparative examples 2 and 13. The crystalline materials not containing one of Sb and Bi showed the high thermoelectric figure of merit ZT substantially equal to or higher than the thermoelectric figure of merit ZT of the comparative example 2 satisfying e=0 and not containing P. For example, in Table 2, the examples 1 to 4 in which x=0.0 and the example 30 in which x=1.74 showed the thermoelectric figure of merit ZT substantially equal to or higher than that of the comparative example 2. The examples 5 to 29 in which the value of x is within the range of 0.2≤x≤1.74, in other words, in which both Sb and Bi are contained, showed the thermoelectric figure of merit ZT that exceeds the thermoelectric figure of merit ZT of the examples 1 to 4 and the example 30. In the examples 1 to 4, x=0.0. In the example 30, x=1.74 and e=0.25. Furthermore, in the examples 5 to 20 in which the value of x satisfies the condition of 0.2≤x≤0.6, it was confirmed that the thermoelectric figure of merit ZT increases as the value of e increases within the range of 0.001≤e≤0.25.

Examples 31 to 60

A crystalline material having a composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01can be produced, for example, as follows. First, elemental Mg, Sb, Bi, Te, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition represented by Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As and Te. These defects are similar in pattern to the defects of the above-described Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01crystalline material. When some of the sites C3 are replaced, the sites C3 are more likely to be replaced by an element having an atom radius closer to the atom radius of Bi. The atom radius of Bi is 0.150 nm. In contrast, the atom radius of the element As is 0.120 nm, and the atom radius of the element P is 0.109 nm. Thus, it is understood that the sites C3 are more likely to be replaced by the element As than by the element P. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the intensity peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material is represented by the formula (1) in which the value of each of a and b is 0, D is at least one of Sb and Bi, and the value of x satisfies 0.0≤x≤1.99-e, E is As, F is Te, and the value off is 0.01. In this crystalline material, the value of a is within the stable composition range of 0.0≤a≤0.04. The values of b and f of the crystalline material are within the stable composition range derived with reference to PTL 1. The value of m of the crystalline material is −0.1≤m≤0.4 with reference to PTL 2.

Referring to NPL 4, when E is P, the value of e is 0.0≤e≤0.5. In contrast, when E is As, the range of e that allows stable synthesis of the crystalline material was calculated by using the above formulas (3) and (4). As a result, it was found that, within the range of 0.0≤e≤0.70, the crystalline material having the composition of Mg₃Bi_2-eAs_ehas a single-phase La₂O₃-type crystal. In other words, this suggests that, within the range of 0.0≤e≤0.70, the Mg₃Bi_2-eAs_ecrystalline material stably form a solid solution and thus the above-described production method can synthesize and produce the crystalline material. Thus, the stable composition range of the value of e, 0.0≤e≤0.70, in the case where E is As is broader than the stable composition range of 0.0≤e≤0.5 in the case where E is P.

As described above, the Bi atom radius of 0.150 nm is closer to the As atom radius of 0.120 nm than to the P atom radius of 0.109 nm, and thus Bi is more likely to be replaced by As than by P. In other words, this suggests that the stable composition range relating to the value of e in the case where E is As is broader than the stable composition range relating to the value of e in the case where E is P. Thus, the evaluation results in which the stable composition range of the value of e, 0.0≤e≤0.70, in the case where E is As is broader than the stable composition range of the value of e, 0.0≤e≤0.5, in the case where E is P described in NPL 4 is consistent with theory. This indicates that the method of determining the stable composition range disclosed herein is reliable. Here, the thermoelectric conversion properties were predicted with the value of e for E within the range of 0.0≤e≤0.5, which corresponds to the narrower stable composition range in the case where E is P. The thermoelectric conversion properties of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01at 330 K was predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. The table 3 shows the calculated values.

TABLE 3

Mg_3+mSb_xBi_1.99−x−eAs_eTe_0.01

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

x
e
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 2
0.0
0.0
−127
2188
2.06
0.56

Ex. 31
0.0
0.001
−127
2202
2.06
0.56

Ex. 32
0.0
0.05
−131
2108
1.97
0.60

Ex. 33
0.0
0.125
−136
2056
1.84
0.68

Ex. 34
0.0
0.25
−112
2506
2.15
0.48

Com. Ex. 14
0.0
0.5
−63
3170
3.33
0.12

Ex. 35
0.2
0.001
−121
2041
1.94
0.51

Ex. 36
0.2
0.05
−133
1822
1.75
0.60

Ex. 37
0.2
0.125
−154
1483
1.48
0.78

Ex. 38
0.2
0.25
−178
1230
1.23
1.05

Ex. 39
0.3
0.001
−129
1711
1.70
0.55

Ex. 40
0.3
0.05
−150
1370
1.44
0.70

Ex. 41
0.3
0.125
−173
1116
1.23
0.89

Ex. 42
0.3
0.25
−184
1046
1.14
1.02

Ex. 43
0.4
0.001
−138
1388
1.44
0.61

Ex. 44
0.4
0.05
−160
1098
1.22
0.76

Ex. 45
0.4
0.125
−176
958
1.09
0.89

Ex. 46
0.4
0.25
−184
952
1.07
0.99

Ex. 47
0.6
0.001
−159
1001
1.13
0.75

Ex. 48
0.6
0.05
−170
900
1.03
0.84

Ex. 49
0.6
0.125
−177
851
0.97
0.91

Ex. 50
0.6
0.25
−181
847
0.97
0.94

Ex. 51
1.0
0.001
−182
725
0.87
0.91

Ex. 52
1.0
0.05
−182
726
0.87
0.91

Ex. 53
1.0
0.125
−182
727
0.87
0.91

Ex. 54
1.0
0.25
−182
725
0.88
0.90

Ex. 55
1.5
0.001
−187
602
0.84
0.83

Ex. 56
1.5
0.05
−187
603
0.85
0.82

Ex. 57
1.5
0.25
−187
605
0.90
0.77

Ex. 58
1.74
0.001
−189
550
0.87
0.74

Ex. 59
1.74
0.05
−189
551
0.89
0.73

Ex. 60
1.74
0.25
−189
552
0.99
0.66

As indicated in Table 3, within the composition range of 0.0≤x≤1.74, when the value of e is in the composition range of 0.001≤e≤0.25, n-type thermoelectric conversion properties were exhibited in which the Seebeck coefficient S is negative. In addition, the thermoelectric figure of merit ZT in this case was high enough to exceed the thermoelectric figure of merit ZT of the comparative examples 2 and 14. Furthermore, Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01not containing one of Sb and Bi showed the high thermoelectric figure of merit ZT substantially equal to or higher than the thermoelectric figure of merit ZT of the comparative example 2 not containing As and satisfying e=0. For example, in Table 3, the examples 31 to 34 that satisfy x=0.0 and the example 60 that satisfy x=1.74 showed the high thermoelectric figure of merit ZT substantially equal to or higher than the thermoelectric figure of merit ZT of the comparative example 2. Furthermore, in the examples 35 to 50 in which the value of x satisfies 0.2≤x≤0.6, the thermoelectric figure of merit ZT increases as the value of e increases within the range of 0.001≤e≤0.25. Tables 2 and 3 indicate the results of the respective cases in which one of P and As is contained. When a crystalline material contains both P and As, a portion of Bi may be replaced by both. In such a case, the crystalline material may be represented by the composition of Mg_3+mSb_xBi_1.99-x-e1-e2P_e1As_e2Te_0.01. In this case, the relation of e=e1+e2 holds. In this case, it is also understood that n-type thermoelectric conversion properties in which the Seebeck coefficient S is negative are exhibited when the value of e is within the composition range of 0.001≤e≤0.25 with the composition range of the value of x being 0.0≤x≤1.74. In addition, it is understood that the thermoelectric figure of merit ZT is higher in this case than in the case where e=0 or e=0.5 is satisfied.

Examples 61 to 63

The thermoelectric conversion properties of Mg_3+mSb_xBi_1.99-x-e1-e2P_e1As_e2Te_0.01at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 4 shows the calculated values.

TABLE 4

Mg_3+mSb_xBi_{1.99−x−e1−e2}P_e1As_e2Te_0.01

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

x
e1
e2
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 2
0.0
0.0
0.0
−127
2188
2.06
0.56

Ex. 61
0.0
0.0625
0.0625
−131
2178
1.88
0.66

Ex. 62
0.0
0.125
0.125
−113
2493
2.12
0.50

Ex. 63
1.74
0.125
0.125
−189
552
0.99
0.66

As indicated in Table 4, when the value of x satisfies 0.0≤x≤1.74 and the condition of 0.001≤e1+e2≤0.25 is satisfied, the crystalline material exhibited n-type thermoelectric conversion properties in which the Seebeck coefficient S is negative. In addition, the thermoelectric figure of merit ZT in this case was substantially equal to or higher than the thermoelectric figure of merit ZT of the comparative example 2. The thermoelectric figures of merit ZT indicated in Table 4 were substantially equal to the thermoelectric figures of merit ZT indicated in Tables 2 and 3. In particular, the example 61, which satisfies x=0.0 and e1+e2=0.125, and the example 63, which satisfies x=1.74 and e1+e2=0.25, showed thermoelectric figures of merit ZT that exceed the thermoelectric figure of merit ZT of a case not containing P or As.

Examples 64 to 71

A crystalline material having a composition of Mg_3+mSb_1.0Bi_0.75As_0.25Te_fcan be produced, for example, as follows. First, elemental Mg, Sb, Bi, Te, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture was put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Te_fbased on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Te_fhas defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As and Te. These defects are similar in pattern to the defects of the above-described crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant of the crystal structure. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Te_fis determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material is represented by the formula (1) in which the value of each of a and b is 0, D is Sb and Bi, E is As, the value of e is 0.25, F is Te, and the value of f satisfies 0.0≤f≤0.06 with reference to PTL 1. In this crystalline material, the value of a is within the stable composition range of 0.0≤a≤0.04. The value of b is within the stable composition range derived with reference to PTL 1. In this crystalline material, the value of m is −0.1≤m≤0.4 with reference to PTL 2. Furthermore, in this crystalline material, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01indicated in Table 3. In this composition range, the value of e satisfies 0.001≤e≤0.25 with the value of x being 0.0≤x≤1.74. Furthermore, the composition ratio of Sb and Bi represented by the value of x is within the composition range indicated in Table 3.

The thermoelectric conversion properties of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Te_fat 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 5 shows the calculated values.

TABLE 5

Mg_3+mSb_1.0Bi_0.75−fAs_0.25Te_f

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

f
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com.
0.0
−568
3
0.49
0.06

Ex. 15

Ex. 64
0.0001
−552
9
0.49
0.18

Ex. 65
0.0005
−428
41
0.50
0.50

Ex. 66
0.001
−370
81
0.52
0.70

Ex. 67
0.005
−236
384
0.68
1.04

Ex. 68
0.01
−182
725
0.88
0.90

Ex. 69
0.02
−133
1316
1.26
0.61

Ex. 70
0.04
−91
2286
1.98
0.32

Ex. 71
0.06
−71
3098
2.65
0.20

As indicated in Table 5, within the composition range of 0.0001≤f≤0.06, n-type thermoelectric conversion properties were exhibited in which the value of S is negative, and the thermoelectric figure of merit ZT exceeded the thermoelectric figure of merit ZT of the comparative example 15.

Examples 72 to 79

A crystalline material having a composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Se_fcan be produced, for example, as follows. First, elemental Mg, Sb, Bi, Se, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Se_fbased on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Se_fhas defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As and Se. These defects are similar in pattern to the defects of the above-described crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01and the above-described crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Te_f. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction pattern shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Se_fis determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material is represented by the formula (1) in which the value of each of a and b is 0, D is Sb and Bi, E is As, the value of e is 0.25, F is Se, and the value of f is 0.0≤f≤0.06 with reference to PTL 1. The crystalline material in which Bi is replaced by Se, which is homologous with Te, can exhibit n-type thermoelectric conversion properties. In this crystalline material, the value of a is within the stable composition range of 0.0≤a≤0.04. The value of b is within the stable composition range derived with reference to PTL 1. The value of m is −0.1≤m≤0.4 with reference to PTL 2.

Furthermore, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01indicated in Table 3. In the composition range, the value of e satisfies the condition of 0.001≤e≤0.25, within 0.0≤x≤1.74. Furthermore, the composition ratio of Sb and Bi indicated from the value of x is within the composition range obtained from the results in Table 3.

The thermoelectric conversion properties of Mg_3+mSb_1.0Bi_0.75-fAs_0.25Se_fat 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 6 shows the calculated values.

TABLE 6

Mg_3+mSb_1.0Bi_0.75−fAs_0.25Se_f

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

f
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com.
0.0
−568
3
0.49
0.06

Ex. 15

Ex. 72
0.0001
−585
5
0.49
0.11

Ex. 73
0.0005
−497
18
0.49
0.30

Ex. 74
0.001
−440
36
0.50
0.46

Ex. 75
0.005
−304
173
0.57
0.93

Ex. 76
0.01
−247
337
0.66
1.04

Ex. 77
0.02
−193
639
0.83
0.95

Ex. 78
0.04
−142
1171
1.16
0.67

Ex. 79
0.06
−116
1635
1.48
0.49

As indicated in Table 6, within the range of 0.0001≤f≤0.06, n-type thermoelectric conversion properties were exhibited in which the value of S is negative and the thermoelectric figure of merit ZT was high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15. Tables 5 and 6 show the results of the respective cases in which one of Te and Se is contained as F. When Te and Se are both contained as F, a portion of Bi may be replaced by both Te and Se. In such a case, the crystalline material has the composition of Mg_3+mSb_1.0Bi_0.75-f1-f2As_0.25Te_f1Se_f2. Here, the relation of f=f1+f2 holds. In this case, it is also understood that, when the value of f is in the composition range of 0.0001≤f≤0.06, n-type properties in which the Seebeck coefficient S is negative are exhibited and the thermoelectric figure of merit ZT is high enough to exceed the thermoelectric figure of merit ZT in the case where f=0 and f>0.06.

The results indicated in Tables 2 to 6 indicate that the composition of the crystalline material can be represented by Mg_3+mSb_xBi_{1.99-x-e1-e2-f1-f2}P_e1As_e2Te_f1Se_f2. In such a case, when the value of x is within the composition range of 0.0≤x≤1.74, 0.001≤e≤0.25 may be satisfied and 0.0001≤f≤0.06 may be satisfied. It is noted that e=e1+e2 holds, and e=f1+f2 holds.

Examples 80 to 82

The thermoelectric conversion properties of Mg_3+mSb_1.0Bi_0.75-f1-f2As_0.25Te_f1Se_f2at 330 K were predicted as those of Mg_3±mSb_xBi_1.99-x-eP_eTe_0.01. Table 7 shows the calculated values.

TABLE 7

Mg_3+mSb_1.0Bi_{0.75−f1−f2}As_0.25Te_f1Se_f2

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

f1
f2
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 15
0.0
0.0
−568
3
0.49
0.06

Ex. 80
0.00005
0.00005
−570
6.8
0.49
0.15

Ex. 81
0.005
0.005
−208
537
0.77
1.00

Ex. 82
0.03
0.03
−87
2418
2.08
0.29

As indicated in Table 7, within the range of 0.0001≤f1+f2≤0.06, n-type thermoelectric conversion properties were exhibited in which the Seebeck coefficient S is negative, and the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Examples 83 to 89

A crystalline material having n-type thermoelectric conversion properties in which the value of S is negative may be obtained by addition of Y, Sc, La or Ce.

A crystalline material having a composition of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25can be produced, for example, as follows. First, elemental Mg, Y, Sb, Bi, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25has defects in which some of the Mg sites C1 are replaced by Y. In addition, the crystalline material has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction pattern shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material having the composition of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25is represented by the formula (1) in which A is Y, the value of a satisfies the condition of 0.0≤a≤0.04 with reference to NPL 7, and the value of b is 0. In addition, D is Sb and Bi, E is As, the value of e is 0.25, and the value off is 0. When Mg is replaced by Y, n-type thermoelectric conversion properties can be exhibited.

The method of determining the stable composition range of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01was used for the crystalline material that contains A in the formula (1). As a result, it was evaluated that the defect generation energy of the crystalline material in the case where A is Sc and in the case where A is La is lower than that in the case where A is Y and thus the crystalline material can be stably synthesized. Furthermore, it is understood from NPL 9 that, when A is Ce, the crystalline material can be more stably synthesized than when A is La. This suggests that the stable composition range of the value of a is the narrowest when A is Y. Thus, the stable composition range of the value of a that allows stable synthesis of the crystalline material even when any one of Sc, Y, La, and Ce is selected as A was set at 0.0≤a≤0.04, which corresponds to the narrowest stable composition range in the case where A is Y. The value of b of the crystalline material having the composition of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25is within the stable composition range derived with reference to PTL 1. In the crystalline material, the value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. Furthermore, in the crystalline material, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01indicated in Table 3. In the composition range, within the range of 0.0≤x≤1.74, the value of e satisfies the condition of 0.001≤e≤0.25. In the crystalline material, the composition ratio of Sb and Bi represented by the value of x is within the composition range obtained from the results in Table 3. The crystalline material contains Y instead of Te and Se, and thus the value of f is within the composition range of 0.0≤f≤0.06 referred to in PTL 1.

The thermoelectric conversion properties of Mg_3+m-aY_aSb_1.0Bi_0.75As_0.25at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 8 shows the calculated values.

TABLE 8

Mg_3+m−aY_aSb_1.0Bi_0.75As_0.25

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

a
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com.
0.0
−568
3
0.49
0.06

Ex. 15

Ex. 83
0.0001
−482
22
0.49
0.34

Ex. 84
0.0005
−347
105
0.53
0.79

Ex. 85
0.001
−289
207
0.59
0.98

Ex. 86
0.005
−162
916
1.00
0.80

Ex. 87
0.01
−116
1635
1.48
0.49

Ex. 88
0.02
−78
2794
2.39
0.23

Ex. 89
0.04
−52
4622
4.02
0.10

As indicated in Table 8, within the range of 0.0001≤a≤0.04, the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Examples 90 to 96

A crystalline material having a composition of Mg_3+m-aSc_aSb_1.0Bi_0.75As_0.25can be produced, for example, as follows. First, elemental Mg, Sc, Sb, Bi, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture was put into a graphite mold and was sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+m-aSc_aSb_1.0Bi_0.75As_0.25based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+m-aSC_aSb_1.0Bi_0.75As_0.25has defects in which some of the Mg sites C1 are replaced by Sc. In addition, the crystalline material has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+m-aSc_aSb_1.0Bi_0.75As_0.25is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material having the composition of Mg_3+m-aSc_aSb_1.0Bi_0.75As_0.25is represented by the formula (1) in which A is Sc, the value of a satisfies the condition of 0.0≤a≤0.04, and the value of b is 0. In addition, D is Sb and Bi, E is As, the value of e is 0.25, and the value of f is 0. In the crystalline material, even when Mg is replaced by Sc, which is homologous with Y, n-type thermoelectric conversion properties can be exhibited. The value of a satisfies the condition of 0.0≤a≤0.03 with reference to NPL 6. However, as described above, it is understood that, when A is Y, the stable composition range of the value of a is the narrowest. Thus, the stable composition range of the value of a that allows stable synthesis of the crystalline material even when any one of Sc, Y, La, and Ce is selected as A was set as 0.0≤a≤0.04, which corresponds to the narrowest stable composition range in the case where A is Y.

In the crystalline material having the composition of Mg_3+m-aSc_aSb_1.0Bi_0.75As_0.25, the value of b is within the stable composition range derived with reference to PTL 1. The value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. Furthermore, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01in Table 3. In the composition range, within the range of 0.0≤x≤1.74, the value of e satisfies the condition of 0.001≤e≤0.25. Furthermore, the composition ratio of Sb and Bi represented by the value of x is within the composition range obtained from the results in Table 3. The crystalline material contains Sc instead of Te or Se, and thus the value of f satisfies the condition of 0.0≤f≤0.06 referred to in PTL 1.

The thermoelectric conversion properties of Mg_3+m-aSc_aSb_1.0Bi_0.75As_0.25at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 9 shows the calculated values.

TABLE 9

Mg_3+m−aSc_aSb_1.0Bi_0.75As_0.25

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

a
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com.
0.0
−568
3
0.49
0.06

Ex. 15

Ex. 90
0.0001
−459
29
0.50
0.40

Ex. 91
0.0005
−323
140
0.55
0.87

Ex. 92
0.001
−266
273
0.62
1.02

Ex. 93
0.005
−142
1171
1.16
0.67

Ex. 94
0.01
−99
2053
1.80
0.37

Ex. 95
0.02
−65
3451
2.95
0.16

Ex. 96
0.04
−46
5705
5.06
0.08

As indicated in Table 9, within the range of 0.0001≤a≤0.04, the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Examples 97 to 103

A crystalline material having a composition of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25can be produced, for example, as follows. First, elemental Mg, La, Sb, Bi, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25has defects in which some of the Mg sites C1 are replaced by La. In addition, the crystalline material has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material having the composition of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25is represented by the formula (1), in which A is La, the value of a satisfies the condition of 0.0≤a≤0.04, the value of b is 0, D is Sb and Bi, E is As, the value of e is 0.25, and the value of f is 0. In this crystalline material, even when Mg is replaced by La, which is homologous with Y and Sc, n-type thermoelectric conversion properties can be exhibited. The value of a satisfies the condition of 0.0≤a≤0.03 with reference to NPL 8. However, as described above, it is understood that, when A is Y, the stable composition range of the value of a is the narrowest. Thus, the stable composition range of the value of a that allows stable synthesis of the crystalline material even when any one of Sc, Y, La, and Ce is selected as A was set at 0.0≤a≤0.04, which corresponds to the narrowest stable composition range in the case where A is Y.

In the crystalline material having the composition of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25, the value of b is within the stable composition range derived with reference to PTL 1. The value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. Furthermore, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01indicated in Table 3. In the composition range, within the range of 0.0≤x≤1.74, the value of e satisfies the condition of 0.001≤e≤0.25. Furthermore, the composition ratio of Sb and Bi represented by the value of x is within the composition range obtained from the results in Table 3. The crystalline material contains La instead of Te or Se, and thus the value of f is within the composition range of 0.0≤f≤0.06 referred to in PTL 1.

The thermoelectric conversion properties of Mg_3+m-aLa_aSb_1.0Bi_0.75As_0.25at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 10 shows the calculated values.

TABLE 10

Mg_3+m−aLa_aSb_1.0Bi_0.75As_0.25

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

a
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com.
0.0
−568
3
0.49
0.06

Ex. 15

Ex. 97
0.0001
−459
29
0.50
0.40

Ex. 98
0.0005
−323
140
0.55
0.87

Ex. 99
0.001
−266
273
0.62
1.02

Ex. 100
0.005
−142
1171
1.16
0.67

Ex. 101
0.01
−99
2053
1.80
0.37

Ex. 102
0.02
−65
3451
2.95
0.16

Ex. 103
0.04
−46
5705
5.06
0.08

As indicated in Table 10, within the range of 0.0001≤a≤0.04, the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Examples 104 to 110

A crystalline material having a composition of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25can be produced, for example, as follows. First, elemental Mg, Ce, Sb, Bi, and As as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture i put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25has defects in which some of the Mg sites C1 are replaced by Ce. In addition, the crystalline material has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material having the composition of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25is represented by the formula (1) in which A is Ce, the value of a satisfies the condition of 0.0≤a≤0.04, and the value of b is 0. In addition, D is Sb and Bi, E is As, the value of e is 0.25, and the value of f is 0. In this crystalline material, even when Mg is replaced by Ce, which is homologous with Y, Sc, and La, n-type thermoelectric conversion properties can be exhibited. Referring to NPL 9, it is understood that the crystalline material can be more stably synthesized when A is Ce than when A is La. Thus, it is understood that the stable composition range relating to the value of a in the case where A is Ce is broader than 0.0≤a≤0.03, which is the range of the value of a in the case where A is La referred to in NPL 8. In contrast, as described above, it is understood that the stable composition range of the value of a is the narrowest when A is Y. Thus, the stable composition range of the value of a that allows stable synthesis of the crystalline material even when any one of Sc, Y, La, and Ce is selected as A was set at 0.0≤a≤0.04, which corresponds to the narrowest stable composition range in the case where A is Y.

In the crystalline material having the composition of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25, the value of b is in the stable composition range derived with reference to PTL 1. The value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. Furthermore, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01indicated in Table 3. In this composition range, within the range of 0.0≤x≤1.74, the value of e satisfies the condition of 0.001≤e≤0.25. Furthermore, the composition ratio of Sb and Bi represented by the value of x is also within the composition range obtained from the results in Table 3. This crystalline material contains Ce instead of Te or Se, and thus the value of f satisfies the condition of 0.0≤f≤0.06 referred to in PTL 1.

The thermoelectric conversion properties of Mg_3+m-aCe_aSb_1.0Bi_0.75As_0.25at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 11 shows the calculated values.

TABLE 11

Mg_3+m−aCe_aSb_1.0Bi_0.75As_0.25

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

a
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com.
0.0
−568
3
0.49
0.06

Ex. 15

Ex. 104
0.0001
−459
32
0.50
0.43

Ex. 105
0.0005
−3133
157
0.56
0.91

Ex. 106
0.001
−256
305
0.64
1.03

Ex. 107
0.005
−134
1292
1.24
0.62

Ex. 108
0.01
−92
2248
1.95
0.32

Ex. 109
0.02
−61
3758
3.23
0.14

Ex. 110
0.04
−44
6248
5.57
0.07

As indicated in Table 11, within the range of 0.0001≤a≤0.04, the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Tables 8 to 11 indicate the results of the respective cases in which the formula (1) contains one of Y, Sc, La, and Ce as F. When the crystalline material contains multiple kinds of elements selected from Y, Sc, La, and Ce, a portion of Mg may be replaced by the multiple kinds of elements. For example, a crystalline material having the composition of Mg_{3+m-a1-a2-a3-a4}Y_a1Sc_a2La_a3Ce_a4Sb_1.0Bi_0.75As_0.25can be provided. In such a case, the relation of a=a1+a2+a3+a4 holds. In this case, it is also understood that, when the condition of 0.0001≤a≤0.04 is satisfied, n-type thermoelectric conversion properties in which the Seebeck coefficient S is negative are exhibited and the thermoelectric figure of merit ZT is higher than that in the case where a=0 and a>0.04.

The results indicated in Tables 2 to 4 and 8 to 11 indicate that a crystalline material having the composition of Mg_{3+m-a1-a2-a3-a4}Y_a1Sc_a2La_a3Ce_a4Sb_xBi_1.99-x-e1-e2P_e1As_e2can be provided. In this case, within the range of 0.0×1.74, the value of e that satisfies the relation of e=e1+e2 may satisfy the condition of 0.001≤e≤0.25 and the value of a that satisfies the relation of a=a1+a2+a3+a4 may satisfy the condition of 0.0001≤a≤0.04.

Examples 111 to 113

The thermoelectric conversion properties of Mg_3+m-a1-a2Y_a1SC_a2Sb_1.0Bi_0.75As_0.25at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 12 shows the calculated values.

TABLE 12

Mg_{3+m−a1−a2}Y_a1Sc_a2Sb_1.0Bi_0.75As_0.25

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

a1
a2
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 15
0.0
0.0
−568
3
0.49
0.06

Ex. Ill
0.00005
0.00005
−470
25
0.49
0.37

Ex. 112
0.0005
0.0005
−276
240
0.60
1.00

Ex. 113
0.02
0.02
−48
5168
4.54
0.09

As indicated in Table 12, within the range of 0.0001≤a1+a2≤0.04, the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Tables 5 and 6 indicate the results of the respective cases in which the formula (1) contains one of Te and Se as F. In contrast, Tables 8 to 11 indicate the results of the respective cases in which the formula (1) contains one of Y, Sc, La, and Ce as A. When the formula (1) contains both F and A, a crystalline material having the composition of Mg_{3+m-a1-a2-a3-a4}Y_a1SC_a2La_a3Ce_a4Sb_1.0Bi_0.75-f1-f2As_0.25Te_f1Se_f2can be provided. In this case, the relations of a=a1+a2+a3+a4 and f=f1+f2 hold. It is understood that, in such a case, within the composition range of 0.0001≤a+f≤0.06, n-type thermoelectric conversion properties in which the Seebeck coefficient S is negative are exhibited and the thermoelectric figure of merit ZT is higher than that in the case where a=0 and a>0.04.

The results indicated in Tables 2 to 12 indicate that a crystalline material having the composition of Mg_{3+m-a1-a2-a3-a4}Y_a1SC_a2La_a3Ce_a4Sb_xBi_{1.99-x-e1-e2-f1-f2}P_e1As_e2Te_f1Se_f2can be provided. It is understood that, in this case, when the value of x satisfies 0.0≤x≤1.74, the value of e that satisfies the relation of e=e1+e2 may satisfy the condition of 0.001≤e≤0.25. Furthermore, it is understood that the sum of the value of a that satisfies the relation of a=a1+a2+a3+a4 and the value of f that satisfies the relation of f=f1+f2 may satisfy the condition of 0.0001≤a+f≤0.06.

Examples 114 to 116

The thermoelectric conversion properties of Mg_3+m-a1Y_a1Sb_1.0Bi_0.75-f1As_0.25Te_f1at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 13 shows the calculated values.

TABLE 13

Mg_3+m−a1Y_a1Sb_1.0Bi_0.75−f1As_0.25Te_f1

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

a1
f1
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Com. Ex. 15
0.0
0.0
−568
3
0.49
0.06

Ex. 114
0.00005
0.00005
−511
15
0.49
0.27

Ex. 115
0.005
0.005
−140
1208
1.19
0.66

Ex. 116
0.03
0.03
−51
4746
4.14
0.10

As indicated in Table 13, within the range of 0.0001≤a1+f1≤0.06, the thermoelectric figures of merit ZT were high enough to exceed the thermoelectric figure of merit ZT of the comparative example 15.

Examples 3, 117, and 118

A crystalline material having a composition of Mg_3+m-bMn_bBi_1.865P_0.125Te_0.01can be produced, for example, as follows. First, elemental Mg, Mn, Bi, P, and Te as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+m-bMn_bBi_1.865P_0.125Te_0.01based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition of Mg_3+m-bMn_bBi_1.865P_0.125Te_0.01has defects in which some of the Mg sites C2 are replaced by Mn. In addition, the crystalline material has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by P. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+m-bMn_bBi_1.865P_0.125Te_0.01is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material having the composition of Mg_3+m-bMn_bBi_1.865P_0.125Te_0.01is represented by the formula (1) in which the value of a is 0, B is Mn, the value of b satisfies the condition of 0.0≤b≤0.48 with reference to PTL 1, and D is Bi. In addition, E is P, the value of e is 0.125, F is Te, and the value off is 0.01. In this crystalline material, the value of a is within the stable composition range of 0.0≤a≤0.04. In this crystalline material, the value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. In addition, in this crystalline material, when E is P, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01indicated in Table 2. In this composition range, the value of e satisfies 0.001≤e≤0.25 with the value of x being 0.0≤x≤1.74. Furthermore, the composition ratio of Sb and Bi represented by the value of x is within the composition range obtained from the results indicated in Table 2. In addition, in this crystalline material, the value of a is 0, and thus the value off is within the stable composition range of 0.0001≤f≤0.06 obtained from the results in Table 5.

The thermoelectric conversion properties of Mg_3+m-bMn_bBi_1.865P_0.125Te_0.01at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 14 shows the calculated values.

TABLE 14

Mg_3+m−bMn_bBi_1.865P_0.125Te_0.01

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

b
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Ex. 3
0.0
−127
2246
1.93
0.62

Ex. 117
0.125
−122
2078
2.00
0.51

Ex. 118
0.25
−122
2152
2.05
0.52

Com.
0.375
−109
2428
2.19
0.44

Ex. 16

As indicated in Table 14, within the composition range of 0.0≤b≤0.25, n-type thermoelectric conversion properties were exhibited in which the Seebeck coefficient S is negative, and the thermoelectric figure of merit ZT was high enough to exceed the thermoelectric figure of merit ZT of the comparative example 16.

Examples 34, 119, and 120

A crystalline material having a composition of Mg_3+m-bZn_bBi_1.74As_0.25Te_0.01can be produced, for example, as follows. First, elemental Mg, Zn, Bi, As, and Te as materials are weighed to be in a desired composition ratio and sealed in a stainless-steel container together with stainless-steel balls under an argon atmosphere, and the materials are pulverized and mixed by a planetary ball milling technique to provide a powder mixture. The generated powder mixture is put into a graphite mold and sintered under an argon atmosphere using a spark plasma sintering technique to provide a cylindrical compact. In this way, the crystalline material having the composition of Mg_3+m-bZn_bBi_1.74As_0.25Te_0.0based on Mg₃(Sb,Bi)₂can be produced.

Referring to FIG. 3, the crystalline material having the composition represented by Mg_3+m-bZn_bBi_1.74As_0.25Te_0.01has defects in which some of the Mg sites C2 are replaced by Zn. This crystalline material has defects in which some of the sites C3 composed of at least one selected from the group consisting of Sb and Bi are replaced by As. These defects may cause lattice deformation in the La₂O₃-type crystal structure. This lattice deformation changes the lattice constant of at least a portion of the crystal. Thus, it is predicted that there is a shift in the intensity peaks of the X-ray diffraction pattern of the thermoelectric conversion material having this composition relative to the intensity peaks of the X-ray diffraction pattern of the Mg₃(Sb,Bi)₂crystalline material indicated in FIG. 2. The shift in the peaks found in the X-ray diffraction pattern results from the change in the lattice constant. The peaks of the X-ray diffraction pattern shift to the low-angle side as the lattice constant increases, and the peaks of the X-ray diffraction patterns shift to the high-angle side as the lattice constant decreases.

The stable composition range of the crystalline material having the composition of Mg_3+m-bZn_bBi_1.74As_0.25T_0.01is determined by using the same method as the method of determining the stable composition range of the above-described Mg_3+m-a-bA_aB_bD_2-e-fE_eF_fcrystalline material. The crystalline material having the composition of Mg_3+m-bZn_bBi_1.74As_0.25Te_0.01is represented by the formula (1), in which the value of a is 0, B is Zn, the value of b satisfies the condition of 0.0≤b≤0.48 with reference to PTL 1, and D is Bi. In addition, E is As, the value of e is 0.25, F is Te, and the value of f is 0.01. In this crystalline material, the value of a is within the stable composition range of 0.0≤a≤0.04. In this crystalline material, the value of m satisfies the condition of −0.1≤m≤0.4 with reference to PTL 2. In addition, in this crystalline material, when E is As, the value of e is within the composition range obtained from the results showing the thermoelectric conversion properties of the crystalline material having the composition of Mg_3+mSb_xBi_1.99-x-eAs_eTe_0.01indicated in Table 3. In this composition range, within the range of 0.0≤x≤1.74, the value of e satisfies the condition of 0.001≤e≤0.25. Furthermore, the composition ratio of Sb and Bi represented by the value of x is within the composition range obtained from the results shown in Table 3. In addition, in this crystalline material, the value of a is 0, and thus the value off is within the stable composition range of 0.0001≤f≤0.06 obtained from the results shown in Table 5.

The thermoelectric conversion properties of Mg_3+m-bZn_bBi_1.74As_0.25Te_0.01at 330 K were predicted as those of Mg_3+mSb_xBi_1.99-x-eP_eTe_0.01. Table 15 shows the calculated values.

TABLE 15

Mg_3+m−bZn_bBi_1.74As_0.25Te_0.01

Seebeck
Electrical
Thermal
Dimensionless

coefficient
conductivity
conductivity
figure of merit

b
S (μV/K)
σ (S/cm)
κ (W/mK)
ZT

Ex. 34
0.0
−112
2506
2.15
0.48

Ex. 119
0.125
−134
2061
1.83
0.67

Ex. 120
0.25
−134
1970
1.83
0.64

Com.
0.375
−108
2387
2.18
0.42

Ex. 17

As indicated by the results in Table 15, within the composition range of 0.0≤b≤0.25, n-type thermoelectric conversion properties were exhibited in which the Seebeck coefficient S is negative, and the thermoelectric figure of merit ZT was high enough to exceed the thermoelectric figure of merit ZT of the comparative example 17.

Tables 14 and 15 show the results of the respective cases in which one of Mn and Zn is contained. When both Mn and Zn are contained, a portion of Mg can be replaced by both the elements. Thus, a crystalline material having the composition of Mg_3+m-b1-b2Mn_b1Zn_b2Bi_1.74As_0.25Te_0.01can be provided. In this case, the relation of b=b1+b2 holds. In this case, it is also understood that, when the value of b satisfies the condition of 0.0≤b≤0.25, n-type thermoelectric conversion properties in which the value of the Seebeck coefficient S is negative are exhibited, and the thermoelectric figure of merit ZT is higher than that in the case where the condition of b>0.25 is satisfied.

The results indicated in Tables 2 to 15 indicate that a crystalline material having a composition of Mg_{3+m-a1-a2-a3-a4-b1-b2}Y_a1SC_a2La_a3Ce_a4Mn_b1Zn_b2Sb_xBi_{1.99-x-e1-e2-f1-f2}P_e1As_e2Te_f1Se_f2can be provided. In this case, when the value of x is in the composition range of 0.0≤x≤1.74, the value of e that satisfies the relation of e=e1+e2 satisfies the condition of 0.001≤e≤0.25. In addition, the value of a that satisfies the relation of a=a1+a2+a3+a4 and the value of f that satisfies the relation of f=f1+f2 satisfy the condition of 0.0001≤a+f≤0.06. The value of b that satisfies the relation of b=b1+b2 satisfies the condition of 0.0≤b≤0.25, for example.

A thermoelectric conversion material according to the present disclosure may be used in a thermoelectric apparatus that converts thermal energy to electrical energy.

	Number	Date	Country
Parent	PCT/JP2021/021701	Jun 2021	US
Child	18068530		US

THERMOELECTRIC CONVERSION MATERIAL, THERMOELECTRIC CONVERSION ELEMENT, THERMOELECTRIC CONVERSION MODULE, METHOD OF POWER GENERATION, AND METHOD OF HEAT TRANSFER

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