Patent Application
20100173438
The present invention relates to a thermoelectric converter comprising ceramics as insulating materials.
A thermoelectric conversion material is a material which can interconvert thermal and electric energies, and constitutes a thermoelectric converter which is used as a thermoelectric cooling element or a thermoelectric power generating element. Thermoelectric conversion material is used for thermoelectric conversion using the Seebeck effect. Thermoelectric converting performance is represented by Formula (1) which is called the performance index ZT.
ZT=α
2
σT/κ (1)
(wherein, α represents the Seebeck coefficient, σ represents the electrical conductivity, κ represents the thermal conductivity, and T represents the measured temperature.)
It is apparent, according to Formula (1), that in order to improve the thermoelectric converting performances of a thermoelectric conversion material, Seebeck coefficient α and electrical conductivity σ of the material are increased, and thermal conductivity κ of the material is decreased. Sometimes, fine particles, which do not react with the base material of the thermoelectric conversion material, are added to the starting material particles of the thermoelectric conversion material to decrease thermal conductivity κ of the material. Thereby, the inactive fine particles can scatter phonons, which are the major factor of the thermal conduction in a thermoelectric conversion material, to decrease thermal conductivity κ.
However, in a conventional conversion material in which the inactive fine particles are unevenly distributed, the inactive fine particles, which provide the scattering effect of the phonon, have a large adverse influence on the other physical properties, such as electrical resistivity, due to the uneven distribution thereof, thus an increase in the performance of the thermoelectric conversion materials is inhibited. In order to solve the problem, Japanese unexamined patent publication No. 2000-261047 and Japanese unexamined patent publication No. 3-148879 disclose, for example, a sintered thermoelectric conversion material, wherein fine particles, such as ceramic particles which do not react with the base material are evenly dispersed in the starting material comprising fine particles.
According to the known technology above, the microparticulation of the starting material in addition to the inactive fine particles to be dispersed makes it possible for the inactive fine particles to be easily dispersed in the entirety of the base material, thus leading to a high probability of the presence of the inactive fine particles between the starting material particles, whereby no crystallization of the starting material particles occurs. Additionally, the above prior art references describe that, by preparing the starting material and the inactive fine particles, so that they have substantially the same particle size, that is to say the diameter ratio is approximately equal to one, the inactive fine particles are evenly distributed in the thermoelectric conversion material, and thus, the degradation of other physical properties, such as the electrical resistivity, due to the uneven distribution of the inactive fine particles, can be suppressed.
But, as the particles having a nanoscale diameter have a large specific surface area and tend to aggregate by Van der Waals' forces, etc. Consequently, the simple mixing of thermoelectric conversion material particles and inactive fine particles causes the inactive fine particles 2 to aggregate into a microscale aggregate, as shown in
In the known arts shown above, the inactive fine particles are evenly dispersed to adjust other physical properties, which do not directly relate to the equation (1), such as the electrical resistivity, but electrical conductivity σ and thermal conductivity κ, both directly relating to the performance index ZT in the equation (1), have not been studied. Therefore, the inactive fine particles in the known arts above have a microscale diameter. The dispersion state of the inactive fine particles has not been precisely studied.
Since the carrier (an electron or electron hole) can carry both heat and electricity, electrical conductivity σ and thermal conductivity κ are proportional. Additionally, it is known that electrical conductivity σ and Seebeck coefficient α are inversely proportional. Therefore, if electrical conductivity σ is increased, thermal conductivity κ is increased and Seebeck coefficient α is decreased accordingly. Furthermore, as the effective mass and mobility are inversely proportional, the effective mass is decreased when the mobility is increased.
Therefore, the object of the present invention is to eliminate the drawbacks of the prior art stated above by providing a method for manufacturing a thermoelectric converter having a good performance index.
In order to achieve the object shown above, the present invention provides a method for manufacturing a thermoelectric element for thermoelectric generation, comprising the steps of:
preparing an alcohol dispersion liquid comprising a ceramic particle having the average diameter of 1 to 100 nm, and a salt of an element constituting a thermoelectric conversion material; and
dropping the dispersion liquid into a solution containing a reducing agent to deposit a raw material particle of the thermoelectric conversion material, which is then subject to heating and sintering.
According to the present invention, thermoelectric conversion material particles are formed by depositing and heating the raw material particles of the thermoelectric conversion material in the dispersion liquid containing ceramic particles having an average diameter of 1 to 100 nm, followed by heat treatment, so that composite particles in which the ceramic particles and the thermoelectric conversion material particles are evenly dispersed without being aggregated can be obtained. Thus, a thermoelectric converter, wherein ceramic particles having an average diameter of 1 to 100 cm are evenly dispersed in the thermoelectric conversion material, is obtained by sintering the composite particles.
At first, the relationship between the performance index ZT and the structure constitution of the thermoelectric conversion material is explained in detail referring to
On the other hand, if the structure size of the thermoelectric conversion material becomes smaller than the mean free path of the phonons, electrical conductivity σ does not decrease, but when the structure size becomes a particle size approximately equal to the length of the mean free path of the carrier or less, electrical conductivity σ decreases. Based on the fact that the structure size of the thermoelectric conversion material at which thermal conductivity κ begins decreasing is different from the structure size of the thermoelectric conversion material at which electrical conductivity σ begins decreasing, performance index ZT represented by the formula (1) above can be further increased by selecting the structure size of the thermoelectric conversion material to be larger than the mean free path of a carrier and smaller than the mean free path of the phonons, so that the decreasing rate of thermal conductivity κ is higher than the decreasing rate of the electrical conductivity.
What determines the structure size of the thermoelectric conversion material is the diameter of the ceramic particles, i.e., an insulating material dispersed in the thermoelectric conversion material, or the dispersion distance between the ceramic particles. Therefore, in the present invention, the dispersion distance between the ceramic particles is controlled so as to obtain the effect mentioned above.
That is, in the thermoelectric converter obtained by the method of the present invention, the distance between the ceramic particles dispersed in the thermoelectric conversion material is less than or equal to the length of the mean free path of the phonons of the thermoelectric conversion material.
The mean free path (MFP) is calculated by the formula below.
Carrier MFP=(“mobility”דeffective mass”דcarrier velocity”/“elementary electric charge”
Phonon MFP=3דlattice thermal conductivity”/“specific heat”/“acoustic velocity”
In the formulae above, each value is obtained from the reference values and the approximation formula for the thermal properties, except that the measured value is used only for the specific heat.
The results of the carrier MFP and the phonon MFP calculated for Co0.94Ni0.06Sb3 and CoSb3 are shown below.
As can be seen above, the carrier MFP and the phonon MFP are determined by the material and the temperature. In the thermoelectric converter obtained by the present invention, it is necessary that the structure size of at least a part of the thermoelectric converter is smaller than the mean free path of the phonons at the maximum. output level of the power factor (α2σ) of the thermoelectric conversion material. As the CoSb3 type material exhibits the maximum output of the power factor (α2σ) at 400° C., it is necessary that the size be smaller than the mean free path of the phonons at 400° C. Specifically, the distance is preferably in the range of 1 nm to 100 nm, and more preferably 10 nm to 100 nm.
In the present invention, at first, an alcohol dispersion liquid containing ceramic particles having the average diameter of 1 to 100 nm and a salt of an element constituting a thermoelectric conversion material is prepared.
As a ceramic, a commonly used material, such as alumina, zirconia, titania, magnesia, and silica, can be used. Among them, silica, zirconia, and titania are preferable because of their low thermal conductivity. One or more kinds of ceramic particles may be used. The specific resistance of the ceramics is preferably more than 1000 μΩm, and more preferably 106 μΩm or more, and most preferably 1010 μΩm or more. The specific resistance not more than 1000 μΩm may interfere with the increase of ZT due to the high thermal conduction.
The average diameter of ceramic particles is equal to or less than the mean free path of the phonons, and is, specifically, 1 to 100 nm. Using a particle having such a diameter reduces thermal conductivity κ of thermoelectric conversion material, thus leading to the improvement of the performance index ZT, because the distance between the ceramic particles dispersed in the formed thermoelectric converter becomes smaller than the mean free path of the phonons of the ceramics, causing the phonons to be considerably scattered in the thermoelectric conversion material.
The thermoelectric conversion material may be of a P-type or a N-type. The material for P-type thermoelectric conversion material is not specifically limited. For example, Bi2Te3 type material, PbTe type material, Zn4Sb3 type material, CoSb3 type material, half Heusler type material, full Heusler type material, SiGe type material, etc., can be used. Likewise, the material for N-type thermoelectric conversion material is not specifically limited, and known material, such as Bi2Te3 type material, PbTe type material, Zn4Sb3 type material, CoSb3 type material, half Heusler type material, full Heusler type material, SiGe type material, Mg2Si type material, Mg2Sn type material, or CoSi type material, can be used.
The thermoelectric conversion material used in the present invention preferably has an output factor of not less than 1 mW/K2, and more preferably, not less than 2 mW/K2, and most preferably, not less than 3 mW/K2. If the output factor is smaller than 1 mW/K2, a dramatic improvement of the performance can not be expected. Thermal conductivity κ of the thermoelectric conversion material is preferably more than 5 W/mK, more preferably more than 7 W/mK, and most preferably is more than 10 W/mK. Particularly, if the thermal conductivity κ is more than 5 W/mK, the effect of the present invention is remarkable. Namely, when the structure size of the thermoelectric conversion material is controlled at the nanoscale as specified in the present invention, there is a tendency that the use of the thermoelectric conversion material having a higher thermal conductivity κ brings about a greater reduction of thermal conductivity κ, and particularly, when the thermoelectric conversion material having thermal conductivity κ of more than 5 W/mK is used, the reducing effect of thermal conductivity κ is enhanced.
The salts of the element constituting the thermoelectric conversion material mean, for example, cobalt chloride hydrate and antimony chloride in the case the thermoelectric conversion material is CoSb3, and mean cobalt chloride hydrate, nickel chloride, and antimony chloride in the case the thermoelectric conversion material is Co1-xNixSb3.
The mixing ratio of the ceramic particles to the thermoelectric conversion material particles is preferably 5 to 40 vol. % in the thermoelectric converter obtained by the method of the present invention. The alcohol, which is a solvent of the dispersion liquid, is not specifically limited, as long as it can disperse a salt of an element constituting the thermoelectric conversion material described above and ceramic particles, but ethanol can be preferably used. A pH controlling agent may be added when needed. As the pH controlling agent, which is used to prevent the aggregation of the particles, etc., in a slurry, known agents such as hydrochloric acid, acetic acid, nitric acid, ammonia water, sodium hydrate, and sodium borohydride (NaBH4) can be used
The pH of the dispersion liquid is preferably 3 to 6 or 8 to 11, and more preferably 4 to 6 or 8 to 10.
After the dispersion liquid is prepared, the dispersion liquid is dropped into a solution containing a reducing agent. The reducing agent can be of any type which can reduce an ion of an element constituting the thermoelectric conversion material, such as NaBH4 or hydrazine.
There is an ion of the raw material of the thermoelectric conversion material, such as Co ion or Sb ion, in the dispersion liquid containing a salt of an element constituting the thermoelectric conversion material. Therefore, as shown in
As described above, when particles of an element constituting the thermoelectric conversion material are deposited, ceramic particles having a diameter of 1 to 100 nm and particles of an element constituting the thermoelectric conversion material are evenly distributed in the dispersion liquid, because ceramic particles having the diameter of 1 to 100 nm are present in the dispersion liquid.
The dispersion liquid is subject to a heat treatment, preferably a hydro-thermal treatment, to form a thermoelectric conversion material from the elements constituting the same. The material is then dried to obtain an aggregate wherein the ceramic particles and the thermoelectric conversion material particles are evenly mixed. After the aggregate is, if necessary, washed and dried, it is SPS-sintered using a conventional sintering method, at 400 to 800° C., preferably at 450 to 650° C., for example, in the case of CoSb3, so that a thermoelectric converter having a continuous phase of the thermoelectric conversion material is obtained, in which a dispersion phase of scattered ceramic particles is formed.
The structure size (the particle diameter of or the dispersion distance between the insulating materials) can be controlled at the nanoscale by the method for manufacturing of the thermoelectric conversion material of the present invention. That is, by preparing an aggregate wherein the ceramic particles having an average particle diameter of 1 to 100 nm and the thermoelectric conversion material particles are evenly distributed, the structure size of the thermoelectric converter (dispersion distance between the ceramics) becomes smaller than the mean free path of the phonons and preferably larger than the mean free path of a carrier, so that the phonons in the thermoelectric converter are sufficiently scattered and thermal conductivity κ can be decreased. Consequently, a thermoelectric converter having a high performance index ZT represented by the formula (1) is obtained. As can be seen above, a thermoelectric converter having a high performance index ZT more than 2, which was difficult to realize in the prior art, can be obtained by the method for manufacturing the thermoelectric converter according to the present invention.
1.0 g of cobalt chloride and 2.88 g of antimony chloride were added to and dissolved in 100 mL of ethanol, and 0.2 g of alumina particles having the average particle diameter of 30 nm were added thereto to prepare a dispersion liquid. The pH of the dispersion liquid was 1. The dispersion liquid was dropped into a reducing agent solution wherein 2.0 g of sodium borohydride was dissolved in 100 mL of ethanol. Then, impurities were removed by washing with a mixed solution of ethanol and water, followed by a hydrothermal synthesis for 24 hours at 240° C. to produce a thermoelectric conversion material of CoSb3 compound. The TEM image of the composite particles thus obtained is shown in
In the thermoelectric converter thus obtained, the dispersion phase of alumina having the average diameter of 1 to 100 nm was evenly distributed in the continuous phase of CoSb3 thermoelectric conversion material.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2007-150585 | Jun 2007 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2008/060321 | 5/29/2008 | WO | 00 | 12/4/2009 |
