CN101345284A - P type europium cadmium stibium based pyroelectric material and preparation method thereof - Google Patents
P type europium cadmium stibium based pyroelectric material and preparation method thereof Download PDFInfo
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- CN101345284A CN101345284A CNA2008100423231A CN200810042323A CN101345284A CN 101345284 A CN101345284 A CN 101345284A CN A2008100423231 A CNA2008100423231 A CN A2008100423231A CN 200810042323 A CN200810042323 A CN 200810042323A CN 101345284 A CN101345284 A CN 101345284A
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Abstract
The invention relates to a p-typed Eu-Cd-Sb based thermoelectric material and a preparation method thereof, belonging to the field of thermoelectric material technique. The invention provides the p-typed Eu-Cd-Sb based thermoelectric material which is characterized in that the composition of the p-typed Eu-Cd-Sb based electro-thermal material is AxByCz (wherein, x=0.9-1.1, y=1.8-2.2 and z=1.8-2.2); wherein, A is Eu or combination of Eu, Mg, Ca, Sr and Yb; B is Cd or the combination of Cd, Mg, Mn and Zn; C is Sb or the combination of Sb, As and Bi. The preparation method of the invention comprises three steps of: compounding, synchronizing and sintering. The p-typed Eu-Cd-Sb based thermoelectric material related to by the invention has high thermoelectric conversion efficiency at the temperature about 300 to 400 DEG C; for example, optimization coefficient of the p-typed Eu-Cd-Sb based thermoelectric material achieves 0.66 at the middle temperature near 377 DEG C and the optimized p-typed Eu-Cd-Sb based thermoelectric material can be used as a middle-temperature thermoelectric conversion device.
Description
Technical field
The present invention relates to a kind of p type europium cadmium stibium based pyroelectric material and preparation method thereof, belong to the technical field of thermoelectric material.
Background technology
Thermoelectric material is a kind of functional material with heat energy and the direct conversion of electric energy, and its principle is based on Seebeck effect and Pei Er Supreme Being's effect, is the key foundation material of high-tech new energy field.There is not mechanical driving part by its thermoelectric conversion element of making (as refrigerator, air-conditioning, military generator, power station etc.), it is simple in structure, in light weight, do not need harmful substances such as fluorine Lyons yet, have cleaning, efficient, pollution-free, do not have noise and series of advantages such as the life-span is long, firm, reliability height, can be widely used in utilization of national defence, space flight, automobile, microelectronics, high-technology field and vehicle exhaust, industry useless (gas) heat.
The key of thermoelectric heat generation system is a thermoelectric material, and its performance is used dimensionless performance index ZT (ZT=S usually
2σ T/ κ, wherein S is the seebeck coefficient; σ is a conductivity; κ is a thermal conductivity, and T is an absolute temperature) expression.The ZT value is high more, and the expression material property is good more, and thermopower generation efficiency is also just high more.At present, the ZT value of practical block thermoelectric material is generally near 1.0.Have the thermoelectric material of using value and application prospect to mainly contain at present (Bi, Sb)
2(Te, Se)
3, β-Zn
4Sb
3, Yb
14MnSb
11, fill drill with ferrule ore deposit, (PbTe)
0.85(AgSbTe)
0.15(TAGS), Pb
18AgSbTe
20, cage shape thing and SiGe etc.
Because the temperature range difference that the thermoelectric material of different systems is used, the preparation technology of existing thermoelectric material adopts methods such as vacuum melting-annealing-fragmentation-hot pressed sintering or long-time solid phase reaction-hot pressed sintering more in addition.The shortcoming of these methods is, solid phase reaction and hot pressed sintering time are long, very easily cause the component deviation, and the dephasign content height of prepared material causes thermoelectricity capability to reduce.The preparation method of p type europium cadmium stibium based pyroelectric material provided by the invention, be to adopt the high purity elemental raw material in glove box, to prepare burden, the assurance raw material is not oxidized, employing is coated with the carbon quartz ampoule as reaction vessel, for guaranteeing reaction evenly, adopts and slowly gives birth to temperature, long-time fusion, slowly the temperature schedule of hypothermic response adopts discharge plasma sintering (Spark Plasma sintering is called for short SPS) technology sintering block materials.SPS is novel special pressurization Fast Sintering technology, claims also on the document that has that SPS is a plasma activated sintering.The process advantage of SPS is: programming rate is fast, homogeneous heating, and sintering temperature is low, and temperature retention time is short, and production efficiency height, product are organized tiny even.
The thermoelectric material of the similar composition of bibliographical information such as Mg
3Sb
2, CaZn
2Sb
2, Ca
xYb
1-Zn
2Sb
2And BaZn
2Sb
2The ZT value between 0.21~0.52, a patent " a kind of cadmium-stibium-based p type thermal electrical material and preparation method thereof " gained sample YbCd is only arranged
2Sb
2The ZT value reaches 0.8 in the time of 430 ℃.The bibliographical information of data such as at present only synthetic about europium cadmium antimony, crystal structure and cryomagnetism does not have the research of thermoelectricity capability aspect.The high conversion efficiency of thermoelectric of p type europium cadmium stibium based pyroelectric material tool that the present invention relates to, during as 377 ℃, the figure of merit of europium cadmium antimony reaches 0.66.
Summary of the invention
The purpose of this invention is to provide a kind of p type europium cadmium stibium based pyroelectric material and preparation method thereof.
The europium cadmium stibium based high efficiency thermoelectric transition material of the p type that the present invention relates to is characterized in that composition formula is A
xB
yC
z(z=1.8-2.2): A is the combination of Eu or Eu and Mg, Ca, Sr, Yb for x=0.9-1.1, y=1.8-2.2; B is the combination of Cd or Cd and Mg, Mn, Zn; C is the combination of Sb or Sb and P, As, Bi.
Preparation method of the present invention comprises batching, synthetic and three steps of sintering:
(1) be raw material with high pure metal simple substance, according to A
xB
yC
z(z=1.8-2.2): A is the combination of Eu or Eu and Mg, Ca, Sr, Yb for x=0.9-1.1, y=1.8-2.2; B is the combination of Cd or Cd and Mg, Mn, Zn; C is the combination of Sb or Sb and P, As, Bi.
(2) the compound inclosure with step (1) preparation is coated with in the quartz ampoule of carbon, and atmosphere is vacuum or charges into small amounts of inert gas.Quartz ampoule slowly is heated to 700~900 ℃ of insulations 7~14 days, makes raw metal carry out abundant chemical reaction, slowly cool to room temperature, fully grind, promptly get the powder of p type europium cadmium stibium based pyroelectric material.
(3) with the fine and close block of the powder sintered one-tenth of the discharging plasma sintering equipment p type europium cadmium stibium based pyroelectric material that step (2) is synthetic, sintering condition is pressure 30~100MPa, 300~500 ℃ of temperature, and temperature retention time 5~30min, atmosphere is vacuum.
Description of drawings
Fig. 1 is p type EuCd provided by the invention
2Sb
2The X ray diffracting spectrum of thermoelectric material illustrates that its principal phase is an europium cadmium antimony.The cell parameter that records is
And
Fig. 2 is p type EuCd provided by the invention
2Sb
2The structure of thermoelectric material illustrates EuCd
2Sb
2Be stratiform CaAl
2Si
2Type trigonal crystal structure (P-3m), Eu is positioned at [Cd
2Sb
2] between the double-layer network.
Fig. 3 is p type EuCd provided by the invention
2Sb
2The conductivity of thermoelectric material and Seebeck coefficient, illustrate europium cadmium antimony have high conductivity (75~113S/cm), high Seebeck coefficient (227~306 μ V/K).
Fig. 4 is p type EuCd provided by the invention
2Sb
2The thermal conductivity of thermoelectric material illustrates EuCd
2Sb
2Has low lattice thermal conductivity (1.42~0.74W/mK).
Fig. 5 is p type EuCd provided by the invention
2Sb
2The power factor of thermoelectric material and figure of merit illustrate p type EuZn
2Sb
2Have high power factor (7.5 μ W/cmK
2) and high figure of merit (0.66).
Embodiment
Further specify the present invention below by embodiment, but be not limited only to embodiment.
In following examples, with conductivity (S/cm), the conductivity of expression material, this numerical value is high more, illustrates that conductivity is good more; With the thermoelectric force of Seebeck coefficient (μ V/K) expression material, this numerical value is high more, illustrates that the electrical potential difference of temperature difference generation is high more; Power (μ W/cmK with the conversion of the thermoelectricity of power factor representation material
2), this numerical value is high more, illustrates that the power of thermoelectric conversion is high more; With the thermal conductivity of thermal conductivity (W/mK) expression material, this numerical value is low more, illustrates that thermal loss is more little; Represent the conversion efficiency of thermoelectric of material with figure of merit, this numerical value is high more, illustrates that the efficient of thermoelectric conversion is high more.
Table 1 has been listed structure and the performance of embodiment 1, and table 2 has been listed composition and the preparation technology of embodiment 1-8.
Embodiment 1
Adopting high-purity (>99.9%) metal simple-substance to press the component batching of table 2 appointment respectively, raw material is put in the graphite crucible, enclose quartz ampoule, is vacuum in the quartz ampoule.Above-mentioned quartz ampoule is put into high temperature furnace, slowly give birth to temperature, be incubated 14 days, slowly cool to room temperature, fully grind, promptly get the thermoelectric material powder to 800 ℃.Above-mentioned powder is prepared into bulk material with the discharging plasma sintering equipment direct sintering, and sintering condition is pressure 60MPa, 400 ℃ of temperature, and temperature retention time 15min, atmosphere is vacuum.Then, test X ray diffracting data, thermal conductivity, Seebeck coefficient and conductivity.Fig. 1-Fig. 5 has provided the characteristic X-ray diffracting spectrum of embodiment 1, structure and The performance test results figure.
The structure of table 1 embodiment 1 and performance
Embodiment 2-8
The preparation process reference example 1 of embodiment 2-8, composition and the preparation technology of embodiment 2-8 see Table 2.
Composition and the preparation technology of table 2 embodiment 2-8
Embodiment | Form | Synthesis temperature time atmosphere | The sintering temperature pressure time |
Embodiment 1 | EuCd 2Sb 2 | 800 ℃ of 14 |
400 ℃ of 60MPa 15 minutes |
Embodiment 2 | Eu 0.9Cd 2.2Sb 1.8 | 800 ℃ of 14 |
400 ℃ of 60MPa 15 minutes |
Embodiment 3 | (Eu 0.5Yb 0.5)Cd 2Sb 2 | 900 ℃ of 14 |
500 ℃ of 80MPa 15 minutes |
Embodiment 4 | (Eu 0.5Yb 0.2Ca 0.2Sr 0.1)Cd 2Sb 2 | 900 ℃ of 14 |
450 ℃ of 100MPa 15 minutes |
Embodiment 5 | Eu(CdZn)Sb 2 | 800 ℃ of 14 days vacuum | 440 ℃ of 40MPa 10 minutes |
Embodiment 6 | Eu(CdZn 0.5Mg 0.3Mn 0.2)Sb 2 | 900 ℃ of 14 |
500 ℃ of 100MPa 30 minutes |
Embodiment 7 | EuCd 2(SbBi) | 700 ℃ of 7 days Ar |
400 ℃ of 30MPa 5 minutes |
Embodiment 8 | EuCd 2(SbBi 0.5P 0.3As 0.2) | 700 ℃ of 7 |
400 ℃ of 30MPa 5 minutes |
Claims (7)
1, a kind of p type europium cadmium stibium based pyroelectric material is characterized in that composition formula is A
xB
yC
z,
Wherein A is the combination of Eu or Eu and Mg, Ca, Sr, Yb;
B is the combination of Cd or Cd and Mg, Mn, Zn;
C is the combination of Sb or Sb and P, As, Bi;
X=0.9-1.1 wherein; Y=1.8-2.2; Z=1.8-2.2.
2, by the described a kind of p type europium cadmium stibium based pyroelectric material of claim 1, it is characterized in that A is Eu, B is Cd, and C is Sb.
3, by the described a kind of p type europium cadmium stibium based pyroelectric material of claim 1, it is characterized in that composition formula is EuCd
2Sb
2Or Eu
0.9Cd
2.2Sb
1.8Or (Eu
0.5Yb
0.5) Cd
2Sb
2Or (Eu
0.5Yb
0.2Ca
0.2Sr
0.1) Cd
2Sb
2Or Eu (CdZn) Sb
2Or Eu (CdZn
0.5Mg
0.3Mn
0.2) Sb
2Or EuCd
2(SbBi) or EuCd
2(SbBi
0.5P
0.3As
0.2).
4, a kind of preparation method by claim 1 or 2 or 3 described p type europium cadmium stibium based pyroelectric materials is characterized in that comprising the steps:
(1) is raw material with the metal simple-substance, presses composition formula proportioning raw material;
(2) compound that step (1) is prepared grinds after 700~900 ℃ of insulations and obtains powder under vacuum or inert atmosphere;
(3) adopt discharge plasma sintering step (2) to obtain the fine and close block of powder sintered one-tenth.
5, a kind of preparation method by the described p type of claim 4 europium cadmium stibium based pyroelectric material is characterized in that described temperature retention time is 7~14 days.
6, a kind of preparation method by the described p type of claim 4 europium cadmium stibium based pyroelectric material is characterized in that described sintering condition is pressure 30~100MPa, 300~500 ℃ of temperature.
7, a kind of preparation method by the described p type of claim 4 europium cadmium stibium based pyroelectric material, the atmosphere that it is characterized in that described sintering process is vacuum.
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Cited By (4)
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CN105612625A (en) * | 2013-10-17 | 2016-05-25 | 株式会社Lg化学 | Thermoelectric material and method for manufacturing same |
CN110218888A (en) * | 2019-06-20 | 2019-09-10 | 电子科技大学 | A kind of novel Zintl phase thermoelectric material and preparation method thereof |
CN110299444A (en) * | 2019-05-30 | 2019-10-01 | 同济大学 | A kind of EuCd2Sb2 base thermoelectricity material and preparation method thereof |
CN113488578A (en) * | 2021-06-29 | 2021-10-08 | 同济大学 | Low-grade waste heat recovery antimonide thermoelectric module with high conversion efficiency and preparation method thereof |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4193940B2 (en) * | 2004-07-13 | 2008-12-10 | 独立行政法人産業技術総合研究所 | Composite oxide with excellent thermoelectric conversion performance |
CN101101954A (en) * | 2007-07-16 | 2008-01-09 | 中国科学院上海硅酸盐研究所 | A cadmium-stibium-based p type thermal electrical material and its making method |
-
2008
- 2008-08-29 CN CN2008100423231A patent/CN101345284B/en not_active Expired - Fee Related
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN105612625A (en) * | 2013-10-17 | 2016-05-25 | 株式会社Lg化学 | Thermoelectric material and method for manufacturing same |
CN105612625B (en) * | 2013-10-17 | 2018-09-25 | 株式会社Lg化学 | Thermoelectric material and its manufacturing method |
CN110299444A (en) * | 2019-05-30 | 2019-10-01 | 同济大学 | A kind of EuCd2Sb2 base thermoelectricity material and preparation method thereof |
CN110218888A (en) * | 2019-06-20 | 2019-09-10 | 电子科技大学 | A kind of novel Zintl phase thermoelectric material and preparation method thereof |
CN110218888B (en) * | 2019-06-20 | 2021-05-04 | 电子科技大学 | Novel Zintl-phase thermoelectric material and preparation method thereof |
CN113488578A (en) * | 2021-06-29 | 2021-10-08 | 同济大学 | Low-grade waste heat recovery antimonide thermoelectric module with high conversion efficiency and preparation method thereof |
CN113488578B (en) * | 2021-06-29 | 2023-02-07 | 同济大学 | Low-grade waste heat recovery antimonide thermoelectric module with high conversion efficiency and preparation method thereof |
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