JPH01304609A - Superconductive wire rod with high critical current density - Google Patents
Superconductive wire rod with high critical current densityInfo
- Publication number
- JPH01304609A JPH01304609A JP63133690A JP13369088A JPH01304609A JP H01304609 A JPH01304609 A JP H01304609A JP 63133690 A JP63133690 A JP 63133690A JP 13369088 A JP13369088 A JP 13369088A JP H01304609 A JPH01304609 A JP H01304609A
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- powder
- tube
- superconducting
- critical current
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000000843 powder Substances 0.000 claims abstract description 82
- 239000000919 ceramic Substances 0.000 claims abstract description 44
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 9
- 239000001301 oxygen Substances 0.000 claims abstract description 9
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 229910052784 alkaline earth metal Inorganic materials 0.000 claims abstract description 4
- 150000001875 compounds Chemical class 0.000 claims abstract description 4
- 150000001342 alkaline earth metals Chemical class 0.000 claims abstract description 3
- 239000010949 copper Substances 0.000 claims abstract description 3
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract 2
- 229910052802 copper Inorganic materials 0.000 claims abstract 2
- 239000011812 mixed powder Substances 0.000 claims description 15
- 239000011248 coating agent Substances 0.000 claims 1
- 238000000576 coating method Methods 0.000 claims 1
- 238000010438 heat treatment Methods 0.000 abstract description 7
- 239000002131 composite material Substances 0.000 description 18
- 239000002245 particle Substances 0.000 description 10
- 238000005245 sintering Methods 0.000 description 6
- 239000002994 raw material Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000008602 contraction Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- 238000005491 wire drawing Methods 0.000 description 2
- -1 alkaline earth metal carbonate Chemical class 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910021521 yttrium barium copper oxide Inorganic materials 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E40/00—Technologies for an efficient electrical power generation, transmission or distribution
- Y02E40/60—Superconducting electric elements or equipment; Power systems integrating superconducting elements or equipment
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、安定した高臨界電流密度を有する超電導線
材に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a superconducting wire having a stable and high critical current density.
一般に、Ｙを含む希土類元素（以下、この元素をＲで示
す）、アルカリ土類金属、Ｃｕおよび酸素からなるペロ
ブスカイト構造を有する化合物（以下、この化合物を超
電導セラミックスという）は、液体窒素で冷却可能な７
７°Ｋにおいて超電導現象を示すことが知られている。In general, compounds with a perovskite structure consisting of rare earth elements (hereinafter referred to as R) including Y, alkaline earth metals, Cu, and oxygen (hereinafter referred to as superconducting ceramics) can be cooled with liquid nitrogen. 7
It is known that superconductivity occurs at 7°K.
上記超電導セラミックスの粉末を用いて超電導線材を製
造する方法としては、原料粉末として、いずれも平均粒
径： １０閘以下のＲ２０３粉末、アルカリ土類金属の
炭酸塩粉末、およびＣｕＯ粉末を用意し、これら原料粉
末を所定の配合組成に配合し、混合し、大気中または酸
素雰囲気中で、温度二８５０〜９５０℃にて焼成し、ペ
ロブスカイト構造を有する超電導セラミックスを製造し
、これを平均粒径：１０訊以下に粉砕して超電導セラミ
ックス粉末とし、この超電導セラミックス粉末をＡｇチ
ューブに充填し、このチューブの両端を封じたのち、ス
ェージング加工、溝ロール加工、またはダイス加工等の
伸線加工を施して、直径：５ｍｍ以下のＡｇ複合ワイヤ
とし、最終的に上記伸線加工されたＡｇ複合ワイヤを大
気中または酸素雰囲気中で、温度＝９００〜９５０℃で
熱処理して超電導線材を製造していた。As a method for manufacturing a superconducting wire using the above superconducting ceramic powder, R203 powder, an alkaline earth metal carbonate powder, and a CuO powder, all of which have an average particle size of 10 or less, are prepared as raw material powders, These raw material powders are blended into a predetermined composition, mixed, and fired at a temperature of 2,850 to 950°C in the air or oxygen atmosphere to produce superconducting ceramics having a perovskite structure, which has an average particle size of: The superconducting ceramic powder is crushed to 10 centimeters or less, and the superconducting ceramic powder is filled into an Ag tube. After sealing both ends of the tube, it is subjected to wire drawing processing such as swaging, groove roll processing, or die processing. A superconducting wire was manufactured by preparing an Ag composite wire with a diameter of 5 mm or less, and finally heat-treating the drawn Ag composite wire at a temperature of 900 to 950° C. in the air or oxygen atmosphere.
このようにして得られた超電導線材はＡｇチューブの内
部に超電導セラミックス粉末の焼結体が充填されている
構造となっている。The superconducting wire thus obtained has a structure in which the inside of an Ag tube is filled with a sintered body of superconducting ceramic powder.
ところが、上記従来の超電導線材は、伸線加工して得ら
れたＡｇ複合ワイヤを大気中または酸素雰囲気中、温度
：９００〜９５０℃で熱処理する工程において、上記Ａ
ｇ複合ワイヤ内に充填されている超電導セラミックス粉
末は焼結収縮し、超電導線材の外被のＡｇチューブと上
記焼結収縮した超電導セラミックス粉末焼結体との間に
間隙が生じ、さらに、上記超電導セラミックス粉末焼結
体自体にも亀裂が発生することがあった。However, in the above-mentioned conventional superconducting wire, the above-mentioned A
g The superconducting ceramic powder filled in the composite wire is sintered and shrunk, and a gap is created between the Ag tube of the outer sheath of the superconducting wire and the sintered superconducting ceramic powder sintered body, and the superconducting Cracks also occurred in the ceramic powder sintered body itself.
このような間隙または亀裂の有する超電導線材は、Ａｇ
チューブから超電導セラミックスへの電気の流れが安定
せず、超電導セラミックスに流れる臨界電流密度も低く
なり、不安定となる等の問題点が生じていた。A superconducting wire having such gaps or cracks is Ag
Problems have arisen in that the flow of electricity from the tube to the superconducting ceramics is not stable, and the critical current density flowing through the superconducting ceramics is also low and unstable.
そこで、本発明者等は、かかる問題点を解決すべく研究
を行なった結果、
Ａｇチューブの中心に超電導セラミックスの有形体を装
入するとともに、上記超電導セラミックス粉末有形体と
Ａｇチューブの間に、Ａｇ粉末またはＡｇ粉末と超電導
セラミックス粉末との混合粉末（以下、Ａｇ混合粉末と
いう）を充填してなるＡｇ複合チューブを作成し、上記
Ａｇ複合チューブを伸線加工してＡｇ複合ワイヤとし、
ついで上記Ａｇ複合ワイヤを大気中または酸素雰囲気中
で熱処理して得られた超電導線材は、Ａｇチューブと、
Ａｇ粉末焼結体層またはＡｇ混合粉末焼結体層と、超電
導セラミックス焼結体とからなる断面構造を有しており
、安定した高臨界電流密度を有することを知見したので
ある。この発明はかかる知見に基づくものであって、以
下この発明の高臨界電流密度を有する超電導線材の断面
構造を図面を用いて説明する。Therefore, the present inventors conducted research to solve such problems, and as a result, they inserted a superconducting ceramic material into the center of an Ag tube, and inserted a material between the superconducting ceramic powder material and the Ag tube. Create an Ag composite tube filled with Ag powder or a mixed powder of Ag powder and superconducting ceramic powder (hereinafter referred to as Ag mixed powder), wire-draw the Ag composite tube to make an Ag composite wire,
Next, the superconducting wire obtained by heat-treating the Ag composite wire in air or oxygen atmosphere has an Ag tube,
They found that it has a cross-sectional structure consisting of an Ag powder sintered body layer or an Ag mixed powder sintered body layer and a superconducting ceramic sintered body, and has a stable high critical current density. The present invention is based on this knowledge, and the cross-sectional structure of the superconducting wire having a high critical current density of the present invention will be explained below with reference to the drawings.
第１図は、この発明の高臨界電流密度を有する超電導線
材の断面説明図であり、第１図において１はＡｇチュー
ブ、２はＡｇ粉末焼結体層、３は超電導セラミックス粉
末焼結体である。第１図に示されるように、Ａｇチュー
ブ１と超電導セラミックス粉末焼結体３の間にＡｇ粉末
焼結体層２を介在せしめることにより、
（１）上記Ａｇ複合ワイヤを大気中または酸素雰囲気中
で熱処理するときに、Ａｇ粉末および超電導セラミック
ス粉末は共に焼結収縮すると同時にＡｇチューブ１とＡ
ｇ粉末焼結体層２の間に間隙４が発生するが、Ａｇチュ
ーブ１とＡｇ粉末焼結体層２とは同一組成の金属である
ために、上記Ａｇチューブ１とＡｇ粉末焼結体層２とは
少なくとも１個所において強固な冶金的接合がなされて
おり、上記間隙４の発生による電流の不安定な流れは起
らない。FIG. 1 is an explanatory cross-sectional view of a superconducting wire having a high critical current density according to the present invention. In FIG. 1, 1 is an Ag tube, 2 is an Ag powder sintered body layer, and 3 is a superconducting ceramic powder sintered body. be. As shown in FIG. 1, by interposing the Ag powder sintered body layer 2 between the Ag tube 1 and the superconducting ceramic powder sintered body 3, (1) the Ag composite wire is placed in the air or oxygen atmosphere; During the heat treatment, the Ag powder and superconducting ceramic powder both sinter and shrink, and at the same time
A gap 4 is generated between the Ag powder sintered body layer 2, but since the Ag tube 1 and the Ag powder sintered body layer 2 are made of metals with the same composition, the Ag tube 1 and the Ag powder sintered body layer are A strong metallurgical connection is made to the electrode 2 at at least one location, and unstable current flow due to the generation of the gap 4 does not occur.
（２）上記超電導セラミックス粉末焼結体３とＡｇ粉末
焼結体層２とは、その境界において、２種類の粉末どう
しが混合接触して焼結されているためにアンカー効果が
働き、電気的接触がきわめて良好である。(2) At the boundary between the superconducting ceramic powder sintered body 3 and the Ag powder sintered body layer 2, two types of powder are mixed and sintered in contact with each other, so an anchor effect works, and electrical Very good contact.
（３）上記熱処理中に超電導セラミックス粉末が焼結収
縮しても、超電導セラミックス粉末の外周に存在するＡ
ｇ粉末も同時に焼結収縮し、上記Ａｇ粉末の焼結収縮量
を上記超電導セラミックス粉末の焼結収縮量よりも大と
なるようにしておけば、上記超電導セラミックス粉末は
、外周に存在するＡｇ粉末の収縮により圧縮力を受けな
がら焼結収縮することになり、超電導セラミックス粉末
焼結体に亀裂が発生することはない。(3) Even if the superconducting ceramic powder undergoes sintering shrinkage during the above heat treatment, A that exists on the outer periphery of the superconducting ceramic powder
The g powder also undergoes sintering shrinkage at the same time, and if the amount of sintering shrinkage of the Ag powder is set to be larger than the amount of sintering shrinkage of the superconducting ceramic powder, the superconducting ceramic powder will shrink due to the Ag powder existing on the outer periphery. The superconducting ceramic powder sintered body undergoes sintering contraction while being subjected to compressive force due to the contraction of the superconducting ceramic powder, and no cracks occur in the superconducting ceramic powder sintered body.
などのすぐれた効果を発揮するものである。It has excellent effects such as:
第１図では、Ａｇ粉末焼結体層２を有する超電導線材に
ついて述べたが、第２図に示されるように、Ａｇ粉末と
超電導セラミックス粉末の混合粉末の焼結体からなる層
、すなわちＡｇ混合粉末焼結体層２′を介在させてもよ
い。Ａｇ混合粉末は、Ａｇ粉末よりも超電導セラミック
ス粉末に近い焼結収縮性を示すので、熱処理して得られ
た上記Ａｇ混合粉末焼結体層２′は、Ａｇ粉末焼結体層
２よりも超電導セラミックス粉末焼結体３に対する接合
性がすぐれている。上記Ａｇ混合粉末焼結体層２′を形
成するＡｇ混合粉末は、Ａｇ粉末に対して超電導セラミ
ックス粉末を７５重量％以下混合してなる粉末であって
、上記超電導セラミックス粉末が７５重量％を越えて添
加されるとＡｇチューブとの十分な冶金的結合が得られ
ないので好ましくない。In Fig. 1, a superconducting wire having a Ag powder sintered body layer 2 was described, but as shown in Fig. 2, a layer consisting of a sintered body of a mixed powder of Ag powder and superconducting ceramic powder, that is, an Ag mixed A powder sintered body layer 2' may be interposed. Since the Ag mixed powder exhibits sintering shrinkage properties closer to those of superconducting ceramic powder than Ag powder, the Ag mixed powder sintered body layer 2' obtained by heat treatment has a higher superconductivity than the Ag powder sintered body layer 2. The bondability to the ceramic powder sintered body 3 is excellent. The Ag mixed powder forming the Ag mixed powder sintered body layer 2' is a powder obtained by mixing 75% by weight or less of superconducting ceramic powder with Ag powder, and the superconducting ceramic powder exceeds 75% by weight. If it is added, sufficient metallurgical bonding with the Ag tube cannot be obtained, which is not preferable.
上記Ａｇ粉末は、平均粒径：１〜２００μｓの範囲の粉
末を使用し、また上記超電導セラミックス粉末は、平均
粒径：２〜１ｏ−の範囲内のものを使用するとよい結果
が得られる。Good results can be obtained by using the Ag powder with an average particle size in the range of 1 to 200 μs, and using the superconducting ceramic powder with the average particle size in the range of 2 to 1°.
この発明の高臨界電流密度を有する超電導線材の超電導
セラミックス粉末焼結体３の断面形状は円形に限らず四
角形、五角形、六角形等の多角形、その他任意の形状を
有するものであってもよい。The cross-sectional shape of the superconducting ceramic powder sintered body 3 of the superconducting wire having a high critical current density according to the present invention is not limited to a circle, but may be a polygon such as a quadrangle, a pentagon, a hexagon, or any other shape. .
つぎに、この発明を実施例にもとづいて具体的に説明す
る。Next, the present invention will be specifically explained based on examples.
実施例 １
原料粉末として、いずれも平均粒径：６ｕｎのＹ２Ｏ３
粉末、Ｂ ａ ＣＯａ粉末、およびＣｕＯ粉末を用意し
、これら原料粉末を、Ｙ２Ｏ３：１５．１３％、Ｂ ａ
ＣＯ３： ５２ 、８９％、Ｃｕ Ｏ：３１．９８％
（以上重量％）の割合で配合し、混合し、この混合粉末
を、大気中、温度、９００’Ｃ１１０時間保持の条件で
焼成し、平均粒径：２．８ｕｍに粉砕してＹＢａ２Ｃｕ
３Ｏ７の組成を有するペロブスカイト構造の超電導セラ
ミックス粉末を製造し、これを直径：４．５ｍ＋ｅＸ長
さ＋１００ｍｍの円柱状圧粉体にプレス成形した。Example 1 As raw material powder, Y2O3 with average particle size: 6un was used in all cases.
Prepare powder, B a COa powder, and CuO powder, and mix these raw powders with Y2O3: 15.13%, B a
CO3: 52, 89%, CuO: 31.98%
The mixed powder was fired in the air at a temperature of 900'C for 110 hours and ground to an average particle size of 2.8 um.
A superconducting ceramic powder with a perovskite structure having a composition of 3O7 was produced, and this was press-molded into a cylindrical compact having a diameter of 4.5 m + length + 100 mm.
一方、内径：６．５ｍｍＸ肉厚：０．３ｍｍＸ長さ＋１
２０ｍｍのＡｇチューブおよび平均粒径：１１０μｓの
Ａｇ粉末を用意し、上記円柱状圧粉体をＡｇチューブの
中央に配置し、上記円柱状圧粉体とＡｇチューブの間に
上記Ａｇ粉末を充填した。On the other hand, inner diameter: 6.5mm x wall thickness: 0.3mm x length + 1
A 20 mm Ag tube and Ag powder with an average particle size of 110 μs were prepared, the cylindrical compact was placed in the center of the Ag tube, and the Ag powder was filled between the cylindrical compact and the Ag tube. .
このようにして得られたＡｇ複合チューブの両端をプレ
ス加工により封じたのち、上記Ａｇ複合チューブを伸線
加工し、外径＝２龍のＡｇ複合ワイヤとした。After sealing both ends of the Ag composite tube thus obtained by press working, the Ag composite tube was wire drawn to obtain an Ag composite wire having an outer diameter of 2 mm.
上記Ａｇ複合ワイヤを、酸素雰囲気中、温度：９２０℃
、２４時間保持の条件で熱処理し、この発明の高臨界電
流密度を有する超電導線材を作成した。The above Ag composite wire was heated in an oxygen atmosphere at a temperature of 920°C.
A superconducting wire having a high critical current density according to the present invention was produced by heat treatment under conditions of holding the wire for 24 hours.
上記この発明の超電導線材を５本作成し、それらの臨界
電流密度を測定し、それらの結果を第１表に示した。Five superconducting wires of the present invention were prepared, and their critical current densities were measured. The results are shown in Table 1.
実施例 ２
平均粒径：５０茄のＡｇ粉末に、平均粒径：８郁の超電
導セラミックス粉末を３０重量％配合し、混合してＡｇ
混合粉末を作成し、上記Ａｇ混合粉末を実施例１で作成
した円柱状圧粉体とＡｇチューブの間に充填し、Ａｇ複
合チューブを作成した。Example 2 30% by weight of superconducting ceramic powder with an average particle size of 8 mm was added to Ag powder with an average particle size of 50 mm, and the mixture was mixed to form Ag powder.
A mixed powder was prepared, and the above Ag mixed powder was filled between the cylindrical green compact prepared in Example 1 and an Ag tube to prepare an Ag composite tube.
上記Ａｇ複合チューブを実施例１と全く同様に伸線加工
および熱処理を施してこの発明の高臨界電流密度を有す
る超電導線材を５本作成し、それらの臨界電流密度を測
定して、その結果を第１表に示した。Five superconducting wires having a high critical current density of the present invention were prepared by subjecting the Ag composite tube to wire drawing and heat treatment in exactly the same manner as in Example 1, and their critical current densities were measured. It is shown in Table 1.
一方、比較のために、従来例として上記実施例１で用い
た平均粒径：２．８ｔｌｒａのＹＢａ２Ｃｕ３Ｏ７の組
成を存するペロブスカイト構造を有する超電導セラミッ
クス粉末を、上記実施例１で用いたＡｇチューブに充填
してＡｇ粉末またはＡｇ混合粉末を充填することなくＡ
ｇ複合チューブを作成し、このＡｇ複合チューブの両端
をプレス加工により封じたのち伸線加工し、外径：２ｍ
ｍのＡｇ複合ワイヤとし、ついて上記Ａｇ複合ワイヤを
上記実施例１と同じ条件（酸素雰囲気中、温度： ９２
０”Ｃ１２４時間保持）で熱処理して従来法による超電
導線材を５本作成し、これらの臨界電流密度を測定し、
その結果を第１表に示した。On the other hand, for comparison, a superconducting ceramic powder having a perovskite structure having an average particle size of 2.8 tlra and a composition of YBa2Cu3O7 used in the above Example 1 as a conventional example was filled into the Ag tube used in the above Example 1. A without filling Ag powder or Ag mixed powder
g A composite tube was created, both ends of this Ag composite tube were sealed by press working, and then wire drawn to give an outer diameter of 2 m.
m Ag composite wire, and the Ag composite wire was then heated under the same conditions as in Example 1 (in oxygen atmosphere, temperature: 92
Five superconducting wires were prepared by the conventional method by heat treatment at 0"C (held for 124 hours), and their critical current densities were measured.
The results are shown in Table 1.
上記第１表の結果から、従来例の超電導線材の臨界電流
密度（Ａ／ｃＪ）は低く、しかもバラツキがあり、安定
した超電導特性を示さないのに対し、この発明の実施例
１および２の超電導線材の臨界電流密度（Ａ／ｃ＋ｔ）
は、はぼ一定の安定した高臨界電流密度を示すことがわ
かる。From the results in Table 1 above, it is clear that the critical current density (A/cJ) of the conventional superconducting wire is low and has variations, and does not exhibit stable superconducting properties, while that of Examples 1 and 2 of the present invention Critical current density of superconducting wire (A/c+t)
It can be seen that this shows a stable high critical current density that is almost constant.
この発明は、Ａｇ粉末焼結体層またはＡｇ混合粉末焼結
体層を、Ａｇチューブと超電導セラミックス粉末焼結体
の間に介在させるという簡単な構造により安定した高臨
界電流密度を有する超電導線材を得ることができるので
産業上すぐれた効果をもたらすものである。The present invention provides a superconducting wire having a stable high critical current density through a simple structure in which an Ag powder sintered body layer or an Ag mixed powder sintered body layer is interposed between an Ag tube and a superconducting ceramic powder sintered body. It has excellent industrial effects.
第１図は、この発明の高臨界電流密度を有する超電導線
材の断面概略図、
第２図は、この発明の高臨界電流密度を有するもう１つ
の超電導線材の断面概略図、
１：Ａｇチューブ
２ ： Ａｇ粉末焼結体層
２’：Ａｇ混合粉末焼結体層
３：超電導セラミックス粉末焼結体
４：間隙FIG. 1 is a schematic cross-sectional view of a superconducting wire having a high critical current density of the present invention. FIG. 2 is a schematic cross-sectional view of another superconducting wire having a high critical current density of the present invention. 1: Ag tube 2 : Ag powder sintered body layer 2': Ag mixed powder sintered body layer 3: Superconducting ceramic powder sintered body 4: Gap
Claims (3)
び酸素からなる組成を有しペロブスカイト構造を有する
化合物（以下、超電導セラミックスという）粉末焼結体
をＡｇチューブで被覆してなる高臨界電流密度を有する
超電導線材において、上記Ａｇチューブと上記超電導セ
ラミックス粉末焼結体の間にＡｇ粉末焼結体層を介在さ
せたことを特徴とする高臨界電流密度を有する超電導線
材。(1) High critical current obtained by coating a powder sintered body of a compound (hereinafter referred to as superconducting ceramics) with a perovskite structure with a composition consisting of rare earth elements including Y, alkaline earth metals, copper, and oxygen with an Ag tube. A superconducting wire having a high critical current density, characterized in that an Ag powder sintered body layer is interposed between the Ag tube and the superconducting ceramic powder sintered body.
焼結体の間にＡｇ粉末と超電導セラミックス粉末の混合
粉末焼結体層を介在させたことを特徴とする請求項１記
載の高臨界電流密度を有する超電導線材。(2) A high critical current density according to claim 1, characterized in that a mixed powder sintered body layer of Ag powder and superconducting ceramic powder is interposed between the Ag tube and the superconducting ceramic powder sintered body. Superconducting wire.
形または多角形であることを特徴とする請求項１または
２記載の高臨界電流密度を有する超電導線材。(3) The superconducting wire having a high critical current density according to claim 1 or 2, wherein the cross-sectional shape of the superconducting ceramic sintered body is circular or polygonal.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63133690A JPH01304609A (en) | 1988-05-31 | 1988-05-31 | Superconductive wire rod with high critical current density |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63133690A JPH01304609A (en) | 1988-05-31 | 1988-05-31 | Superconductive wire rod with high critical current density |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01304609A true JPH01304609A (en) | 1989-12-08 |
Family
ID=15110600
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63133690A Pending JPH01304609A (en) | 1988-05-31 | 1988-05-31 | Superconductive wire rod with high critical current density |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01304609A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2362268B (en) * | 2000-05-12 | 2005-05-11 | Notetry Ltd | Electrical machine |
-
1988
- 1988-05-31 JP JP63133690A patent/JPH01304609A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2362268B (en) * | 2000-05-12 | 2005-05-11 | Notetry Ltd | Electrical machine |
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