JPH0230618A - Oxide high-temperature superconductor - Google Patents
Oxide high-temperature superconductorInfo
- Publication number
- JPH0230618A JPH0230618A JP63180900A JP18090088A JPH0230618A JP H0230618 A JPH0230618 A JP H0230618A JP 63180900 A JP63180900 A JP 63180900A JP 18090088 A JP18090088 A JP 18090088A JP H0230618 A JPH0230618 A JP H0230618A
- Authority
- JP
- Japan
- Prior art keywords
- temperature
- oxide
- oxide high
- temperature superconductor
- superconductor
- 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
- 239000002887 superconductor Substances 0.000 title claims description 25
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 8
- 239000001301 oxygen Substances 0.000 claims description 8
- 229910052760 oxygen Inorganic materials 0.000 claims description 8
- 230000002950 deficient Effects 0.000 claims description 6
- 229910052727 yttrium Inorganic materials 0.000 claims description 4
- 229910052693 Europium Inorganic materials 0.000 claims description 3
- 229910052688 Gadolinium Inorganic materials 0.000 claims description 3
- 229910052689 Holmium Inorganic materials 0.000 claims description 3
- 229910052779 Neodymium Inorganic materials 0.000 claims description 3
- 229910052769 Ytterbium Inorganic materials 0.000 claims description 3
- 229910052746 lanthanum Inorganic materials 0.000 claims description 3
- 229910052691 Erbium Inorganic materials 0.000 claims description 2
- 229910052765 Lutetium Inorganic materials 0.000 claims description 2
- 229910052772 Samarium Inorganic materials 0.000 claims description 2
- 229910052775 Thulium Inorganic materials 0.000 claims description 2
- 230000000694 effects Effects 0.000 description 14
- 239000012071 phase Substances 0.000 description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 10
- 239000007788 liquid Substances 0.000 description 6
- 239000012770 industrial material Substances 0.000 description 5
- 229910052757 nitrogen Inorganic materials 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052692 Dysprosium Inorganic materials 0.000 description 2
- -1 NbTi Substances 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 239000001307 helium Substances 0.000 description 2
- 229910052734 helium Inorganic materials 0.000 description 2
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 231100000331 toxic Toxicity 0.000 description 2
- 230000002588 toxic effect Effects 0.000 description 2
- 229910014454 Ca-Cu Inorganic materials 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000006227 byproduct Substances 0.000 description 1
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010574 gas phase reaction Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000004570 mortar (masonry) Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000008188 pellet Substances 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000003746 solid phase reaction Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 229910052718 tin 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
Landscapes
- Compositions Of Oxide Ceramics (AREA)
- Inorganic Compounds Of Heavy Metals (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】 （産業上の利用分野） この発明は、酸化物高温超電導体に関するものである。[Detailed description of the invention] (Industrial application field) This invention relates to oxide high temperature superconductors.
さらに詳しくは、この発明は、臨界電流密度（Ｊｃ）と
マイスナー効果を向上させた酸化物高温超電導体に関す
るものである。More specifically, the present invention relates to an oxide high temperature superconductor with improved critical current density (Jc) and Meissner effect.
（従来の技術）
超電導体は、超高速スイッチング素子、超高感度センサ
、超電導磁石、超電導コイル、電力用超電導線、磁気シ
ールド材料等への応用が期待されている材料である。(Prior Art) Superconductors are materials that are expected to be applied to ultra-high-speed switching elements, ultra-high sensitivity sensors, superconducting magnets, superconducting coils, superconducting wires for power use, magnetic shielding materials, and the like.
従来よりこの超電導体としては、液体ヘリウム温度付近
の冷却を必要とする
ＮｂＴｉやＮｂ、Ｓｎ等の合金系超電導体が知られてい
たが、近年では、より高い臨界温度（Ｔｃ）をもち、液
体窒素温度の冷却で使用できるＬｎ−Ｂａ−Ｃｕ−０、
Ｂ１−３ｒ−Ｃａ−Ｃｕ−０、Ｔｌ−Ｂａ−Ｃａ−Ｃｕ
−０系等の酸化物高温超電導体が見出されており、新た
な超電導用工業材料として注目されている。Conventionally, alloy superconductors such as NbTi, Nb, and Sn, which require cooling near liquid helium temperature, have been known as superconductors, but in recent years, superconductors with higher critical temperatures (Tc) and liquid helium Ln-Ba-Cu-0, which can be used with nitrogen temperature cooling;
B1-3r-Ca-Cu-0, Tl-Ba-Ca-Cu
High-temperature oxide superconductors such as -0 series have been discovered and are attracting attention as new industrial materials for superconductivity.
特に、これらの酸化物高温超電導体のうちＢ１−３ｒ−
Ｃａ−Ｃｕ−０系は、約１１０にの臨界温度をもつとい
う報告がある。しかしながら、この酸化物は通常の製造
条件下では８０に前後の臨昇温度をもつ相を生成し易い
ので、液体窒素温度よりも高い臨界温度の単相からなる
酸化物に安定に製造することは困難である。In particular, among these oxide high temperature superconductors, B1-3r-
It has been reported that the Ca-Cu-0 system has a critical temperature of about 110°C. However, under normal production conditions, this oxide tends to produce a phase with a critical temperature of around 80°C, so it is difficult to stably produce an oxide consisting of a single phase with a critical temperature higher than the liquid nitrogen temperature. Have difficulty.
また、Ｔ ｌ−Ｂａ−Ｃａ−Ｃｕ−０系ら１２０にとい
うこれまでに最高のＴｃを達成しているものの、ＴＩが
猛毒性であるため、これを工業材料として実用化するこ
とは極めて困難である。In addition, although the Tl-Ba-Ca-Cu-0 system has achieved the highest Tc to date of 120, it is extremely difficult to put it into practical use as an industrial material because TI is highly toxic. It is.
これに対してＬｎ−Ｂａ−Ｃｕ−０系はＴＩのような猛
毒性はない、その臨界温度は９０に前後であり上記二種
の酸化物高温超電導体に比べると低いが、酸素欠陥三重
ペロブスカイト構造からなる単相を比較的再現性よく製
造することができ、また、安定に液体窒・素温度以上の
臨界温度を有するものにすることができるので、工業材
料として期待されるものである。On the other hand, the Ln-Ba-Cu-0 system is not highly toxic like TI, and its critical temperature is around 90°C, which is lower than the two oxide high-temperature superconductors mentioned above, but it is an oxygen-deficient triple perovskite. It is expected to be used as an industrial material because it can produce a single-phase structure with relatively good reproducibility and stably have a critical temperature higher than the temperature of liquid nitrogen.
（発明が解決しようとする課題）
しかしながら、このＬｎ−Ｂａ−Ｃｕ−０系も他の酸化
物高温超電導体と同様に臨界電流密度が低くマイスナー
効果が小さい、このため、超電導コイル、電力用超電導
線、磁気シールド材料等の工業材料へ利用するには問題
が残されている。(Problem to be solved by the invention) However, like other oxide high-temperature superconductors, this Ln-Ba-Cu-0 system also has a low critical current density and a small Meissner effect. Problems remain in its use in industrial materials such as wires and magnetic shielding materials.
そこで、臨界温度だけでなく臨界電流密度とマイスナー
効果にも優れた、工業材料として有用な酸化物高温超電
導体の開発が望まれていた。Therefore, it has been desired to develop a high-temperature oxide superconductor that is useful as an industrial material and has excellent not only critical temperature but also critical current density and Meissner effect.
この発明は、以上の通りの事情を踏まえてなされたもの
であり、粒界相のような異相を共存させることなく、液
体窒素温度以上の臨界温度を安定にもち、しかも高い臨
界電流密度と優れたマイスナー効果を発揮する酸化物高
温超電導体を提供することを目的としている。This invention was made based on the above-mentioned circumstances, and has a stable critical temperature higher than the liquid nitrogen temperature without the coexistence of different phases such as grain boundary phases, as well as high critical current density and excellent properties. The purpose of this research is to provide an oxide high-temperature superconductor that exhibits the Meissner effect.
（課題を解決するための手段）
この発明は、上記の課題を解決するために、酸素欠陥三
重ペロブスカイト構造の
Ｌ ｎ Ｂ ａｚ Ｃｕ ｓ ０７−ａ（式中、Ｌｎは
Ｙ、Ｌａ、Ｎｄ、Ｓｍ、Ｅｕ、Ｇｄ、Ｄｙ、Ｈｏ、Ｅｒ
、Ｔｍ、ＹｂまたはＬｕを示す）
のＬｎサイトおよびＢａサイトをＣａで一部置換したこ
とを特徴とする酸化物高温超電導体を提供する。(Means for Solving the Problems) In order to solve the above problems, the present invention has an oxygen-deficient triple perovskite structure L n B az Cu s 07-a (wherein Ln is Y, La, Nd, Sm , Eu, Gd, Dy, Ho, Er
, Tm, Yb or Lu) is partially substituted with Ca for the Ln site and Ba site.
この発明の酸化物高温超電導体は、この発明者が、酸素
欠陥三重ペロブスカイトｍ造のＬｎＢａ２Ｃｕ、０７−
＃にＣａを固溶させることにより新たに見出されたもの
であり、ＬｎＢａｚＣｕ、０７−、にＣａを固溶させる
と、そのＬｎサイトだけでな（Ｂａサイトも一部Ｃａで
置換した酸素欠陥三重ペロブスカイト構造の酸化物が得
られ、この酸化物が高い臨界電流密度と大きなマイスナ
ー効果を発揮する優れた超電導体となるとの知見に基づ
いている。なお、その場合、基本構造となるＬｎＢａｚ
Ｃｕ、Ｑ、−、のＬｎとしては、Ｙ、Ｌａ、Ｎｄ、Ｓ
ｍ、Ｅｕ、Ｇｄ、Ｄｙ、Ｈｏ、Ｅｒ、Ｔｍ、Ｙｂまたは
Ｌｕを用いることができ、これらからなる酸化物はいず
れも優れた超電導体になる。The oxide high-temperature superconductor of the present invention has been developed by the present inventor to provide LnBa2Cu, 07-
This was newly discovered by making Ca a solid solution in LnBazCu, 07-, and when Ca is made a solid solution in LnBazCu, 07-, not only the Ln site (but also the Ba site is partially replaced with oxygen vacancies) This is based on the knowledge that an oxide with a triple perovskite structure can be obtained, and that this oxide becomes an excellent superconductor that exhibits a high critical current density and a large Meissner effect.In this case, the basic structure of LnBaz
Ln of Cu, Q, -, Y, La, Nd, S
m, Eu, Gd, Dy, Ho, Er, Tm, Yb, or Lu can be used, and oxides made of these are all excellent superconductors.
このようにこの発明の酸化物高温超電導体は、Ｌ ｎ
Ｂ ａｚ Ｃｕ ５０ｙ−ａをＣａで置換した酸化物で
あるが、特に、その組成式を、
Ｌｎ、、Ｃａ ＋＋＋ｇ＋ｘＢ ａｘ−ｅｘｃ ｕ ｓ
Ｏｙ（式中、Ｏ＜ｘ＜０．２．０．０５ ＜ ａ ＜
０．２０である）とすると、その相を酸素欠陥三重ペ
ロブスカイト構造を有するＣａ固溶体の単相にすること
ができるので好ましい、さらに、上記式中のＸおよびα
について、Ｏ＜ｘ≦０．１．０．０７≦α≦０．１２
とすると、臨界電流密度およびマイスナー効果を著し
く向上させることができるのでより好ましい。In this way, the oxide high temperature superconductor of the present invention has L n
It is an oxide in which B az Cu 50y-a is replaced with Ca, but in particular, its composition formula is Ln,, Ca +++g+xB ax-exc u s
Oy (where O<x<0.2.0.05<a<
0.20), it is preferable because the phase can be a single phase of Ca solid solution having an oxygen-deficient triple perovskite structure.
For, O<x≦0.1.0.07≦α≦0.12
This is more preferable since the critical current density and the Meissner effect can be significantly improved.
一方、Ｘおよびαを上記範囲外とするとＢ ａＣｕ Ｏ
，が副成して酸素欠陥三重ペロブスカイト構造からなる
Ｃａ固溶体の単相にすることが困難となり、超電導特性
が低下する。On the other hand, if X and α are outside the above range, B aCu O
, is formed as a by-product, making it difficult to form a single phase Ca solid solution consisting of an oxygen-deficient triple perovskite structure, and the superconducting properties deteriorate.
なお、上記組成範囲にあるこの発明の酸化物高温超電導
体が臨界電流密度やマイスナー効果等の超電導特性に優
れたものとなるのは、酸素欠陥三重ペロブスカイト構造
のＬｎＢａｉ Ｃｕｓ ０７−ａを置換するＣａがその
結晶の電子構造を超電導特性に有利に変化させるためと
考えられ、特に焼結法によりＣａを固溶させる場合には
、そのＣａが焼結助剤として機能し、緻密な焼結体を生
成させるためと考えられる。The oxide high-temperature superconductor of the present invention having the above composition range has excellent superconducting properties such as critical current density and Meissner effect because Ca substitutes for LnBai Cus 07-a in the oxygen-deficient triple perovskite structure. This is thought to be because it changes the electronic structure of the crystal favorably to superconducting properties. Especially when Ca is dissolved in solid solution by the sintering method, the Ca functions as a sintering aid and forms a dense sintered body. It is thought that this is to generate the data.
この発明の酸化物高温超電導体は、成分元素の酸化物、
炭酸化物等を粉砕、混合し、焼結する固相反応により容
易に製造でき、また真空蒸着法、スパッタリング等のＰ
ＶＤ法、溶射法等の気相反応により行っても製造できる
。The oxide high temperature superconductor of the present invention comprises oxides of component elements,
It can be easily produced by a solid phase reaction in which carbonates, etc. are crushed, mixed, and sintered, and P
It can also be produced by a gas phase reaction such as a VD method or a thermal spraying method.
以下、この発明を実施例に基づいて具体的に説明する。Hereinafter, this invention will be specifically explained based on examples.
実施例１
組成式 Ｙ １−ｔ ｅ ａ ＋１＋ｇｌ ＩＩＢ ａ
ｘ−１１Ｋｃ ｕ ｓ Ｏｙで示される組成からなる
Ｙ−Ｃａ−Ｂａ−ＣｕＯ超電導体について、ｘ＝０．０
５ かつα＝０．１ となるように、Ｙ２Ｏ５、Ｃａ
ｃＯｉ、ＢａＣ０，およびＣｕＯ？！：Ｙ、Ｃａ、Ｂａ
および再びメノウ乳鉢で粉砕し、ベレット形成して、酸
素気流中で９３５℃で１０時間の焼結を行い、９０’ｃ
、’ｈｒの冷却速度で４００℃まで炉冷して焼結体を製
造した。Example 1 Compositional formula Y 1-te a +1+gl IIB a
For the Y-Ca-Ba-CuO superconductor having the composition shown by x-11Kc u s Oy, x = 0.0
5 and α=0.1, Y2O5, Ca
cOi, BaC0, and CuO? ! :Y, Ca, Ba
Then, it was ground again in an agate mortar to form a pellet, and sintered at 935°C for 10 hours in an oxygen stream to give a 90'c
A sintered body was produced by furnace cooling to 400° C. at a cooling rate of , 'hr.
この例について、Ｘ線回折、Ｔｃおよび７７Ｋにおける
Ｊｃおよびマイスナー効果を測定したものが表１である
。Table 1 shows the measurements of X-ray diffraction, Tc, Jc at 77K, and Meissner effect for this example.
表１に示したように、後述の比較例との対比か比較例Ｉ
Ｙｘ Ｏｓ 、Ｂａｃｔ）およびＣｕＯをＹ ： Ｂ
ａ ：Ｃｕ＝１：２：３となるように配合して実施例１
と同様の製造条件において焼結体を製造した。As shown in Table 1, in comparison with the comparative example described later, Comparative Example I (YxOs, Bact) and CuO were
Example 1 by blending a:Cu=1:2:3
A sintered body was manufactured under the same manufacturing conditions.
Ｃａは配合しなかった。得られた焼結体は、従来のＹ−
Ｂａ−Ｃａ７Ｃｕ−０超電導体と同一であった。Ca was not blended. The obtained sintered body is a conventional Y-
It was the same as the Ba-Ca7Cu-0 superconductor.
実施例１と同様にＸ線回折、Ｔｃおよび７７Ｋにおける
Ｊｃおよびマイスナー効果を測定し、その結果を表１に
示した。As in Example 1, X-ray diffraction, Tc, Jc at 77K and Meissner effect were measured, and the results are shown in Table 1.
単相の超電導相であり、Ｔｃについては、実施例よりわ
ずかに高い値を示しているが、Ｊｃおよびマイスナー効
果は、著しく低下している。It is a single-phase superconducting phase, and the Tc value is slightly higher than that of the example, but the Jc and Meissner effect are significantly reduced.
比較例２
Ｙ２０ｓ 、ＣａｃＯ３，Ｂａｃｔ３およびＣｕＯをＹ
：Ｃａ：Ｂａ：Ｃｕ＝ ０．９５ ：０．０５：２：３
となるように配合して、実施例１表 １
におけるＪｃおよびマイスナー効果を測定し、その結果
を表１に示した。Comparative Example 2 Y20s, CacO3, Bact3 and CuO
:Ca:Ba:Cu=0.95 :0.05:2:3
The Jc and Meissner effect in Example 1 Table 1 were measured, and the results are shown in Table 1.
ＢａＣｕＯ，が析出し、超電導特性は著しく劣化してい
た。BaCuO was precipitated, and the superconducting properties were significantly deteriorated.
も臨界電流密度（Ｊｃ）とマイスナー効果が著しく向上
し、優れた超電導体となる。Also, the critical current density (Jc) and Meissner effect are significantly improved, making it an excellent superconductor.
（発明の効果）
この発明により、以上詳しく説明したように、Ｌｎサイ
トおよびＢａサイトをＣａで一部置換したＬｎ−Ｃａ−
Ｂａ−Ｃｕ−０系超電導体を単相として容易に製造でき
、液体窒素温度以上の臨界温度を安定に保持しつつ、し
かも高い臨界電流密度と優れたマイスナー効果を発揮さ
せることかできる。(Effects of the Invention) According to the present invention, as explained in detail above, Ln-Ca-
A Ba-Cu-0 based superconductor can be easily manufactured as a single phase, and can exhibit a high critical current density and excellent Meissner effect while stably maintaining a critical temperature higher than the liquid nitrogen temperature.
Claims (2)
ｙ、Ｈｏ、Ｅｒ、Ｔｍ、ＹｂまたはＬｕを示す） のＬｎサイトおよびＢａサイトをＣａで一部置換したこ
とを特徴とする酸化物高温超電導体。(1) Oxygen-deficient triple perovskite structure LnBa_2Cu_3O_7_-_■ (wherein, Ln is Y, La, Nd, Sm, Eu, Gd, D
An oxide high-temperature superconductor characterized in that the Ln sites and Ba sites of (representing y, Ho, Er, Tm, Yb or Lu) are partially replaced with Ca.
Ｂａ＿２＿−＿α＿ｘＣｕ＿３Ｏ＿ｙ（式中、０＜Ｘ＜
０．２、０．０５＜α＜０．２０である） で示される請求項（１）記載の酸化物高温超電導体。(2) Ln_1_−_xCa_(_1_+_α_)_x
Ba_2_−_α_xCu_3O_y (where 0<X<
0.2, 0.05<α<0.20) The oxide high temperature superconductor according to claim 1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63180900A JPH0230618A (en) | 1988-07-20 | 1988-07-20 | Oxide high-temperature superconductor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63180900A JPH0230618A (en) | 1988-07-20 | 1988-07-20 | Oxide high-temperature superconductor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0230618A true JPH0230618A (en) | 1990-02-01 |
Family
ID=16091274
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63180900A Pending JPH0230618A (en) | 1988-07-20 | 1988-07-20 | Oxide high-temperature superconductor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0230618A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003095652A (en) * | 2001-09-20 | 2003-04-03 | Internatl Superconductivity Technology Center | Ca-substituted rare earth 123 superconductor |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS642217A (en) * | 1987-06-25 | 1989-01-06 | Mitsubishi Metal Corp | Manufacture of superconductive ceramic wire material |
| JPH01102975A (en) * | 1987-10-16 | 1989-04-20 | Sumitomo Cement Co Ltd | Manufacture of superconducting ceramic |
| JPH01141867A (en) * | 1987-11-26 | 1989-06-02 | Mitsubishi Metal Corp | Production of target material for forming superconducting film having no residual strain |
| JPH01257159A (en) * | 1988-04-04 | 1989-10-13 | Mitsubishi Kasei Corp | oxide superconducting material |
-
1988
- 1988-07-20 JP JP63180900A patent/JPH0230618A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS642217A (en) * | 1987-06-25 | 1989-01-06 | Mitsubishi Metal Corp | Manufacture of superconductive ceramic wire material |
| JPH01102975A (en) * | 1987-10-16 | 1989-04-20 | Sumitomo Cement Co Ltd | Manufacture of superconducting ceramic |
| JPH01141867A (en) * | 1987-11-26 | 1989-06-02 | Mitsubishi Metal Corp | Production of target material for forming superconducting film having no residual strain |
| JPH01257159A (en) * | 1988-04-04 | 1989-10-13 | Mitsubishi Kasei Corp | oxide superconducting material |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003095652A (en) * | 2001-09-20 | 2003-04-03 | Internatl Superconductivity Technology Center | Ca-substituted rare earth 123 superconductor |
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