JPH07282650A - Compound superconductor - Google Patents
Compound superconductorInfo
- Publication number
- JPH07282650A JPH07282650A JP6087673A JP8767394A JPH07282650A JP H07282650 A JPH07282650 A JP H07282650A JP 6087673 A JP6087673 A JP 6087673A JP 8767394 A JP8767394 A JP 8767394A JP H07282650 A JPH07282650 A JP H07282650A
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- Prior art keywords
- compound
- heat treatment
- conductor
- diameter
- fiber
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Classifications
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- 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
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- Superconductors And Manufacturing Methods Therefor (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明はＮｂ3 Ｓｎ系の化合物超
電導導体に関し、特に、導体の加工性を低下させずに連
続繊維の極細化が図れるようにして、臨界電流特性の向
上と履歴損失特性の低減を図った化合物超電導導体に関
する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a Nb 3 Sn-based compound superconducting conductor, and more particularly, to improving the critical current characteristics and the history loss by making it possible to make the continuous fiber extremely fine without deteriorating the workability of the conductor. The present invention relates to a compound superconducting conductor with reduced characteristics.
【０００２】[0002]
【従来の技術】従来の化合物超電導導体として、例え
ば、Ｃｕ−Ｓｎ合金を用いてブロンズ法によって形成さ
れたＮｂ3 Ｓｎ超電導導体がある。2. Description of the Related Art As a conventional compound superconducting conductor, for example, there is an Nb 3 Sn superconducting conductor formed by a bronze method using a Cu--Sn alloy.
【０００３】この種の化合物超電導導体は、Ｓｎを含有
したマトリックス中に多数本のＮｂの連続繊維を埋設
し、これに所定の加工（例えば、熱処理）を施してＮｂ
3 Ｓｎ化合物層を形成して構成されている。In this type of compound superconducting conductor, a large number of continuous fibers of Nb are embedded in a matrix containing Sn, and a predetermined process (for example, heat treatment) is performed on the continuous fiber to make Nb.
3 Sn compound layer is formed.
【０００４】また、化合物超電導導体の製造では、一般
に、Ｃｕ−Ｓｎ合金マトリックスが冷間による減面加工
で著しく硬化し、導体の加工が困難になることから、工
程中にＣｕ−Ｓｎ合金マトリックスの加工性を回復させ
るための中間熱処理として、６００℃以上の焼鈍を冷間
加工中に多数回施している。In the production of compound superconducting conductors, generally, the Cu-Sn alloy matrix is significantly hardened by cold surface-reduction processing, which makes it difficult to process the conductor. As an intermediate heat treatment for recovering workability, annealing at 600 ° C. or higher is performed many times during cold working.
【０００５】[0005]
【発明が解決しようとする課題】しかし、従来の化合物
超電導導体によると、上述したＣｕ−Ｓｎ合金マトリッ
クスの中間熱処理によってＣｕ−Ｓｎ合金マトリックス
とＮｂ連続繊維の界面に微量のＮｂ3 Ｓｎ系化合物が生
成される。このＮｂ3 Ｓｎ系化合物はＮｂ連続繊維の径
が大きいものでは全く導体の加工性を阻害する要因とは
ならないが、Ｎｂ連続繊維の径がミクロンオーダーにな
ると、Ｎｂ連続繊維にネッキングや破断が発生し、断線
回数の増大等から加工性を低下させると共に臨界電流特
性を低下させるという不都合をもたらす。このため、Ｎ
ｂ連続繊維の径をＮｂ3 Ｓｎ系化合物を生成する最終熱
処理前において３μｍ以下にすることができなかった。However, according to the conventional compound superconducting conductor, a trace amount of Nb 3 Sn compound is present at the interface between the Cu-Sn alloy matrix and the Nb continuous fiber by the intermediate heat treatment of the Cu-Sn alloy matrix. Is generated. This Nb 3 Sn-based compound does not become a factor that hinders the processability of the conductor when the diameter of the Nb continuous fiber is large, but when the diameter of the Nb continuous fiber becomes in the order of micron, necking or breakage occurs in the Nb continuous fiber. However, there is an inconvenience that the workability is deteriorated due to an increase in the number of wire breakages and the critical current characteristics are deteriorated. Therefore, N
The diameter of the b-continuous fiber could not be reduced to 3 μm or less before the final heat treatment for producing the Nb 3 Sn-based compound.
【０００６】従って、本発明の目的は導体の加工性を低
下させずに連続繊維の極細化が図れ、臨界電流特性の向
上と履歴損失特性の低減を図ることができる化合物超電
導導体を提供することである。Therefore, an object of the present invention is to provide a compound superconducting conductor which can make the continuous fibers ultrafine without deteriorating the processability of the conductor and can improve the critical current characteristics and the hysteresis loss characteristics. Is.
【０００７】[0007]
【課題を解決するための手段】本発明は上記問題点に鑑
み、導体の加工性を低下させずに連続繊維の極細化が図
れ、臨界電流特性の向上と履歴損失特性の低減を図るた
め、連続繊維をＮｂの外周にＴａ，或いはＴａ−Ｎｂ合
金を被覆した複合繊維より構成した化合物超電導導体を
提供するものである。In view of the above-mentioned problems, the present invention is capable of achieving ultrafine continuous fibers without deteriorating the workability of the conductor, improving the critical current characteristics and reducing the hysteresis loss characteristics. The present invention provides a compound superconducting conductor comprising continuous fibers composed of composite fibers in which the outer circumference of Nb is coated with Ta or Ta-Nb alloy.
【０００８】上記複合繊維は、ＴａのとＮｂのモル数の
比が０．０３：１以下になっていることが好ましい。ま
た、Ｎｂの外周に被覆されるＴａ−Ｎｂ合金としては、
Ｔａが５０％以上の組成になっていることが必要であ
る。すなわち、Ｔａがこれ以下であると、中間熱処理に
おける化合物生成を防止できなくなるためである。The composite fiber preferably has a molar ratio of Ta to Nb of 0.03: 1 or less. Further, as the Ta-Nb alloy coated on the outer periphery of Nb,
It is necessary that Ta has a composition of 50% or more. That is, if Ta is less than this, compound formation in the intermediate heat treatment cannot be prevented.
【０００９】また、Ｎｂの外周に被覆可能な材料として
は、本発明のＴａの他にＮｂの固溶限が大きく、且つ、
マトリックス中のＣｕ，Ｓｎと中間熱処理条件で金属間
化合物を生成しないＨｆ，Ｖ，或いはこれらの元素とＴ
ａの少なくとも１種以上が添加されたＮｂ合金が適用可
能である。Further, as a material capable of coating the outer periphery of Nb, in addition to Ta of the present invention, the solid solution limit of Nb is large, and
Cu and Sn in the matrix and Hf and V that do not form an intermetallic compound under the intermediate heat treatment conditions, or these elements and T
An Nb alloy to which at least one of a is added can be applied.
【００１０】更に、Ｓｎを含んだマトリックスは、Ｃｕ
−Ｓｎ系合金より構成され、Ｃｕ−Ｓｎ系合金はＳｎの
他にＴｉ，Ｎｉ，Ｇａ，Ｓｉ，Ａｌ，Ｚｎ，Ｔａ，Ｂの
少なくとも１種を合計で５ａｔ％以下含んでも良い。Further, the matrix containing Sn is Cu
The Cu-Sn alloy may include at least one of Ti, Ni, Ga, Si, Al, Zn, Ta, and B in addition to Sn in a total amount of 5 at% or less.
【００１１】[0011]
【実施例】以下、本発明の化合物超電導導体について添
付図面を参照しながら詳細に説明する。The compound superconducting conductor of the present invention will be described in detail below with reference to the accompanying drawings.
【００１２】図１には、本発明の化合物超電導導体の最
終熱処理前の断面構造が示されている。この化合物超電
導導体は、複数本（本実施例では、３６１本）集合され
た断面六角形のサブエレメント線１と、サブエレメント
線１の外周に形成されたＴａの拡散バリヤ２と、更に、
その外周に形成されたＣｕの安定化材３より構成されて
いる。FIG. 1 shows a sectional structure of the compound superconducting conductor of the present invention before the final heat treatment. This compound superconducting conductor is composed of a plurality of (361 in this embodiment) sub-element wires 1 having a hexagonal cross section, a Ta diffusion barrier 2 formed on the outer periphery of the sub-element wire 1, and further,
It is composed of a Cu stabilizing material 3 formed on the outer periphery thereof.
【００１３】図２には、上記サブエレメント線１を製造
するための単心線用押出ビレットの断面構造が示されて
いる。すなわち、この押出ビレットは、Ｎｂ丸棒７の外
周にＴａシート６を被覆し、更にその外周にＣｕ−Ｓｎ
合金管５を配置して構成されている。このように構成さ
れた単心線用押出ビレットは、静水圧押出し，冷間引抜
き，及び中間熱処理を繰り返し行って六角断面の単心線
とし、これを定寸に切断した後、これを８５本集合させ
てサブエレメント用押出ビレット（図示せず）を組立て
て、単心線と同様に静水圧押出した後，冷間引抜き，及
び中間熱処理を繰り返して行ってサブエレメント線１と
なる。FIG. 2 shows a sectional structure of an extrusion billet for a single core wire for manufacturing the sub-element wire 1. That is, in this extruded billet, the outer periphery of the Nb round bar 7 is covered with the Ta sheet 6, and further the outer periphery thereof is Cu-Sn.
The alloy pipe 5 is arranged and configured. The extruded billet for single-core wire configured in this way is subjected to hydrostatic extrusion, cold drawing, and intermediate heat treatment repeatedly to form a single-core wire with a hexagonal cross section, which is cut to size, and then 85 After being assembled, an extruding billet for sub-elements (not shown) is assembled and hydrostatically extruded in the same manner as the single core wire, and then cold drawing and intermediate heat treatment are repeated to form the sub-element wire 1.
【００１４】以下、本発明の実施例を詳細に説明する。
まず、上記構成を有する実施例１の化合物超電導導体
と、Ｎｂの外周にＴａが被覆されていない比較例の化合
物超電導導体を表１の条件に基づいて作成した。すなわ
ち、マトリックスの組成がＣｕ−８．３ａｔ％Ｓｎ−
０．４ａｔ％Ｔｉの三元合金，マトリックスと連続繊維
の体積比が２．０：１，安定化銅と非安定化銅の体積比
が１．６：１，導体径が０．８ｍｍ，最終熱処理前の連
続繊維径が約１．５μｍのものを作成した。The embodiments of the present invention will be described in detail below.
First, the compound superconducting conductor of Example 1 having the above structure and the compound superconducting conductor of Comparative Example in which the outer periphery of Nb was not coated with Ta were prepared based on the conditions of Table 1. That is, the composition of the matrix is Cu-8.3 at% Sn-
0.4 at% Ti ternary alloy, volume ratio of matrix to continuous fiber is 2.0: 1, volume ratio of stabilized copper to non-stabilized copper is 1.6: 1, conductor diameter is 0.8 mm, final The continuous fiber diameter before heat treatment was about 1.5 μm.
【表１】 [Table 1]
【００１５】これは、まず、実施例の単心線用押出ビレ
ットを、直径１９．９ｍｍの工業用純Ｎｂ丸棒を厚さ
０．０５ｍｍ，幅６５ｍｍのＴａシートで包み、これら
を内径２０．１ｍｍ，外径２８．４ｍｍの表１に示した
組成のＣｕ−Ｓｎ−Ｔｉ合金管に挿入して、また、比較
例の単心線用押出ビレットを、直径２０ｍｍのＮｂ丸棒
を実施例と同一寸法のＣｕ−Ｓｎ−Ｔｉ合金管に挿入し
てそれぞれ製造する。First, an extruded billet for a single core wire of the example is wrapped with a Ta sheet having a diameter of 19.9 mm and a pure Nb rod for industrial use with a thickness of 0.05 mm and a width of 65 mm. The extruded billet for a single core wire of Comparative Example was inserted into a Cu-Sn-Ti alloy tube having a composition shown in Table 1 having an outer diameter of 1 mm and an outer diameter of 28.4 mm. They are manufactured by inserting them into Cu-Sn-Ti alloy tubes having the same dimensions.
【００１６】そして、これらの押出ビレットを４００℃
で加熱した後、直径１２ｍｍに静水圧押出し、それらに
減面率３５〜４０％の冷間引抜きと６００℃×３０ｍｉ
ｎの中間熱処理を繰り返し行って、それぞれ対辺長２．
３ｍｍの正六角断面の単心線とする。次に、これらの単
心線を定尺切断した後、これを８５本集合させた状態で
内径２４ｍｍ，外径２８．７ｍｍの表１に示す組成のＣ
ｕ−Ｓｎ−Ｔｉ合金管にそれぞれ挿入してサブエレメン
ト用押出ビレットとし、これらの押出ビレットを４００
℃で加熱後、直径１２ｍｍに静水圧押出し、それらに減
面率３５〜４０％の冷間引抜きと６００℃×３０ｍｉｎ
の中間熱処理を繰り返し行って、それぞれ対辺長０．８
０５ｍｍのサブエレメント線とした。Then, these extruded billets were heated to 400 ° C.
After being heated at 80 ° C., it is hydrostatically extruded to have a diameter of 12 mm, subjected to cold drawing with a surface reduction rate of 35 to 40%, and 600 ° C. × 30 mi.
n intermediate heat treatment is repeated to obtain opposite side lengths of 2.
A single core wire with a regular hexagonal cross section of 3 mm is used. Next, after cutting these single-filamentary wires to a fixed length, in the state where 85 of them were assembled, the C of the composition shown in Table 1 having an inner diameter of 24 mm and an outer diameter of 28.7 mm was obtained.
The extruded billets for sub-elements were inserted into the u-Sn-Ti alloy tubes, and these extruded billets were 400
After heating at ℃, it is hydrostatically extruded to a diameter of 12 mm, and cold drawing with a surface reduction rate of 35 to 40% and 600 ℃ × 30 min.
Repeated the intermediate heat treatment of, opposite side length 0.8
It was a sub-element line of 05 mm.
【００１７】この後、これらのサブエレメント線を定尺
に切断した後、これを３６１本集合させた状態で内径１
７ｍｍ，外径１８ｍｍのＴａ管（拡散バリヤ）に挿入
し、その外側に内径１８．２ｍｍ，外径２８．３ｍｍの
安定化銅管に配置してビレットとした。After that, after cutting these sub-element wires to a fixed length, 361 pieces of these sub-element wires are gathered to form an inner diameter of 1
It was inserted into a Ta tube (diffusion barrier) having a diameter of 7 mm and an outer diameter of 18 mm, and a billet was formed by arranging a stabilized copper tube having an inner diameter of 18.2 mm and an outer diameter of 28.3 mm on the outside thereof.
【００１８】最後に、このようにして製造されたビレッ
トを４００℃で加熱後、直径１２ｍｍに押出し、単心線
やサブエレメント線と同様な条件で冷間引抜きと中間熱
処理を繰り返し行い、外径０．８ｍｍの導体に加工し
た。Finally, the billet produced in this manner is heated at 400 ° C. and extruded to a diameter of 12 mm, and cold drawing and intermediate heat treatment are repeated under the same conditions as for the single core wire and the sub-element wire to obtain the outer diameter. It was processed into a 0.8 mm conductor.
【００１９】次に、これらの実施例１と比較例の化合物
超電導導体で形成された導体に対して６５０℃×２００
ｈｒで化合物生成熱処理を施した後、両者の臨界電流特
性を比較した。図３は、その考察結果を示すもので、実
施例１の化合物超電導導体は外部磁場１２Ｔにおいて１
５５Ａと良好な特性を示しているのに対し、比較例の化
合物超電導導体は７７Ａと大幅に低下している。この場
合の臨界電流の定義は導体の非銅部断面積基準で１０
-13 Ω・ｍである（以下の実施例も同定義）。Next, the conductors formed of the compound superconducting conductors of Example 1 and Comparative Example are 650 ° C. × 200.
After performing the compound formation heat treatment at hr, the critical current characteristics of both were compared. FIG. 3 shows the result of the consideration, and the compound superconducting conductor of Example 1 has an external magnetic field of 12T.
The compound superconducting conductor of the comparative example shows a significant decrease of 77 A while the excellent characteristic of 55 A is exhibited. The definition of the critical current in this case is 10 based on the cross-sectional area of the non-copper part of the conductor.
-13 Ω · m (same definition in the following examples).
【００２０】次に、表１の実施例１の導体で導体径を変
えた場合、すなわち、連続繊維の径を変えた例について
説明する。表２に、そのときの実施例２から実施例５の
導体径，Ｔａ／Ｎｂ複合連続繊維径，及び最終の化合物
生成熱処理によって得られた外部磁場１２Ｔにおける非
銅部の臨界電流特性を示す。Next, a case where the conductor diameter of the conductor of Example 1 in Table 1 is changed, that is, the diameter of the continuous fiber is changed will be described. Table 2 shows the conductor diameter, the Ta / Nb composite continuous fiber diameter, and the critical current characteristics of the non-copper portion in the external magnetic field 12T obtained by the final compound formation heat treatment in Examples 2 to 5 at that time.
【表２】 [Table 2]
【００２１】これから判るように、複合連続繊維の径が
３μｍを越えると、最終熱処理において複合連続繊維中
のＴａ層が化合物生成を阻害するために化合物生成が進
行しなくなって臨界電流が低下するが、３μｍ以下では
Ｔａ層の厚さが充分に薄くなるためにマトリックス中の
Ｓｎ，Ｔｉが容易にＴａ層を透過でき、且つ、最終熱処
理中にＴａ自体がＮｂ中に拡散して複合連続繊維がＮｂ
−Ｔａ合金化するために化合物生成が阻害されなくな
り、臨界電流が高くなる。As can be seen from the above, when the diameter of the composite continuous fiber exceeds 3 μm, the Ta layer in the composite continuous fiber inhibits the compound formation in the final heat treatment, so that the compound formation does not proceed and the critical current decreases. If the thickness is 3 μm or less, the thickness of the Ta layer becomes sufficiently thin so that Sn and Ti in the matrix can easily pass through the Ta layer, and Ta itself diffuses into Nb during the final heat treatment to form a continuous composite fiber. Nb
The compound formation is not hindered by the Ta-alloying, and the critical current increases.
【００２２】次に、表１の実施例１の単心線用押出ビレ
ットで複合連続繊維のＴａシートの被覆率を変えた実施
例について説明する。表３に、そのときの実施例６から
実施例９のＴａシートの厚さ，幅，Ｎｂ丸棒の径，及び
Ｔａ被覆率と、導体としたときの導体径，繊維径，及び
最終熱処理によって得られた外部磁場１２Ｔにおける非
銅部の臨界電流特性を示す。Next, an example in which the coverage of the Ta sheet of the composite continuous fiber is changed with the single-strand wire extrusion billet of Example 1 in Table 1 will be described. Table 3 shows the thickness, width, Nb round bar diameter, and Ta coverage of the Ta sheet of Example 6 to Example 9 at that time, the conductor diameter when the conductor was used, the fiber diameter, and the final heat treatment. The critical current characteristic of the non-copper part in the obtained external magnetic field 12T is shown.
【表３】 [Table 3]
【００２３】これから判るように、複合連続繊維中のＴ
ａシートの被覆率が約４％以上になると、臨界電流が大
幅に低下するのに対し、３％の被覆率では充分に高い特
性が得られている。これらの導体は連続繊維の最終熱処
理によってほぼ完全にＮｂ−Ｔａ合金されており、複合
連続繊維中のＴａシートの被覆率が３％の実施例８のＴ
ａとＮｂのモル比は約０．０３：１となる。As can be seen, the T in the composite continuous fiber
When the coverage of the a-sheet is about 4% or more, the critical current is significantly reduced, whereas at the coverage of 3%, sufficiently high characteristics are obtained. These conductors were almost completely Nb-Ta alloyed by the final heat treatment of the continuous fiber, and the T sheet of Example 8 in which the coverage of the Ta sheet in the composite continuous fiber was 3%.
The molar ratio of a to Nb is about 0.03: 1.
【００２４】[0024]
【発明の効果】以上説明したように、本発明の化合物超
電導導体によると、臨界電流特性の向上と履歴損失特性
の低減を図るため、連続繊維をＮｂの外周にＴａ，或い
はＴａ−Ｎｂ合金を被覆した複合繊維より構成したた
め、導体の加工性を低下させずに連続繊維の極細化が図
ることができ、これにより臨界電流特性の向上と履歴損
失特性の低減を図ることができる。As described above, according to the compound superconducting conductor of the present invention, in order to improve the critical current characteristics and reduce the hysteresis loss characteristics, continuous fibers are provided with Ta or Ta-Nb alloy on the outer periphery of Nb. Since it is composed of the coated composite fiber, it is possible to make the continuous fiber extremely fine without deteriorating the workability of the conductor, thereby improving the critical current characteristic and reducing the hysteresis loss characteristic.
【図１】本発明の一実施例を示す断面図。FIG. 1 is a sectional view showing an embodiment of the present invention.
【図２】本発明の一実施例を示す断面図。FIG. 2 is a sectional view showing an embodiment of the present invention.
【図３】一実施例における臨界電流特性を示すグラフ。FIG. 3 is a graph showing a critical current characteristic in one example.
１ サブエレメント線 ２ 拡散
バリヤ ３ 安定化材 ５ Ｃｕ
−Ｓｎ合金管 ６ Ｔａシート ７ Ｎｂ
丸棒1 Sub-element line 2 Diffusion barrier 3 Stabilizer 5 Cu
-Sn alloy tube 6 Ta sheet 7 Nb
Round bar
Claims (3)
含有した多数本の連続繊維を埋設し、熱処理等を施して
Ｎｂ3 Ｓｎ系化合物層を形成してなる化合物超電導導体
において、 前記連続繊維は、Ｎｂの外周にＴａ，或いはＴａ−Ｎｂ
合金を被覆した複合繊維より構成されていることを特徴
とする化合物超電導導体。1. A compound superconducting conductor obtained by embedding a large number of continuous fibers containing Nb in a matrix containing Sn and performing a heat treatment or the like to form an Nb 3 Sn compound layer. , Nb on the outer periphery of Ta, or Ta-Nb
A compound superconducting conductor comprising a composite fiber coated with an alloy.
の比が０．０３：１以下になっている構成の請求項１の
化合物超電導導体。2. The compound superconducting conductor according to claim 1, wherein the composite fiber has a molar ratio of Ta to Nb of 0.03: 1 or less.
物を生成する最終熱処理前の径が３μｍ以下になってい
る構成の請求項１の化合物超電導導体。3. The compound superconducting conductor according to claim 1, wherein the composite fiber has a diameter of 3 μm or less before the final heat treatment for producing the Nb 3 Sn-based compound.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6087673A JPH07282650A (en) | 1994-04-01 | 1994-04-01 | Compound superconductor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6087673A JPH07282650A (en) | 1994-04-01 | 1994-04-01 | Compound superconductor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07282650A true JPH07282650A (en) | 1995-10-27 |
Family
ID=13921471
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6087673A Pending JPH07282650A (en) | 1994-04-01 | 1994-04-01 | Compound superconductor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07282650A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013251180A (en) * | 2012-06-01 | 2013-12-12 | Sh Copper Products Corp | Precursor wiring material of triniobium-tin superconducting multi-core wiring material, and triniobium-tin superconducting multi-core wiring material arranged using the same |
-
1994
- 1994-04-01 JP JP6087673A patent/JPH07282650A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013251180A (en) * | 2012-06-01 | 2013-12-12 | Sh Copper Products Corp | Precursor wiring material of triniobium-tin superconducting multi-core wiring material, and triniobium-tin superconducting multi-core wiring material arranged using the same |
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