JPH02129023A - Oxide superconducting material - Google Patents
Oxide superconducting materialInfo
- Publication number
- JPH02129023A JPH02129023A JP63282919A JP28291988A JPH02129023A JP H02129023 A JPH02129023 A JP H02129023A JP 63282919 A JP63282919 A JP 63282919A JP 28291988 A JP28291988 A JP 28291988A JP H02129023 A JPH02129023 A JP H02129023A
- Authority
- JP
- Japan
- Prior art keywords
- phase
- superconducting
- transition temperature
- composition
- temperature
- 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
- 239000000463 material Substances 0.000 title abstract description 11
- 229910052712 strontium Inorganic materials 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 229910052745 lead Inorganic materials 0.000 claims abstract description 4
- 229910052769 Ytterbium Inorganic materials 0.000 claims abstract description 3
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 3
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 3
- 229910052684 Cerium Inorganic materials 0.000 claims abstract 2
- 229910052692 Dysprosium Inorganic materials 0.000 claims abstract 2
- 229910052691 Erbium Inorganic materials 0.000 claims abstract 2
- 229910052693 Europium Inorganic materials 0.000 claims abstract 2
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract 2
- 229910052689 Holmium Inorganic materials 0.000 claims abstract 2
- 229910052765 Lutetium Inorganic materials 0.000 claims abstract 2
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract 2
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract 2
- 229910052772 Samarium Inorganic materials 0.000 claims abstract 2
- 229910052771 Terbium Inorganic materials 0.000 claims abstract 2
- 229910052775 Thulium Inorganic materials 0.000 claims abstract 2
- 229910052706 scandium Inorganic materials 0.000 claims abstract 2
- 230000007704 transition Effects 0.000 abstract description 19
- 239000000203 mixture Substances 0.000 abstract description 17
- 239000000843 powder Substances 0.000 abstract description 7
- 239000002887 superconductor Substances 0.000 abstract description 7
- 231100000331 toxic Toxicity 0.000 abstract description 3
- 230000002588 toxic effect Effects 0.000 abstract description 3
- FIXNOXLJNSSSLJ-UHFFFAOYSA-N ytterbium(III) oxide Inorganic materials O=[Yb]O[Yb]=O FIXNOXLJNSSSLJ-UHFFFAOYSA-N 0.000 abstract description 2
- 229910002480 Cu-O Inorganic materials 0.000 abstract 1
- 239000011369 resultant mixture Substances 0.000 abstract 1
- LEDMRZGFZIAGGB-UHFFFAOYSA-L strontium carbonate Chemical compound [Sr+2].[O-]C([O-])=O LEDMRZGFZIAGGB-UHFFFAOYSA-L 0.000 abstract 1
- 229910000018 strontium carbonate Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 5
- 239000000919 ceramic Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000010304 firing Methods 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 239000002612 dispersion medium Substances 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000012212 insulator Substances 0.000 description 1
- 238000005339 levitation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000000126 substance Substances 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
Description
【発明の詳細な説明】
産業上の利用分野
本発明は、高い超伝導転移温度を持つ酸化物超伝導材料
に関するものである。DETAILED DESCRIPTION OF THE INVENTION Field of the Invention The present invention relates to oxide superconducting materials with high superconducting transition temperatures.
従来の技術
超伝導材料は、１）電気抵抗がゼロである、２）完全反
磁性である、 ３）ジ１セフソン効果がある、といった
、他の材料にない特性を持っており、電力輸送、発電器
、核融合プラズマ閉じ込め、磁気浮上列車、磁気シール
ド、高速コンピュータ等の幅広い応用が期待されている
。ところが、従来の金属系超伝導体では、超伝導転移温
度は最も高いものでも２３に程度であり、実使用時には
高価な液体ヘリウムと大がかりな断熱装置を使って冷却
しなければならず、工業上大きな問題であった。Conventional technology Superconducting materials have properties not found in other materials, such as 1) zero electrical resistance, 2) complete diamagnetism, and 3) di1-Sefson effect, and are useful for power transport, It is expected to have a wide range of applications, including power generators, fusion plasma confinement, magnetic levitation trains, magnetic shields, and high-speed computers. However, with conventional metallic superconductors, the highest superconducting transition temperature is around 23°C, and in actual use, they must be cooled using expensive liquid helium and large-scale insulation equipment, making it difficult for industrial use. It was a big problem.
このため、より高温で超伝導体となる材料の探索が行わ
れていた。For this reason, research has been underway to find materials that become superconductors at higher temperatures.
１９８６年にベト°ノルフ（Ｂｅｄｎｏｒｚ）とミュー
５−（Ｍｕｌｌｅｒ）により約４０にという高い超伝導
転移温度をもつ、酸化物系超伝導材料（Ｌａ＋−ｚＳ
ｒｚ）ｐｃｕＯＸが見いだされ、それ以後Ｙ Ｂ ａ
２ Ｃｕ ａ Ｏｘ＊ Ｂ１−５ｒ−Ｃａ−Ｃｕ−０
，Ｔｌ−Ｂａ−Ｃａ−Ｃｕ−０などで、あいついでより
高い温度での超伝導転移が報告されている。超伝導転移
温度が高いほど、冷却が容易となり、また同じ温度で使
用した場合の臨界電流密度や臨界磁場も太き（なる事が
予想され、応用範囲も広がるものと期待される。このた
め現在、これらの材料の製造法、物性、応用等に関して
多くの研究がなされている。In 1986, Bednorz and Muller developed an oxide-based superconducting material (La+-zS) with a high superconducting transition temperature of about 40.
rz) pcuOX was discovered, and since then Y B a
2 Cu a Ox* B1-5r-Ca-Cu-0
, Tl-Ba-Ca-Cu-0, and the like, superconducting transitions at higher temperatures have been reported. The higher the superconducting transition temperature, the easier the cooling becomes, and the critical current density and critical magnetic field are also expected to become thicker when used at the same temperature, and the range of applications is expected to expand.For this reason, the current Many studies have been conducted on the manufacturing methods, physical properties, applications, etc. of these materials.
発明が解決しようとする課題
ところが上記の材料のうち、（Ｌ ａｔ−ｚｓ ｒｚ）
ａｃＵＯＸは超伝導転移温度が４０に以下と比較的低く
、Ｙ Ｂ ａ ２Ｃｕ ｓ ０１１は焼成時に雰囲気を
制御する必要があり、Ｂ１−５ｒ−Ｃａ−Ｃｕ−０は単
一相とするのが困難な上に、長時間の焼成が必要であり
、Ｔｌ−Ｂａ−Ｃａ−Ｃｕ−０はＴＩの毒性が強い上に
、Ｔｌの蒸発のために組成を一定に保つ事が難しいとい
う問題点があった。また、何れの組成でも、セラミック
スとした場合に焼結体の密度が低かった。Problem to be solved by the invention However, among the above materials, (L at-zs rz)
acUOX has a relatively low superconducting transition temperature of 40 or less, YBa 2Cu s 011 requires atmosphere control during firing, and B1-5r-Ca-Cu-0 is difficult to form into a single phase. Moreover, it requires long firing time, and Tl-Ba-Ca-Cu-0 has the problem that TI is highly toxic and it is difficult to keep the composition constant due to evaporation of Tl. Ta. In addition, regardless of the composition, the density of the sintered body was low when it was made of ceramic.
課題を解決する為の手段
少なくともＬｎ （ＬｎはＹ、 Ｌａ、 Ｃｅｔ
Ｐｒ＋ＮｃＬ Ｓｍ＋ Ｅｕ＋ ＧｃＬ Ｔ
ｂ＋ Ｄｙ＋ Ｈｏｔ Ｅｒ＋ Ｔｍ＋ Ｙ
ｂ＋ Ｌｕ＋ Ｓｃより選択された、１種類以上の
元素）ｔ Ｐｂ＋ ＳｒおよびＣｕを含む組成とす
る。Means to solve the problem At least Ln (Ln is Y, La, Cet
Pr+NcL Sm+ Eu+ GcL T
b+ Dy+ Hot Er+ Tm+ Y
The composition contains one or more elements selected from b+ Lu+ Sc)t Pb+ Sr and Cu.
作用
発明者等は、従来知られていない酸化物高温超伝導体の
組成比を探索・研究した結果、上記の組成からなる物質
において、比較的高い温度における超伝導転移を見いだ
した。As a result of exploring and researching the composition ratio of oxide high temperature superconductors, which was hitherto unknown, the inventors discovered superconducting transition at relatively high temperatures in a substance having the above composition.
本発明の組成では、ＴＩ等の毒性の高い成分を含まず、
また空気中での短時間の焼成で超伝導体を合成する事が
出来る。The composition of the present invention does not contain highly toxic components such as TI,
Moreover, superconductors can be synthesized by short-time firing in air.
実施例
出発原料として、純度９９％以上のＹｂ２Ｏ３、ＰｂＯ
９ＳｒＣＯ３、ＣｕＯの各粉末を用いた。これらの粉末
を、表１の組成比となり、かつ粉末の総重量が２０ｇと
なるようにそれぞれ秤量した。Examples Starting materials include Yb2O3 and PbO with a purity of 99% or more.
Each powder of 9SrCO3 and CuO was used. These powders were each weighed so that the composition ratios shown in Table 1 were achieved and the total weight of the powders was 20 g.
表１．配合組成比（モル比）
秤量粉末を振動ミルにて直径２ｍｍのＺｒＯ２ボールを
用い、エタノール２０ｍ１を分散媒として１時間粉砕混
合した。混合終了後、分散媒ごと全量を乾燥機中で１２
０°Ｃで乾燥させた。得られた粉末を８００℃で５時間
、空気中で仮焼した後、振動ミルにて前述と同様の方法
で３０分間粉砕し、１２０℃で乾認させた。得られた粉
末の０．６ｇを１８ｍｍＸ４ｍｍの金型中で８００Ｋｇ
／ｃｍ２の圧力で一軸加圧成形した。この成形体を、電
気炉にて空気中で９５０℃で５時間焼成し、冷却した。Table 1. Composition Ratio (Mole Ratio) The weighed powders were pulverized and mixed in a vibration mill for 1 hour using a ZrO2 ball with a diameter of 2 mm and 20 ml of ethanol as a dispersion medium. After mixing, the entire amount including the dispersion medium was placed in a dryer for 12 hours.
Dry at 0°C. The obtained powder was calcined in air at 800°C for 5 hours, then ground in a vibration mill for 30 minutes in the same manner as described above, and dried at 120°C. 0.6g of the obtained powder was transferred to 800Kg in a 18mm x 4mm mold.
Uniaxial pressure molding was carried out at a pressure of /cm2. This molded body was fired in air at 950° C. for 5 hours in an electric furnace, and then cooled.
焼結体は銀電極を付け、通常の４端子法により電気抵抗
の温度変化を測定電流１０ｍＡで３００Ｋから ４．２
Ｋまで測定し、超伝導転移により電気抵抗が急激に低下
し始める温度（ＴＩ）と、抵抗がＯとなる温度（Ｔｌ）
を求めた。また、焼結体の帯磁率の温度変化を測定し、
マイスナー効果により帯磁率が急激に変化し始める温度
（Ｔ３）を求めた。結果を表２に示した。A silver electrode was attached to the sintered body, and the temperature change in electrical resistance was measured using the usual 4-terminal method from 300 K at a current of 10 mA. 4.2
Measured up to K, the temperature at which the electrical resistance begins to rapidly decrease due to superconducting transition (TI) and the temperature at which the resistance becomes O (Tl)
I asked for In addition, we measured the temperature change in the magnetic susceptibility of the sintered body,
The temperature (T3) at which the magnetic susceptibility begins to change rapidly due to the Meissner effect was determined. The results are shown in Table 2.
表２．焼結体の特性（単位Ｋ）
ＴＩ：電気抵抗低下開始温度（Ｔｃ ｏｎｓｅｔ）Ｔｌ
：電気抵抗消失温度 （Ｔｃ Ｒ＝０）Ｔ３：マイス
ナー効果開始温度
表２より明らかなように、Ｐｂを含まないＮｏ、１の試
料では、３００にではある程度導電性があるが温度を下
げていくにしたがって、電気抵抗は半導体的に増加し、
４．２にでは絶縁体となった。Table 2. Characteristics of sintered body (unit: K) TI: Temperature at which electrical resistance begins to decrease (Tconset) Tl
: Electrical resistance vanishing temperature (Tc R=0) T3: Meissner effect starting temperature As is clear from Table 2, samples No. 1, which do not contain Pb, have some conductivity at 300, but the temperature is lowered. Accordingly, the electrical resistance increases in a semiconducting manner,
4.2, it became an insulator.
これに対し、Ｐｂを含むＮｏ、２． Ｎｏ、３の試料で
は、３００−１００に間ではやはり電気抵抗が若干増加
する傾向にあるが、Ｎｏ、２で５９に１ Ｎｏ、３で５
６により電気抵抗は減少に転じ、それぞれ９にと６にで
電気抵抗が実質状消失した。また、マイスナー効果によ
る帯磁率の変化もそれぞれ１２にと１０にで観察された
。従って、Ｙｂ、Ｐｂ＋Ｓｒ、Ｃｕを含む本発明の酸化
物はオンセット温度約Ｅ３０にの超伝導体である。On the other hand, No. 2 containing Pb. In the sample No. 3, the electrical resistance tends to increase slightly between 300 and 100, but it is 59 for No. 2 and 5 for No. 3.
6, the electrical resistance started to decrease, and the electrical resistance substantially disappeared at 9 and 6, respectively. In addition, changes in magnetic susceptibility due to the Meissner effect were also observed in samples 12 and 10, respectively. Therefore, the oxides of the present invention containing Yb, Pb+Sr, Cu are superconductors with an onset temperature of about E30.
発明者等は、本実施例の組成比以外にも、種々の組成比
のセラミックスを作製し、その電気抵抗の温度変化を測
定した。その結果、組成比の選択によって超伝導相の生
成量や転移温度には差があるが、広い組成範囲で超伝導
転移の存在を確認した。In addition to the composition ratio of this example, the inventors produced ceramics with various composition ratios, and measured changes in electrical resistance with temperature. As a result, although the amount of superconducting phase produced and the transition temperature differ depending on the selection of the composition ratio, we confirmed the existence of superconducting transition over a wide composition range.
次に、生成した超伝導相の結晶構造について少し説明す
る。Ｎｏ 、２の試料をＸ線回折測定にかけると、観察
される回折ピークは、Ｓ ｒ Ｐ ｂ Ｏａ 相と未知
相によるものである。５ｒＰｂＯｓ相は超伝導相ではな
いので、未知相が超伝導相と考えられる。この未知相に
よると考えられる回折ピークは、ａ軸長約３．８１Ａ、
ａ軸長約１１．８Ａをとる正方品の回折パターンとして
説明されうる。この格子定数は、一般に１２３構造と呼
ばれる、９０に程度の超伝導転移温度をもつ、ペロブス
カイト相ＹｂＢａ２Ｃｕ３０．より、ａ軸が少し短い（
ＹｂＢａ２Ｃｕ３０ｘ相はａ軸が約３．８３Ａ、ｂ軸が
約ｓ、ｅＡｔｃ軸が約１１．７Ａの斜方晶であるが、酸
素欠損の増加により超伝導とならない正方品となると、
ａ軸長約３．８８ＡＸ ａ軸長約１１．７５Ａ）が、よ
く似た値となっている。Next, we will briefly explain the crystal structure of the superconducting phase produced. When the sample No. 2 is subjected to X-ray diffraction measurement, the observed diffraction peaks are due to the S r P b Oa phase and the unknown phase. Since the 5rPbOs phase is not a superconducting phase, the unknown phase is considered to be a superconducting phase. The diffraction peak thought to be due to this unknown phase has an a-axis length of about 3.81A,
It can be described as a diffraction pattern of a square piece with an a-axis length of about 11.8A. This lattice constant is a perovskite phase YbBa2Cu30.0 with a superconducting transition temperature of the order of 90°C, commonly referred to as the 123 structure. , the a-axis is a little shorter (
The YbBa2Cu30x phase is an orthorhombic crystal with an a-axis of about 3.83 A, a b-axis of about s, and an eAtc axis of about 11.7 A, but when it becomes a tetragonal product that does not become superconducting due to an increase in oxygen vacancies,
The a-axis length is approximately 3.88AX and the a-axis length is approximately 11.75A), which are very similar values.
Ｙ ｂ Ｂ ａ ２ Ｃｕ ３０ ＊のペロブスカイト
相は、ＢａがＳｒで６０％程度まで置換可能である。こ
の置換を行うと、Ｓｒのイオン半径がＢａのそれより小
さいために、ａ、 ｂ軸とも小さくなる。一方、Ｂａ
を含まず、ＳｒとＣｕを含む超伝導酸化物として、Ｂ１
−５ｒ−Ｃａ−Ｃｕ−０系が知られている。この化合物
は若干式なる結晶構造をもつが、ＹｂＢａ２Ｃｕ ３０
ｘ相のａｓ ｂ軸に相当する軸の長さは約３．８２
Ａであり、本発明のものに近い値をとる。In the perovskite phase of Y b B a 2 Cu 30 *, Ba can be replaced by Sr up to about 60%. When this substitution is performed, since the ionic radius of Sr is smaller than that of Ba, both the a and b axes become smaller. On the other hand, Ba
As a superconducting oxide containing Sr and Cu, B1
-5r-Ca-Cu-0 system is known. This compound has a crystal structure of the following formula, YbBa2Cu 30
The length of the axis corresponding to the as b axis of the x phase is approximately 3.82
A, which takes a value close to that of the present invention.
以上の事実より、本発明の超伝導相の格子定数は、Ｙ
ｂ Ｂ ａ ２Ｃｕ ｓ Ｏｘ相のＢａサイトがＳｒで
１ｏｏＶｏ置換された時に期待される値を持つ。しかし
ながら、ＹｂＢａ２ＣｕａＯｘ相のＢａサイトを単純に
Ｓｒで１００％置換する事は不可能であり、１００％置
換組成比で配合して焼成すると、ちとのペロブスカイト
相は消失し、超伝導転移も示さなくなる。この事は、Ｎ
ｏ、１の試料の結果からも明らかである。ところが、こ
のＮ００１の組成にＰｂを加えていく事により、Ｂａが
０となっても、１２３＋Ｍ造のペロブスカイト相が生成
するものと考えられる。従って、本発明の超伝導相は、
ＹｂＢａ２Ｃｕ３０ｘ相のＢａサイトがＳｒとＰｂで置
換されたものと考えられる。From the above facts, the lattice constant of the superconducting phase of the present invention is Y
b It has the expected value when the Ba site of the B a 2Cu s Ox phase is replaced with 1ooVo of Sr. However, it is impossible to simply replace 100% of the Ba sites of the YbBa2CuaOx phase with Sr, and when the composition is blended with 100% substitution and fired, the original perovskite phase disappears and no superconducting transition is exhibited. This matter is N
This is also clear from the results of samples o and 1. However, it is thought that by adding Pb to the composition of N001, a 123+M perovskite phase is generated even if Ba becomes 0. Therefore, the superconducting phase of the present invention is
It is considered that the Ba site of the YbBa2Cu30x phase was replaced with Sr and Pb.
発明の効果
本発明・によれば、Ｌｎ−Ｐｂ−８ｒ−Ｃｕ−０系組成
の酸化物超伝導体とすることにより、得られたセラミッ
クスの転移温度は（Ｌ ａｓ−ｘｓ ｒｘ）２ｃＵＯＺ
相を越え、また、焼結体は緻密である。Effects of the Invention According to the present invention, by using an oxide superconductor having an Ln-Pb-8r-Cu-0 composition, the transition temperature of the obtained ceramic is (Las-xs rx)2cUOZ
Beyond the phase, the sintered body is also dense.
Claims (1)
，Ｓｍ，Ｅｕ，Ｇｄ，Ｔｂ，Ｄｙ，Ｈｏ，Ｅｒ，Ｔｍ，
Ｙｂ，Ｌｕ，Ｓｃより選択された、１種類以上の元素）
，Ｐｂ，Ｓｒ，およびＣｕを含む組成を有することを特
徴とする、酸化物超伝導材料。At least Ln (Ln is Y, La, Ce, Pr, Nd
, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm,
one or more elements selected from Yb, Lu, Sc)
, Pb, Sr, and Cu.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63282919A JPH02129023A (en) | 1988-11-09 | 1988-11-09 | Oxide superconducting material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63282919A JPH02129023A (en) | 1988-11-09 | 1988-11-09 | Oxide superconducting material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02129023A true JPH02129023A (en) | 1990-05-17 |
Family
ID=17658811
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63282919A Pending JPH02129023A (en) | 1988-11-09 | 1988-11-09 | Oxide superconducting material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02129023A (en) |
-
1988
- 1988-11-09 JP JP63282919A patent/JPH02129023A/en active Pending
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