Oxide superconducting material and process for producing the same

Abstract: A RE-Ba-Cu-O type oxide superconducting material (RE represents Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or a combination of two or more of them) having a phase structure comprises a REBa₂Cu₃O Y phase and a RE₂BaCuO₅ phase of 2⊘ µm or less in diameter, dispersed in the REBa₂Cu₃O y phase, in which superconducting material RE consists of at least two elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu. Said oxide superconducting material can be produced by melt processing.

Description: The present invention relates to an oxide superconducting material and a process for producing said superconducting material. More particularly, the present invention relates to a REBa₂Cu₃O y oxide superconducting material (RE represents Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or a combination of two or more of them), in which superconducting material RE consists of at least two elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu. It is desirable to achieve a high critical current density (Jc) even in a high magnetic field. We also provide a production process for such superconducting material by subjecting raw material powders containing the at least two RE elements, to melting, slow cooling and heat treatment in this order under particular conditions. Oxide superconducting materials have high critical temperatures and vigorous research is under way in order to put them into practical use. For example, Japanese Patent Application Laid-Open No. 291814/1988 proposes, as an oxide superconducting material, a superconducting composition containing rare earth elements (Y and Ce). In obtaining an oxide superconducting material as a bulk material, sintering has heretofore been used generally. The oxide superconducting materials obtained by sintering have such a microstructure as the grains are fine and a number of grain boundaries exist inside. In these oxide superconducting bulk materials obtained by sintering, the superconducting grains are combined with each other by a weak-link, making it impossible to obtain a high Jc. Meanwhile, in superconducting materials of single crystal structure, it is known that no grain boundary problems as mentioned above exist and that a high Jc is obtained even in a high magnetic field. Hence, it was investigated to allow the superconducting material of microstructure obtained by sintering to approximate a single crystal structure. Furthermore it was proposed to disperse particles of non-superconducting phase in a single crystal phase to fix the magnetic flux line coming into, that is, to form pinning centers. For example, melting processes represented by the MTG process (the Melt Textured Growth process) were proposed. In the MTG process, a rare earth oxide superconducting material, for example, is slowly cooled generally from the incongruent melting point of 123 phase [REBa₂Cu₃O y (RE is a rare earth element including Y)] to give rise to a peritectic reaction between 211 phase (RE₂BaCuO₅) and liquid phase to cause crystal growth; the 211 phase exists inside the crystals because of incomplete peritectic reaction after growth and acts as pinning centers; as a result, the rare earth oxide superconducting material obtained shows a high Jc even in a magnetic field. The oxide superconducting material obtained by the MTG process, however, has various disadvantages in that the particles of the 211 phase are large and their distribution is non-uniform and that cracks exist along the direction of crystal growth. Also, the QMG process (the Quench and Melt Growth process) was proposed in Japanese Patent Application Laid-Open No. 1538⊘3/199⊘, as an improved process for the MTG process. In the QMG process, raw materials for rare earth oxide superconducting material are subjected to melting, quenching and solidification to obtain an intermediate comprising a Ba-Cu oxide phase and an Y₂O₃ phase or the like of 5⊘ µm or less dispersed in said oxide phase, or Y₂O₃ and a Ba-Cu oxide are mixed to obtain a plate-like material of 5 mm or less in thickness or a linear material; the intermediate or the plate-like or linear material is heated at the incongruent melting point of 123 phase to convert to a semi-molten state and then is cooled slowly from that temperature at a given cooling rate to give rise to a peritectic reaction between the 211 phase and the liquid phase to grow a 123 phase in which a 211 phase of 2⊘ µm or less is finely and uniformly dispersed. According to the disclosure in the above document, the superconducting material obtained by the QMG process exhibits a very high pinning effect and gives an excellent Jc in a highly magnetic field. Further, the MPMG process (the Melt Powder and Melt Growth process) was proposed. In the MPMG process, a material obtained by melting, quenching and solidification according to the QMG process is ground for higher shapability and the obtained superconducting material is said to give the same high Jc as in the QMG process. The QMG process and the MPMG process, as compared with the melting process, can exhibit a high pinning effect and give an excellent Jc, but require molding into a particular shape or two-stage melting (i.e. melting - quenching and solidification - semi-melting - slow cooling), making the procedure complex. Further, when the QMG process and the MPMG process are conducted via a step of quenching and solidification to prevent the agglomeration of Y₂BaCuO₅ phase to obtain a finely dispersed structure, a platinum crucible is requisite but the platinum may react with the rare earth oxide superconducting material and may cause deterioration of or variation in superconductivity of the material; moreover, a means for enabling the high-rate quenching is required. Therefore, a process is desired which can produce industrially in a simple procedure an oxide superconducting material exhibiting the same properties as those obtained in the QMG process or the MPMG process. The general problems addressed herein are to provide novel superconducting materials and processes for making them. In particular it would be preferably to provide an oxide superconducting material which exhibits a very high pinning effect and gives an excellent Jc in a highly magnetic field similarly to those obtained by the QMG process or the MPMG process. It would also be preferable to provide a process for producing the above oxide superconducting material giving an excellent Jc, by utilizing the simple procedure employed in melt processing. According to the present invention, there is provided a RE-Ba-Cu-O type oxide superconducting material (RE represents Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or a combination of two or more of them) having a phase structure comprising a REBa₂Cu₃O y phase and a RE₂BaCuO₅ phase of 2⊘ µm or less in diameter, dispersed in the REBa₂Cu₃O y phase, in which superconducting material RE consists of at least two elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu. According to the present invention, there is further provided a process for producing a RE-Ba-Cu-O type oxide superconducting material (RE represents Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or a combination of two or more of them) having a phase structure comprising a REBa₂Cu₃O y phase and a RE₂BaCuO₅ phase of 2⊘ µm or less in diameter, dispersed in the REBa₂Cu₃O y phase, in which superconducting material RE consists of at least two elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, which process comprises (a) shaping raw material powders containing RE (RE consists of at least two elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu), Ba and Cu, (b) heat-treating the shaped material at a temperature equal to or higher than the incongruent melting point of the oxide superconducting material to be finally obtained, and (c) subjecting the resulting material to slow cooling and heat treatment in this order, to obtain a REBa₂Cu₃O y oxide superconducting material. The RE-Ba-Cu-O type oxide superconducting material (RE represents Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu or a combination of two or more of them) of the present invention contains at least two rare earth elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu; comprises a REBa₂Cu₃O y phase and a RE₂BaCuO₅ phase of 2⊘ µm or less in diameter uniformly dispersed in the REBa₂Cu₃O y phase; accordingly, is uniform as a whole and gives excellent superconductivity and a high Jc. The process for producing such an oxide superconducting material according to the present invention employs one-stage melting similarly to the conventional melt processing. In this way, we have been able to make material having the same excellent superconductivity as exhibited by the oxide superconducting materials obtained by the QMG process or the MPMG process. DETAILED DESCRIPTION The present concepts are now discussed in more detail. The RE-Ba-Cu-O type oxide superconducting material of the present invention has a multi-layered perovskite structure containing at least two rare earth elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu. Said oxide superconducting material takes (1) a form represented by, for example, (YDy)₁Ba₂Cu₃O₇, wherein the RE of RE-Ba-Cu-O consists of two rare earth elements, i.e. a major RE component and a minor RE component, and/or (2) a form of a mixture consisting of (a) an oxide superconducting material containing at least one of the RE elements, having an ordinary multi-layered perovskite structure and (b) at least one of or one of others than the RE elements contained in the material (a) (the exact structure of said mixture is not known yet). In the present invention, RE includes Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu but excludes Sc, La and Pr because these three rare earth elements cannot exhibit the effects aimed at by the present invention. In the present invention, the RE-Ba-Cu-O type oxide superconducting material includes the above two forms having the RE₂BaCuO₅ phase. The raw material powders containing RE, Ba and Cu elements, used for obtaining the RE-Ba-Cu-O type oxide superconducting material have no particular restriction as long as they are a mixed oxide powder of oxides of at least two rare earth elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, a carbonate, oxide or peroxide of Ba and an oxide of Cu, a calcined powder obtained from said mixed oxide powder, a frit powder obtained from said mixed oxide powder, or the like, in which powder the individual raw materials are contained so as to constitute, after firing, REBa₂Cu₃O y and RE₂BaCuO₅. The particle diameters of the raw material powders have no particular restriction, either, but are generally 2⊘ µm or less, preferably as fine as 1-5 µm. The use of raw material powders having particle diameters of more than 2⊘ µm is not preferable because they give a non-uniform composition at the incongruent melting point of the desired oxide superconducting material. When raw material powders are used having particle diameters of 1 µm or less, powders obtained by, for example, coprecipitation are preferred; however, powders obtained by other methods can also be used as long as they are fine powders of 1 µm or less. In the present invention, the raw material powders are compounded so as to contain, as RE, at least two elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu. In this case, it is generally preferable that the at least two elements consist of a major RE component (e.g. Y or Er) and a minor RE component consisting of at least one other rare earth element (e.g. Ce, Nd, Sm, Eu). The minor RE component is particularly preferably Ce. The content of oxide of the minor RE component is generally ⊘.1-1⊘% by weight, preferably ⊘.5-5% by weight in the obtained final oxide superconducting material. When the content is within the range, agglomeration of RE₂BaCuO₅ in the oxide superconducting material obtained is suppressed, however, when the content is outside the range, the suppression of RE₂BaCuO₅ agglomeration is not much expected. The suppression of RE₂BaCuO₅ agglomeration by the minor RE component in the oxide superconducting material of the present invention comprising a REBa₂O₃O y phase and a RE₂BaCuO₅ phase of 2⊘ µm or less in diameter uniformly dispersed in the REBa₂O₃O y phase, has been found for the first time by the present inventors. The reason why the minor RE component suppresses the agglomeration of RE₂BaCuO₅ phase is not clear. However, the elemental analysis of the present oxide superconducting material by electron beam microanalyzer (EPMA) indicates that the at least two RE elements do not exist in the form of a complete solid solution and the minor RE component exists in the form of partial replacement of the major RE component and/or in the form of a compound containing substantially no major RE component. This compound containing the minor RE component is believed to have close connection with suppression of the agglomeration of RE₂BaCuO₅ phase. The raw material powders as mentioned above are thoroughly mixed; the resulting mixed powder is shaped into a desired shape; the shaped material is heated to a temperature equal to or higher than the incongruent melting point of the oxide superconducting material to be obtained finally; the resulting material is cooled slowly as in the known melt processing and then subjected to a heat treatment in an oxygen atmosphere to obtain a rare earth oxide superconducting material of the present invention. The shaping can be conducted according to a known method such as the doctor blade method, the press molding method, the slurry casting method or the like, to obtain a shaped material as a bulk material of rare earth oxide superconducting material. It is also possible to obtain a shaped material by spray- or powder-coating the above-mentioned mixed powder on a substrate made of a metal, a ceramic or the like to form a layer of rare earth oxide superconducting material on the substrate. The temperature equal to or higher than the incongruent melting point of desired REBa₂Cu₃O y , used in the present invention varies depending upon the kinds and combination of the RE elements used but is generally 1,⊘5⊘-1,2⊘⊘°C. The temperature can be appropriately selected for the material, etc. The elevation rate to said temperature is not particularly restricted. An ordinary elevation rate of about 1⊘-3⊘⊘°C/hr can be employed. The heat treatment is conducted by keeping the shaped material within the above temperature range for a given length of time. The length of time is not particularly restricted and, similarly to the above temperature range, can be appropriately selected depending upon the heating conditions, etc. But, it is generally 1⊘ minutes to 3 hours. The material is cooled slowly after the above heat treatment as in ordinary melt processing and then subjected to a heat treatment in an oxygen atmosphere at a given temperature to obtain a REBa₂Cu₃O y oxide superconducting material. In this case, the slow cooling can be conducted at a certain cooling rate or lower so as to assure crystal growth, but is ordinarily conducted preferably at a rate of ⊘.5-5°C/hr. The heat treatment after slow cooling can be conducted at a temperature of 5⊘⊘°C or below for a time as long as possible in an oxygen atmosphere in order to obtain an oxide superconducting crystal phase containing a desired amount of oxygen, but is ordinarily conducted at 3⊘⊘-5⊘⊘°C for about 1⊘-1⊘⊘ hours. As described above, the REBa₂Cu₃O y oxide superconducting material of the present invention contains at least two rare earth elements selected from Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, and max be obtained by substantially the same melting as employed in conventional melt processing, slow cooling and heat treatment. In the conventional QMG process, when the raw material powders are not subjected to melting and quenching, a RE₂BaCuO₅ phase is formed at the incongruent melting point of desired oxide superconducting material; the phase causes easy agglomeration and develops into large particles while the incongruent melting, point is kept; consequently, no oxide superconducting material giving a high Jc can be obtained. In contrast, in oxide superconducting materials as described herein, agglomeration of RE₂BaCuO₅ phase can be suppressed and the RE₂BaCuO₅ phase is finely dispersed as mentioned above by allowing the oxide superconducting material to contain at least two rare earth elements; as a result, the oxide superconducting material can give a high Jc. EXAMPLES Embodiments of the invention are described in detail by way of Examples. Example 1 and Comparative Example 1 Powders of Y₂O₃, BaCO₃ and CuO were compounded so that the atomic ratio of Y, Ba and Cu became 1.5⊘ : 2.25 : 3.25, and mixed by a dry mixer for 1 hour. The resulting mixed powder was calcined at 7⊘⊘°C for 1⊘ hours in air. To the calcined product was added a rare earth element oxide powder or other element powder each shown in Table 1, 2, 3 or 4 (Tables 1-3 are for Example 1 and Table 4 is for Comparative Example 1), in such an amount that the content of said element oxide in sintered material obtained became as shown in said Table. They were ground and mixed for 15 hours by a dry mixer using zirconia flint pebbles. The resulting mixed powder was press-molded at a pressure of 1 ton/cm² into pellets of 2⊘ mm in thickness and 3⊘ mm in diameter. The pellets were placed on a dense alumina setter in an electric furnace and subjected to temperature elevation to 1,15⊘°C in 1⊘ hours in a nitrogen atmosphere. After the temperature elevation, dry air was introduced into the electric furnace and incongruent melting was effected at 1,15⊘°C for 1 hour in an air atmosphere. Then, the temperature was lowered to 1,⊘5⊘°C in 1 hour, after which slow cooling was effected from 1,⊘5⊘°C to 9⊘⊘°C at a rate of 1°C/hr. Thereafter, oxygen was introduced into the furnace to convert the atmosphere inside the furnace to a 1⊘⊘% oxygen atmosphere, and the temperature was lowered to 5⊘⊘°C at a rate of 2⊘°/hr. The pellets were subjected to a heat treatment for 3⊘ hours at this temperature (5⊘⊘°C) and then allowed to stand in the furnace until the temperature decreased to 1⊘⊘°C or below, to obtain various sintered materials of pellet form. The cross-section of each sintered material of pellet form was polished and observed under an optical microscope to examine the dispersion state of RE₂BaCuO₅ phase. The average particle diameter and maximum particle diameter of RE₂BaCuO₅ phase were determined by image analysis and the results are shown in Table 1, 2, 3 or 4. A cubic sample of 3 mm x 3 mm x 3 mm was cut out from each sintered material and measured for hysteresis of magnetization at 77K using a magnetometer. From the measurement was calculated a Jc (A/cm²) at a magnetic field of 1T. The calculation results are shown in Table 1, 2, 3 or 4. As is clear from the above Example, an oxide superconducting material containing a dispersed RE₂BaCuO₅ phase of 2⊘ µm or less in maximum diameter and giving a high Jc of 6,⊘⊘⊘ A/cm² or more can be obtained by allowing said superconducting material to contain, in addition to a major RE component (Y in the Example), a minor RE component in an amount of ⊘.1-1⊘% by weight as oxide. When the minor RE component is Ce, in particular, the dispersed RE₂BaCuO₅ phase has a maximum particle diameter of 12 µm or less and there is obtained a preferable Jc of 12,⊘⊘⊘ A/cm² or more. When there is contained, as the minor RE component, Sm, Ho or Lu in an amount of 2-1⊘% by weight as oxide, or Tm, Nd or Tb in an amount of 2% by weight as oxide, or Dy or Yb in an amount of 1⊘% by weight as oxide, there is obtained a Jc of 1⊘,⊘⊘⊘ A/cm² or more. Meanwhile, in the Comparative Example (Run Nos. 1-6⊘ and 1-61) wherein the minor RE component is Ce but is contained in an amount of ⊘.⊘4 or 2⊘% by weight as oxide, the obtained Jc is as low as 4,⊘⊘⊘ A/cm² or less. Also when no minor RE component is added or a non-RE element (Ag) powder is added, the obtained Jc is as low as 3,5⊘⊘ A/cm² or less. Also when La or Pr is added as the main RE component, the obtained Jc is as low as 3,⊘⊘⊘ A/cm² or less. Example 2 and Comparative Examples 2 and 3 Powders of BaCO₃ and CuO were compounded so that the atomic ratio of Ba and Cu became 2.25 : 3.25, and mixed by a dry mixer for 1 hour. The resulting mixed powder was calcined in air at 85⊘°C for 1⊘ hours. To the calcined product were added powders of Y₂O₃ and CeO₂ so that the atomic ratio of Y : Ce : Ba : Cu became 1.5 : ⊘.⊘9 : 2.25 : 3.25. They were ground and mixed for 15 hours by a dry mixer using zirconia flint pebbles. In this case, the CeO₂ content in the product was 2% by weight. In Comparative Example 2, the same procedure as above was employed except that no CeO₂ powder was added. In Comparative Example 3, in accordance with the conventional QMG process disclosed in Japanese Patent Application Laid-Open No. 1538⊘3/199⊘, powders of Y₂O₃, CeO₂, BaCO₃ and CuO were compounded so that the atomic ratio of Y : Ce : Ba : Cu became 1.5 : ⊘.⊘9 : 2.25 : 3.25, and mixed by a dry mixer for 1 hour; the resulting mixed powder was placed in a platinum crucible and melted in air at 1,4⊘⊘°C for 3 minutes; the melt was cast between a stainless-steel twin-roller for quenching and solidification; the resulting solid was ground and mixed in ethyl alcohol for 15 hours by a wet mixer using zirconia flint pebbles. The same procedure was repeated for a case using no CeO₂ powder. Each of the above obtained mixed powders was subjected to molding, incongruent melting, slow cooling and heat treatment in the manner similar to Example 1, to obtain sintered materials (Example 2: Run No. 2-1, Comparative Example 2: Run No. 2-2, Comparative Example 3: Run Nos. 2-3 and 2-4). Each sintered material was subjected to surface observation and measurement of hysteresis of magnetization, and a Jc was calculated. The results are shown in Table 5. Run No. Ce addition Average particle diameter (µm) Maximum particle diameter (µm) Jc (A/cm²) Example 2 2-1 Presence 4 10 14000 Comparative 2 2-2 Absence 10 30 3000 Comparative 3 2-3 Presence 3 10 14000 2-4 Absence 3 10 15000 When raw material powders are not subjected to melting and quenching, the resulting sintered material containing Ce (Run No. 2-1) embodying the present invention shows a high Jc, while the sintered material containing no Ce (Run No. 2-2) according to Comparative Example 2 shows a low Jc of 3,⊘⊘⊘ A/cm². In contrast, when raw material powders are subjected to melting and quenching in accordance with the conventional QMG process, a high Jc of 14,⊘⊘⊘ A/cm² or more is obtained regardless of addition or no addition of Ce. Therefore, it is obvious that the use of minor RE component in addition to major RE component is very effective in the present melting process for producing an oxide superconducting material. Example 3 and Comparative Example 4 A calcined powder was obtained in the same manner as in Example 1 except that raw material powders of Er₂O₃, BaO₂ and CuO were compounded so that the atomic ratio of Er, Ba and Cu became 1.5⊘ : 2.25 : 3.25. To the powder was added CeO₂ so that the CeO₂ content in sintered material obtained became as shown in Table 6, and the same procedure as in Example 1 was repeated to obtain sintered materials (Example 3: Run Nos. 3-1 to 3-6, Comparative Example 4: Run No. 3-7). In the same manner as in Example 1, each sintered material was subjected to surface observation, measurement of hysteresis of magnetization and calculation of Jc. The results are shown in Table 6. Run No. CeO₂ content (Wt.%) Average particle diameter (µm) Maximum particle diameter (µm) Jc (A/cm²) Example 3 3-1 0.1 5 15 10000 3-2 0.5 3 10 13000 3-3 1 4 12 12000 3-4 2 4 12 13000 3-5 5 4 12 12000 3-6 10 5 15 10000 Comparative 4 3-7 0 10 30 2500 Example 4 A calcined powder was obtained in the same manner as in Example 1 except that raw material powders of Y₂O₃, BaO and CuO were compounded so that the atomic ratio of Y, Ba and Cu became 1.4⊘ : 2.25 : 3.25. To the calcined powder was added an Ag powder so that the Ag content in fired product became 1% by weight in form of element. There was further added CeO₂ so that the CeO₂ content in fired product became as shown in Table 7. Then, the same procedure as in Example 1 was repeated to obtain sintered materials. In the same manner as in Example 1, each sintered material was subjected to surface observation, measurement of hysteresis of magnetization and calculation of Jc. The results are shown in Table 7.

Claims: A process for producing a RE-Ba-Cu-O type oxide superconducting material (RE being selected from the elements Y, Ce, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu) having a phase structure comprising a fine particulate RE₂BaCuO₅ phase, of 20µm or less in diameter, dispersed in a REBa₂Cu₃O y phase; in which the RE component consists of at least two of said elements, and the process comprises (a) shaping raw material powders containing the RE components, Ba and Cu, (b) heat-treating the shaped material at a temperature equal to or higher than the incongruent melting point of the oxide superconducting material to be obtained, and (c) subjecting the resulting material to (i) slow cooling at a rate of from 0.5 to 5 C°/hr, and then (ii) heat treatment in an oxygen atmosphere at from 300 to 500°C for from 10 to 100 hours. A process according to claim 1, in which one of the at least two RE elements is a major RE component and the remaining RE element(s) is (are) a minor RE component. A process according to claim 1 or claim 2 in which the minor RE component is contained in an amount of from 0.1 to 10wt%, as oxide, in the oxide superconducting material. A process according to any one of claims 1 to 3 in which the minor RE component is Ce. A process according to any one of claims 1 to 4 in which the heat treatment after shaping is conducted at a temperature of from 1050 to 1200°C. An oxide superconducting material of the RE-Ba-Cu-O type comprising (a) a matrix of REBa₂Cu₃O y phase with, uniformly dispersed in the matrix, fine particles of RE₂BaCuO₅ phase of diameter up to 20µm (RE being selected from the group Y, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb and Lu), and (b) cerium, in a quantity corresponding to 0.1 to 10wt% cerium (IV) oxide in the oxide superconducting material. An oxide superconducting material according to claim 6 in which RE is only one element selected from said group.

Inventors: BABA HIDEYUKI MARUMISHATO TAKA, SAKAI HITOSHI, YOSHIDA HITOSHI, YOSHIDA MANABU -, BABA, HIDEYUKI, MARUMISHATO TAKATSUJI, SAKAI, HITOSHI, YOSHIDA, HITOSHI, YOSHIDA, MANABU,, YOSHIDA, MANABU, 61-3 AZA-YADAI
Applicants: NGK INSULATORS LTD, NGK INSULATORS, LTD.
Application year: 1992
Main classification: C04B35
IPC codes: H01B13, C04B35, C01G1, H01B12, H01L39, C01G3