Method for preparing oxide superconductors

Abstract: There is provided a method for stably preparing rare earth (RE) 123 type oxide superconductors exhibiting outstanding superconductive properties in the atmosphere. In the method for preparing RE 123-type oxide superconductors by melting, cooling and solidifying a starting composition containing one or more than two kinds of RE such as Y, Sm, Nd, etc., and Ba, Cu and O as constituent elements to crystallize the RE 123-type oxide superconductors, quantity of replacement between RE and Ba in "RE 123 crystals to be formed" is controlled by changing initial constitution of the starting composition (for example, by changing the initial constitution to a more Ba-rich side than a composition on a 123-211 (or 422) tie line on a phase diagram to yield RE 123-type oxide superconductors in the atmosphere, which exhibit critical temperature of 90 K or above and higher critical current density (Jc) in a magnetic field. A trace amount of Pt or CeO 3 may be added to micronize the 211 (or 422) phase so as to further improve Jc.

Description: The present invention relates to a method for preparing rare earth (hereinafter referred to as RE) 123-type oxide superconductors including Y 123 oxide superconductors which exhibit higher critical temperature of 90 K or above and have excellent superconductive properties in the atmosphere. Since oxide superconductors exhibiting critical temperature more than liquid nitrogen temperature (77.3 K) were recently found, superconductor applying technology has been receiving wider appreciation thereby accelerating competitive development of materials which exhibit stable superconductivity at higher temperature. Especially, in the case of a Y-Ba-Cu-O oxide superconductor as a 123-type oxide in which mole ratio of Y:Ba:Cu in the material is 1:2:3, higher critical current density (Jc) has been successfully achieved by improving a process for preparing such a superconductor, while the material has been used as current lead wires as a matter of course and further tried extensively to apply to magnet, etc. by taking advantage of superconductive properties which can generate large electromagnetic force due to an interaction thereof with magnetic field. In addition to the above mentioned Y 123-type oxide superconductor, superior superconductive properties are successively confirmed in other RE 123-type oxides in which Y (yttrium) as a component thereof is replaced by various rare earth elements other than Y and are also widely studied to develop possible devices and instruments by applying these properties. A "flux process", "melt-solidifying process" and the like are mainly used as a method to prepare RE 123-type oxide superconductors including the Y 123-type (hereinafter Y is included in the expression of rare earth elements of RE). According to the "flux process" as a method for preparing oxide superconductors, temperature of a relatively homogeneous supersaturated solution (molten liquid) of a starting composition (flux) comprising an oxide mixture of components to be required is gradually lowered to crystallize oxide superconductive crystals from the solution cooled below solubility limit. On the other hand, according to the "melt-solidifying process", a starting composition (flux) is heated beyond peritectic temperature of an intended oxide to form a mixed state of solid and liquid phases, the temperature of which is then slowly lowered from the thus heated condition to cause a peritectic reaction so as to form oxide superconductive crystals. In these processes, initial constitution of the starting composition is adjusted to reside on a "123-211 (or 422) tie line" of a ternary phase diagram as will be described later (see Fig. 1) while considering to keep sufficient but not excessive mass balance to yield a superconductive phase (123 phase) and to cause micro-dispersion of the 211 phase (in cases of Y, Sm, etc.) or the 422 phase (in cases of Nd, La, etc.) which functions as a magnetic flux pinning center in the superconductive phase to increase the critical current density (Jc), or considering to keep the mass balance to minimize a residue of unreacted Cu, Ba, etc. It should be understood that the above mentioned "tie line" means a line on the phase diagram which shows a relationship between a crystalline phase composition and a liquid phase composition in the range where crystalline and liquid phases are equilibrated. It is pointed out, however, that the thus prepared 123-type oxide superconductors, i.e., the RE 123-type other than Y exhibit neither sufficient critical temperature (Tc) nor higher critical current density (Jc) in a magnetic field, although only Y 123-type has relatively preferable superconductive properties. As the reason why, it is considered that an ionic radius of rare earth elements (RE) except Y is relatively large and comparable to that of Ba, which causes a mutual replacement of RE and Ba when a molten raw material is cooled and solidified to form a superconductive phase, so that a chemical composition of the thus formed oxide crystals deviates from that of the 123 phase to be yielded. Fig. 1 shows a "ternary phase diagram of 1/2RE 2 O 3 -BaO-CuO" in the atmosphere of oxides including RE such as La, Nd, Sm, Pm, Eu, Gd, etc. having relatively larger ionic radius. "A solid solution region of certain width" exists along a line extending right upward from the RE 123 phase, as shown in Fig. 1. The solid solution region exists to stabilize a phase of RE1+x Ba 2 -x Cu 3 O y (x>0, 6.0<y<7.2) which deviates from the RE 123 phase in the atmosphere. As is clear from existence of the solid solution region, a mutual replacement of RE and Ba occurs in oxides of RE having relatively larger ionic radius when the superconductive phase is solidified in the air atmosphere. As shown in Fig. 2. superconductive properties of the RE 123-type oxide superconductors change depending on quantity of replacement (x) between RE and Ba. Accordingly, critical temperature thereof is lowered considerably as the quantity of replacement x increases and, on the contrary, is raised as the quantity of replacement x decreases, i.e., as the composition comes close to that of the RE 123-type oxide. As is described above, it is considered that the mutual replacement of RE and Ba at a stage to form the superconductive phase by cooling and solidifying the starting material from a molten state thereof (a nucleating and growing stage) is a major cause for hindering an attainment of higher critical temperature. Then, there has been proposed an "Oxygen Controlled Melt Growth" process (hereinafter referred to as OCMG process) in which a starting composition is molten and solidified to promote crystal growth not in the atmosphere but in an atmosphere where a content of oxygen in the atmosphere is controlled to a lower level. It is known that RE 123 type oxide superconductors of Sm, Nd, etc. prepared by the OCMG process exhibit higher critical temperature (Tc) and higher critical current density (Jc) in a high magnetic field compared with the Y 123-type oxide superconductor of similar crystal structure because of a phenomenon in which replacement of RE to a Ba site is controlled in an atmosphere of low oxygen partial pressure. A process of this kind is disclosed e.g. in EP 0 660 423 A2. In the OCMG process, however, it is quite disadvantageous from a standpoint of production that crystal growth should be performed in a controlled atmosphere of lower oxygen, although the RE 123-type oxide superconductors of higher critical temperature and higher critical current density in a magnetic field can be obtained because RE 123 crystals containing less quantity of replaced Ba are easily formed. On the other hand, in the above described other process in which the starting composition is molten, cooled and solidified to form 123-type oxide superconductive crystals, the initial constitution thereof is adjusted to richen the 211 (or 422)-phase on the 123-211 (or 422) tie line so that grains of the 211 phase (or grains of the 422 phase) are dispersed in the 123 phase, thereby functioning as a magnetic flux pinning center to improve the critical current density (Jc). The magnetic flux pinning center should be fine to the utmost. In this case, a trace amount of Pt or CeO 2 is generally added to the starting composition to micronize grains of the 211 phase (or grains of the 422 phase) formed in the 123 superconductive phase. However, even when the dispersed phase is micronized by a trace addition of Pt or CeO 2 , grains of the 211 phase (or grains of 422 phase) formed in the RE 123 phase are micronized at most to an extent of micron order in the RE 123-type oxide superconductors except Y, which causes a problem, although grains of the 211 phase formed in the Y 123 phase are micronized to an extent of submicron order to exhibit preferable critical current density in the Y 123-type oxide superconductor. After all, in order to impart "higher critical current density in a lower magnetic field" of a level of the Y 123-type oxide superconductor to the RE 123-type oxide superconductors except Y, it is considered that grains of the RE 211 phase (or grains of the 422 phase) formed and dispersed in the RE 123 phase should be further micronized. Accordingly, it is an object of the present invention to provide a method for preparing, stably even in the air atmosphere, RE 123-type oxide superconductors in which quantity of mutual replacement between RE and Ba is extremely reduced to exhibit critical temperature of 90 K or above and grains of a RE 211 phase (or grains of a RE 422 phase) dispersed in a RE 123 phase are further micronized to exhibit higher critical current density in a magnetic field. This object is solved according to the invention by the features of claim 1. There has been found the following fact as a result of the inventors' eager investigation to achieve the above mentioned object. (a) Superconductive properties of RE 123-type oxide superconductors are varied with the quantity of replacement between RE atoms and Ba atoms, and such superconductors exhibit higher critical temperature as a composition thereof comes closer to the 123 ratio of the RE phase. However when a starting composition is molten, cooled and solidified in the atmosphere to grow crystals of the RE 123 phase, it is difficult to control the quantity of replacement between RE atoms and Ba atoms at a lower level and it is impossible to yield higher critical temperature stably, if "initial constitution of starting composition" is adjusted to a composition given on a tie line 123-211 (or 422) from a conventional standpoint of mass balance According to a conventional way of thinking, the initial constitution of starting composition is determined by considering a mass balance so as not to leave unreacted Cu, Ba etc., because they would cause deterioration of superconductive properties. However, when the initial constitution of starting composition is changed, the unreacted Cu, Ba, etc. are not left in a superconductive phase to adversely affect the superconductive properties. This would probably be caused by a phenomenon in which excessive Cu, Ba, etc. are expelled from the crystals of the superconductive phase (crystals of RE 123 phase) around thereof and taken out of a system as the crystals grow. Furthermore, it is possible to control appropriately quantity of replacement between RE and Ba in "RE 123-type oxide crystals to be formed" by changing the initial constitution of starting composition. Applying this procedure, it is possible to extremely approximate a composition of "RE123-type oxide crystals to be formed" to that of the RE 123 phase even in the atmosphere, which allows to produce "RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above" in the air atmosphere. (b) Especially, when the initial constitution of starting composition for preparing the RE 123-type oxide superconductors is shifted to a more Ba-rich side which shows a liquid phase in equilibrium in the atmosphere with a superconductive phase having a composition approximated to the RE 123 phase, i.e., a more Ba-rich side than a composition on the 123-211 (or 422) tie line, it is possible to prepare RE 123-type oxide superconductors of extremely high critical temperature, in which quantity of replacement between RE and Ba is controlled to quite a low level even by a melt-solidifying treatment in the atmosphere. (c) Further, when the initial constitution of starting composition is changed, particularly when the constituent is shifted to a more Ba-rich side than a composition on the 123-211 (or 422) tie line, excessive growth of "grains of the RE 211 phase (or grains of the RE 422 phase) to be formed" is controlled, thereby yielding superconductors in which grains of RE 211 phase (or grains of the RE 422 phase), still finer than "those grains prepared by using conventional initial constitution on the 123-211 (or 422) tie line, are dispersed in the RE 123 phase and critical current density thereof in a magnetic field is remarkably improved. When a slight amount of Pt or CeO 2 is simultaneously used as a conventional micro-dispersing agent in the above mentioned case, a micronizing effect of grains of the RE 211 phase (or grains of the RE 422 phase) is remarkably increased to a submicron order, thereby further improving critical current density thereof in a magnetic field. The present invention is based on the above mentioned fact and provides a method for preparing RE 123-type oxide superconductors as in the following. 1. A method for preparing rare earth element (RE) 123-type oxide superconductors exhibiting critical temperature of 90 K or above in the air atmosphere by melting, cooling and solidifying a starting composition containing one or more than two kinds of RE, and Ba, Cu and O as constituent elements to crystallize the RE 123-type oxide superconductors, which comprises a step to control quantity of replacement between RE and Ba in "RE 123 crystals to be formed" by changing initial constitution of said starting composition. 2. A method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above in the air atmosphere described in the above item 1 in which quantity control of replacement between RE and Ba by changing initial constitution of starting composition is conducted by a procedure wherein a RE:Ba:Cu mole ratio of "RE 123 crystals to be formed" is approximated to 1:2:3 as close as possible by changing the initial constitution of starting composition to a more Ba-rich side than a composition on a "123-211 (or 422) tie line of a REO-BaO-CuO ternary phase diagram", so that grains of a RE 211 phase or grains of RE 422 phase dispersed in a RE 123 phase are micronized to secure high critical current density in a magnetic field. 3. A method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above in the air atmosphere described in the above item 1 or 2 in which a slight amount of Pt or CeO 2 is added to a starting composition as a micro-dispersing agent for grains of a RE 211 phase or grains of a RE 422 phase. 4. A method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above in the atmosphere described in any one of the above items 1 to 3 in which a means to melt, cool and solidify the starting composition so as to crystallize thereof is a "melt-solidifying process". 5. A method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above in the air atmosphere described in any one of the above items 1 to 4 in which RE is Sm. 6. A method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above in the atmosphere described in any one of the above items 1 to 4 in which RE is Nd. In the RE 123-type oxide superconductors of the present invention, RE may include one or more than two kinds of Sm, Nd, La, Pm, Eu, Gd, Y, etc. A "method for crystallizing RE 123-type oxide superconductors by melting, cooling and solidifying a starting composition to crystallize thereof" used in the present invention may either be a "flux process" or a "melt-solidifying process" in which a starting composition is heated to peritectic temperature or above to bring about a mixed state of solid-liquid and then cooled slowly to cause a peritectic reaction, while it is preferable to use the melt-solidifying process in which a process control is comparably easy and stable products can be obtained smoothly. It should be understood that, after the starting composition is molten, cooled and solidified to crystallize thereof according to the present invention, the thus formed oxide crystals are conventionally subjected to an annealing (heat treating) step in an oxygen atmosphere to secure desired superconductive properties. As has been described above, it is the most characteristic feature of the present invention to control a quantity of replacement between RE and Ba in "RE 123 crystals to be formed" by changing initial constitution of starting composition when the starting composition is molten, cooled and solidified to form RE 123-type oxide superconductors. In general, although constitution of a simple composition changes if proportion of each component contained therein is changed as a matter of course, it is a novel fact no one ever reported to control the quantity of replacement between RE and Ba in "RE 123 crystals to be formed" without adversely affecting superconductive properties by simply changing the initial constitution of starting composition to a slight extent. According to the above mentioned fact, it is possible to satisfactorily conduct a quantity control of mutual replacement between RE and Ba in the RE 123 phase even when RE 123-type oxide superconductors are prepared in the air atmosphere, and it is thus possible to grow RE 123-type oxide crystals which composition is approximated to that of the RE 123 phase as close as possible in the low oxygen pressure atmosphere. Superconductive properties of the RE 123-type oxide superconductors are changed by the quantity of mutual replacement between a RE atom and a Ba atom, and the closer the composition is approximated to RE 123, i.e., RE(such as Sm, Nd, Y, etc.)Ba 2 Cu 3 O 7 , the higher the critical temperature is exhibited. Accordingly, the RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above can be yielded actually when the quantity of mutual replacement between RE and Ba in the "RE 123 phase to be formed" is reduced so that a composition thereof is approximated to that of RE 123 by changing the initial constitution of the starting composition. Further, while such quantity control of mutual replacement between RE and Ba by changing the initial constitution of starting composition is sufficiently applied to the melt-solidifying process which is conducted in the atmosphere, it is possible to prepare the RE 123-type oxide superconductors exhibiting higher critical temperature quite easily at low cost. In order to reduce the quantity of mutual replacement (solid solubility) between RE and Ba in the RE 123 phase of RE 123-type oxide superconductors, it is effective to change the initial constitution of starting composition to a more Ba-rich side than a composition on the 123-211 (or 422) tie line as will be apparently described in the following embodiment. That is, the quantity of replacement between RE and Ra in the RE 123 phase is increased or decreased depending on an "extent to be changed to the Ba-rich side". On the other hand, while surface energy in the liquid phase of molten starting material is changed with a change in the initial constitution of starting composition, it is also possible to control growth of grains of the RE 211 phase (or grains of the RE 422 phase) dispersed in the RE 123 phase. For example, when the initial constitution of starting composition is changed to a more Ba-rich side on the 123-211 (or 422) tie line to reduce the quantity of replacement between RE and Ba in the "RE 123 phase to be formed", an excessive increase in grain size in the RE 211 phase or the RE 422 phase is controlled in cases where RE is Sm, etc. and Nd, etc., respectively, thereby greatly contributing to micronize grains of the RE 211 phase (or grains of RE 422 phase) dispersed in the RE 123 phase. While the thus micronized grains of the RE 211 phase (or grains of the RE 422 phase) dispersed in the RE 123 phase allow to improve critical current density in a magnetic field of the RE 123-type oxide superconductors, control of the initial constitution of starting composition causes to impart higher critical current density in a magnetic field to the superconductors. As a matter of course, a combined use of "Pt or CeO 2 addition in a trace amount" as a conventional means to micronize grains of the RE 211 phase (or grains of the RE 422 phase) tends to further promote such a micronizing effect, which preferably results in an improvement of critical current density in a magnetic field. As has been described above, the RE 123-type oxide superconductors of improved superconductive properties which exhibit critical temperature of 90 K or above and higher critical current density in a magnetic field can be stably prepared in the atmosphere by the present invention which results in extremely useful effects from a stand point of industry. Fig. 1 is a ternary phase diagram of 1/2RE 2 O 3 -BaO-CuO. Fig. 2 is a graph showing relationship between a value x of a superconductor RE 1 +x Ba 2 -x Cus O 7 -d and critical temperature. Fig. 3 is a model diagram in main part showing relationship between an initial constitution used in the present embodiment and a Sm123 composition thereof after crystal growth on a ternary phase diagram of 1/2SmO-BaO-CuO. Fig. 4 is electron micrographs showing "grains of the 211 phase dispersed in the 123 phase" of each Sm 123 superconductor specimen used for a metallographical observation. Fig. 5 is a graph showing relationship between temperature and magnetization of Sm 123 superconductor specimens which initial constitution is changed. Fig. 6 is a graph showing relationship between an impressed magnetic field and critical current density (Jc) of Sm 123 superconductor specimens which initial constitution is changed. The present invention will be described in detail together with effects thereof in the following embodiment. Using powder of respective Sm 2 O 3 , BaCO 8 , CuO and a trace amount of Pt as a starting material, Sm 123 superconductors were prepared in the atmosphere by way of trial according to a "seeding process by the use of Nd 123 seed crystal" as in the following. The starting material is sintered to form a sintered body, which is put on a magnesia single crystal plate and then heated to peritectic temperature or above with Nd 123 seed crystal placed thereon to cause a mixed state of solid and liquid phases, followed by isothermal retention thereof by subcooling from such a state so that a peritectic reaction is induced to form oxide superconductive crystals. The initial constitution of starting material was changed variously as shown in Table 1 below. type of starting material proportion of cationic Sm, Ba and Cu Pt content (wt. %) Sm Ba Cu A 0.2368 0.3158 0.4474 0.5 B 0.2348 0.3230 0.4422 0.5 C 0.2327 0.3302 0.4371 0.5 D 0.2286 0.3446 0.4268 0.5 The initial constitution mentioned in Table 1 is based on a standard composition of "Sm 123 + 0.4 Sm 211 + 0.5 wt. % Pt" (type A) on a 123-211 tie line of a ternary phase diagram of 1/2SmO-BaO-CuO (in main part) shown in Fig. 3, and that of other types (B, C and D) is slightly slid to a more Ba-rich side to keep the quantity of 123-211 constant. Specimens of each Sm 123 superconductor thus prepared were observed metallographically, while superconductive properties thereof were evaluated after subjecting a heat treatment in an oxygen flow at 340 °C for 200 hours by a conventional manner. Fig. 4 is electron micrographs showing "grains of the 211 phase dispersed in the 123 phase" of each Sm 123 superconductor specimen used for a metallographical observation, wherein symbols A to D correspond to the initial constitution mentioned in Table 1. In Fig. 4, black parts show grains of the 211 phase captured by the 123 phase and gray parts show 123 phase matrixes, from which it is possible to confirmed that a grain size grains of the 211 phase decreases as the initial constitution changes from A to D. Especially in the case of the initial constitution D, it is considered that an average grain size of grains of the 211 phase is a submicron order, i.e., these grains are micronized to an approximately similar level as a grain size of "dispersed grains of a Y 211 phase in a Y 123 phase of Y type oxide superconductors" yielded by a conventional process in which a preeminently micronized dispersing phase can be obtained. Figs. 5 and 6 are graphs showing test results related to superconductive properties of each Sm 123 superconductor specimen after the heat treatment. Fig. 5 shows relationship between critical temperature and magnetization of the Sm 123 superconductor specimens which initial constitution has been changed. It is confirmed from Fig. 5 that the critical temperature of the Sm 123 superconductor having Ba-rich initial constitution is 93 K, which is a greatly outstanding value compared with that of a "conventional specimen prepared in the atmosphere by starting from initial constitution on the 123-211 tie line". Relationship between an "extent of change in the initial constitution of starting composition" and "quantity x of replacement between Sm and Ba in a Sm 123 superconductor of Sm 1 +x Ba 2 -x Cu 3 O y to be formed" was calculated back from data showing relationship between known "quantity of replacement x and critical temperature Tc". As a result, it was found that the quantity x of replacement is 0.02 (Tc = 92 K), 0.01 (Tc = 93 K) and slightly less than 0.01 in Sm 123 superconductors prepared by using the initial constitution A, B and C, respectively. Accordingly, it was confirmed that the quantity x of replacement between Sm and Ba in "Sm 123 superconductive crystals to be formed" can be controlled by adjusting the initial constitution of starting composition. Fig. 6 shows relationship between an impressed magnetic field and critical current density (Jc) of Sm 123 superconductor specimens which initial constitution has been changed. It is apparent from Fig. 6 that the Sm 123 superconductor exhibits greatly outstanding properties at a side of lower magnetic field (in the vicinity of 1T) compared with a product prepared by the OCMG process. This would be caused by an "improvement in the critical temperature (Tc) due to control of Sm to replace to a Ba site" and an "improvement in the flux pinning effect due to micronized grains of Sm 211 phase". In general, the measurement of atomic abundance ratio by means of EPMA is used to determine the quantity x of replacement between RE and Ba in RE oxide superconductors of RE 1 +x Ba 2 -x Cu 3 O y . The atomic abundance ratio of each Sm 123 superconductor specimen formed in the present embodiment was determined by means of EPMA, and it was confirmed that the quantity x of replacement is vague even in the case of the initial constitution A wherein the value x is considered as the highest, and that the value x in the Sm 123 phase falls almost within a measurement error range. Although production of the Sm 123 superconductors has been described in the present embodiment, it was also ascertained that a similar result can be obtained in the case of Nd 123 superconductors. Further, it was confirmed that the method of the present can be effectively applied to prepare RE 123-type oxide superconductors in which RE other than Sm and Nd, such as Y, La, Pm, Bu, Gd, etc. is used. The features disclosed in the foregoing description, in the claims and/or in the accompanying drawings may, both separately and in any combination thereof, be material for realizing developed configurations of the invention in diverse forms thereof without departing from the scope of the invention.

Claims: A method for preparing rare earth element RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above comprising the steps of: providing a starting composition containing one or more than two kinds of RE, and Ba, Cu and O as constituent elements to crystallize into the RE 123-type oxide superconductors; melting by heating the starting composition beyond a peritectic temperature of an intended RE 123-type oxide superconductor to form a state of liquid phase or mixed solid and liquid phases; cooling by lowering the temperature of the starting composition to cause a peritectic reaction; solidifying thereby forming oxide superconductive crystals; characterized in that the steps of melting, cooling and solidifying are performed in the air atmosphere, and by the step of changing the initial constitution of said starting composition by controlled replacement between RE and Ba in RE 123 crystals to be formed; said changing step being conducted by a procedure wherein a RE:Ba:Cu mole ratio of said RE 123 crystals to be formed is approximated to 1:2:3 as close as possible by changing the initial constitution of starting composition to a more Ba-rich side than a composition on a 123-211 or 422 tie line of a REO-BaO-CuO ternary phase diagram, so that grains of a RE 211 phase or grains of RE 422 phase dispersed in a RE 123 phase are micronized to secure high critical current density in a magnetic field. The method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above as claimed in claim 1, characterized in that the starting composition is composed of powders forming a starting material; the starting material is sintered to form a sintered body; the sintered body is put on a magnesia single crystal plate; and the step of melting is performed by heating the sintered body beyond the peritectic temperature having a Nd 123 seed crystal placed thereon. The method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above as claimed in claim 2, characterized in that the step of cooling is performed following to the melting step by isothermal retention of the melted sintered body by subcooling. The method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above as claimed in claims 1, 2 or 3 in which a trace amount of Pt or CeO 2 is added to the starting composition as a micro-dispersing agent for grains of the RE 211 phase or grains of the RE 422 phase. The method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above as claimed in any one of claims 1 to 4 in which a means to melt, cool and solidify the starting composition so as to crystallize thereof is a melt-solidifying process. The method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above as claimed in anyone of claims 1 to 5 in which RE is Sm. The method for preparing RE 123-type oxide superconductors exhibiting critical temperature of 90 K or above as clamed in anyone of claims 1 to 5 in which RE is Nd.

Inventors: ENDO TERUHIKO, SHIOHARA YUH, TANAKA SHOJI, UMEDA TAKATERU, WATANABE YASUO, ENDO, TERUHIKO, SHIOHARA, YUH, TANAKA, SHOJI, UMEDA, TAKATERU, WATANABE, YASUO, Endo, Teruhiko, c/o Div. 4, Supercond. Res. Lab., Shiohara, Yuh, c/o Div. 4, Supercond. Res. Lab., Tanaka, Shoji, c/o Div. 4, Supercond. Res. Lab., Watanabe, Yasuo, c/o Div. 4, Supercond. Res. Lab.
Applicants: SUPERCONDUCTIVITY RES LAB, UNIV TOKYO, SUPERCONDUCTIVITY RESEARCH LABORATORY, THE UNIVERSITY OF TOKYO
Application year: 1998
Main classification: H01L39
IPC codes: H01L39, C01G3, C30B29, C01G1