Ceramic superconducting composition and process and apparatus for preparing thereof

Abstract

In a ceramic superconducting composition, Ag20 is added thereto in an amount of 0.1 wt. % to 70 wt. % per mole of LaBa2Cu3O3-.delta.. The critical current density of the ceramic superconducting composition is affected by heat treatment conditions. The critical electric current density of the ceramic superconducting composition is increased when it is prepared through heat treatment while controlling the partial pressure of oxygen in a heat treatment atmosphere in steps with successive stages including a temperature-elevating step, a sintering step, a temperature-lowering step, and an annealing step.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to ceramic superconducting materials, processes for preparing the same, and heat treatment apparatuses for preparing the same. More particularly, the invention relates to a lanthanum-based ceramic superconducting material, a process and an apparatus for preparing the same.

2. Description of the Prior Art

A ceramic superconducting composition represented by the compositional formula: YBa.sub.2 Cu.sub.3 O.sub.7-.delta., which is indicative of oxygen insufficiency, is known as a ceramic superconductor having a high superconducting transition temperature. Y.sub.2 O.sub.3 for use in the preparation of this ceramic superconductor is scarce in mineral resources and hence expensive. Since La.sub.2 O.sub.3 is more inexpensive than Y.sub.2 O.sub.3, an LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. superconductor, which contains La in place of Y of the above-mentioned YBa.sub.2 Cu.sub.3 O.sub.7-.delta., will be of a great industrial value if it can be put into practical use.

However, an LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. superconductor having a superconducting transition temperature of 92 K., which has recently been reported in Applied Physics Letters, 52 (23), P. 1989, 1988, is prepared according to a process requiring double calcination at 900.degree. C. and 950.degree. C., sintering at 980.degree. C. for 40 hours, and annealing at 300.degree. C. for 40 hours to give rise to a superconducting phase. Such long hours of the heat treatments present problems of low productivity and poor energy efficiency.

Furthermore, the critical electric current density of the LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. superconducting oxide has not been reported yet and the optimum heat treatment conditions for preparation thereof has not been revealed yet as well. Thus, there are problems to be solved before this superconducting material is put into practical use.

The preparation of oxide superconductors, not to mention lanthanum-based oxide superconducting materials, requires a heat treatment process including sintering and annealing to develop a superconducting phase. The superconducting characteristics of oxide superconductors are greatly affected by heat treatment conditions, among which the control of atmospheres in respective heat treatment stages is of particular importance. However, no apparatuses capable of strictly controlling the partial pressure of oxygen in the vicinity of a material being heat-treated in step with successive stages during the course of heat treatment have been proposed to date.

SUMMARY OF THE INVENTION

An object of the present invention is to provide a superconducting composition mainly comprising LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., and having a high superconducting transition temperature and a high critical electric current density which can be realized even through heat treatment for a short period of time.

Another object of the present invention is to provide a process for preparing a superconducting composition improved in superconducting characteristics even through heat treatment for a short period of time.

Still another object of the present invention is to provide a heat treatment apparatus capable of controlling the heat treatment atmosphere in step with successive stages during the course of heat treatment so as to enable a material being heat-treated to develop the best characteristics.

A further object of the present invention is to provide a heat treatment apparatus which can be effectively used for the preparation of an oxide superconducting material.

In an aspect of the present invention, a ceramic superconducting composition comprises:

an oxide represented by a formula LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and including Ag.sub.2 O in an amount of 0.1 wt. % to 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

Here, the amount of Ag.sub.2 O may be in the range of 5 wt. % to 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

The amount of Ag.sub.2 O may be in the range of 10 wt. % to 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

The amount of Ag.sub.2 O may be in the range of 20 wt. % to 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

The amount of Ag.sub.2 O may be in the range of 20 wt. % to 25 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

In another aspect of the present invention, a process for preparing a ceramic superconducting composition comprising the steps of:

elevating the temperature of a ceramic superconducting composition;

sintering the composition;

lowering the temperature of the composition; and

annealing the composition;

while controlling the partial pressure of oxygen in the vicinity of the composition in the respective steps.

Here, the ceramic superconducting composition may comprise LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and Ag.sub.2 O added thereto in an amount of 0.1 wt. % to 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

Ba(OH).sub.2 .multidot.8H.sub.2 O may be used as the starting Ba material of the composition.

The partial pressures of oxygen respectively in the temperature-elevating step and the sintering step may be each at most 20%, while the partial pressures of oxygen respectively in the temperature-lowering step and the annealing step are each at least 70%.

The partial pressures of oxygen respectively in the temperature-lowering step and the annealing step may be 100%.

The partial pressure of oxygen in the sintering step may be 0%.

The partial pressures of oxygen respectively in the temperature-elevating step, the sintering step, the temperature-lowering step and the annealing step may be all 20%.

In still another aspect of the present invention, a heat treatment apparatus for preparing a ceramic superconducting composition comprises:

a heat treatment furnace;

a heating means for heating a material disposed in the heat treatment furnace and to be heat-treated;

a temperature control means for controlling the heating means in such a way as to change the temperature of the above-mentioned material in accordance with a predetermined time versus temperature profile;

a gas feeding means for feeding an oxygen gas and an inert gas into the heat treatment furnace;

a gas pressure control means for controlling the gas pressure inside the heat treatment furnace to a predetermined level;

an oxygen detection means for detecting the amount of oxygen in the vicinity of the material; and

gas flow rate control means for controlling the flow rate of the oxygen gas and the flow rate of the inert gas in such a way as to set the partial pressure of oxygen in the vicinity of the material at a predetermined level on the basis of the result of detection by the oxygen detection means, the gas flow rate control means being capable of preliminarily memorizing a predetermined partial-pressure-of-oxygen versus time profile.

The above and other objects, effects, features and advantages of the present invention will become more apparent from the following description of embodiments thereof taken in conjunction with the accompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a diagram illustrative of the heat treatment process of the present invention;

FIG. 2 is a schematic diagram of the heat treatment apparatus of the present invention;

FIG. 3 is a diagram showing the electric resistance versus temperature characteristic curve of an example of the ceramic superconducting composition of the present invention;

FIG. 4 is a diagram showing the AC susceptibility versus temperature characteristic curve of an example of the ceramic superconducting composition of the present invention; and

FIG. 5 is a diagram showing the X-ray diffraction pattern of an example of the ceramic superconducting composition of the present invention.

DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS

The following examples will now illustrate the present invention in detail by reference to the accompanying drawings.

La.sub.2 O.sub.3, Ba(OH).sub.2 .multidot.8H.sub.2 O and CuO each in a dry state were weighed and mixed and pulverized at an La:Ba:Cu ratio of 1:2:3. The resulting powdery mixture was heat-treated at 800.degree. to 900.degree. C. for 10 hours. Such a heat treatment may be effected in any atmosphere selected from air, oxygen and nitrogen. The heat-treated mixture was pulverized again and passed through a 30 .mu.m sieve to obtain an LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. powder.

BaCO.sub.3 is usually used as a starting Ba material. The use of BaCO.sub.3 as the starting Ba material results in carbonate groups remaining even after a heat treatment at 900.degree. to 950.degree. C. and causing to shift the resultant composition away from the intended one. In view of this, highly reactive Ba(OH).sub.2.8H.sub.2 O free of carbonate groups was used as the starting Ba material in the present invention. For comparison, however, a sample was prepared using BaCO.sub.3 as the starting Ba material.

The LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. powder thus obtained was admixed with a predetermined amount of an Ag.sub.2 O powder (purity: 99.99%), followed by formation therefrom of a pellet of 15 mm in diameter and 1.5 mm in thickness under a pressure of 1 to 2 tons/cm.sup.2. The above-mentioned predetermined amount of the Ag.sub.2 O powder was varied within the range of 0 to 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. powder to prepare a plurality of pellets. Each of the pellets was placed in a crucible and heat-treated while controlling the temperature and total pressure of a heating atmosphere and the partial pressure of oxygen in the heating atmosphere.

FIG. 1 shows an example of the time versus temperature profile during the course of heat treatment. As shown in FIG. 1, the heat treatment process comprises four steps consisting of the step (a) of elevating the temperature up to a sintering temperature, the step (b) of sintering at the constant temperature, the step (c) of lowering the temperature down to an annealing temperature, and the step (d) of annealing at the constant temperature for developing a superconducting phase.

In the following examples, the temperature-elevating rate and the temperature-lowering rate were kept constant at 200.degree. C./hr and 60.degree. C./hr, respectively. The sintering temperature was arbitrarily chosen from within the range of 900.degree. C. to 980.degree. C., while the sintering time was set to be 5 hours for all runs. The annealing temperature was set to be 300.degree. C. for all runs, while the annealing time was set to be 5 hours or 10 hours.

As shown in FIG. 1, the heat treatment process was divided into four segments (a), (b), (c) and (d), in step with which the atmosphere was controlled during the course of heat treatment. The segment (a) corresponds to a stage of elevating the temperature up to 700.degree. C. The segment (b) comprises a stage of elevating the temperature above 700.degree. C., the central step of sintering, and a stage of lowering the temperature down to 900.degree. C. The segment (c) corresponds a stage of lowering the temperature from 900.degree. C., while the segment (d) corresponds to the step of annealing for developing the superconducting phase. According to the present invention, the total pressure inside the heat treatment furnace was controlled while at the same time the partial pressure of oxygen was controlled in step with the successive segments through detection of the partial pressure of oxygen in the vicinity of the pellet being heat-treated. In the foregoing manner, samples differing in the amount of Ag.sub.2 O added thereto were prepared through heat treatment.

FIG. 2 diagrammatically shows an apparatus used for effecting the foregoing heat treatment. A heat treatment furnace 1 is first evacuated to a predetermined degree of vacuum with a pumping system 2 including a rotary pump 2A, an electromagnetic vacuum valve 2B, an air filter 2C, a leak valve 2D and a vacuum indicator 2E. Subsequently, a mixed gas of oxygen and nitrogen (or argon) is fed into the heat treatment furnace 1. Oxygen is fed from a cylinder 3A through a stop valve 3B, a needle valve 3C, a mass flow controller 3D, a chuck valve 3E and a control valve 3F into a gas mixer 5. Likewise, nitrogen (or argon) is fed from a cylinder 4A through a stop valve 4B, a needle valve 4C, a mass flow controller 4D, a chuck valve 4E and a control valve 4F into the gas mixer 5. Oxygen and nitrogen (or argon) are mixed with each other in the gas mixer 5. A mixed gas (or a single gas) is passed through a gas feed valve 6 and guided into the heat treatment furnace 1. The pressures of the gases guided from the respective cylinders 3A and 4A to the respective stop valves 3B and 4B are detected with primary pressure gauges 3G and 4G, respectively. An oxygen sensor 7 is disposed in the vicinity of a material being heat-treated inside the heat treatment furnace 1 to detect the amount of oxygen in the vicinity of the material being heat-treated. A signal detected is input to an oxygen concentration meter 8, from which the signal of oxygen concentration is then input to a partial oxygen pressure controller 9. The partial pressures of oxygen respectively predetermined for the aforementioned segments are memorized in a temperature controller 10 for controlling the temperature inside the heat treatment furnace 1 through control of an electric current flowing through a resistance heating element 11. The above-mentioned predetermined partial pressures of oxygen are compared with the signal of oxygen concentration from the oxygen concentration meter 8 by means of the partial oxygen pressure controller 9, which then controls the partial pressure of oxygen in the vicinity of the material being heat-treated to a predetermined value through opening or closing of the control valves 3F and 4F. Drawing of a termocouple for measuring the temperature inside the heat treatment furnace 1 is omitted from FIG. 2.

A signal of the pressure of the gas fed into the heat treatment furnace 1 is input to a gas pressure controller 12, which operates an exhaust valve 13 in such a way as to keep the pressure inside the heat treatment furnace 1 at a predetermined level. When the pressure inside the heat treatment furnace 1 happens to become excessively high, a safety valve 14 is operated to prevent any damage to the heat treatment furnace 1 from occurring. The body of the heat treatment furnace 1 is capable of being cooled with water.

The various samples prepared using the apparatus as shown in FIG. 2 were examined with respect superconducting transition temperature and critical electric current density and subjected to an analysis of crystal structure through X-ray diffractmetry. The superconducting transition temperature T.sub.C (end), at which the electric resistance of each sample falls down to zero, was determined using a four probe method of measuring the DC resistance of the sample. The superconducting transition temperature TcI of each sample was determined from the variation of the AC susceptibility of the sample with temperature which was examined using a hartshorn bridge. The maximum value of electric current, at which the superconducting state of each sample placed deep in liquid nitrogen was maintained when a large electric current pulse was flowed through the sample, was determined. This maximum value of electric current was used to find the critical current density J.sub.C of the sample.

The superconducting transition temperatures Tc(end) and TcI and the critical current densities of the various samples prepared by varying the Ag.sub.2 O concentration and the heat treatment conditions are shown in Table 1, in which the total pressures in the furnace are listed using atmospheric pressure as a standard and Sample No. 42 with a mark of * refers to a sample prepared using BaCO.sub.3 as the starting Ba material.

By way of example, FIGS. 3 and 4 show the electric resistance versus temperature characteristic curve and the AC susceptibility versus temperature characteristic curve of Sample No. 7.

TABLE 1__________________________________________________________________________ Total Pres- Critical Amount by sure in Current wt. % of Ag Partial Pressure of Furnace Density SinteringSample per mol of Oxygen in Furnace (%) (kg/cm.sup.2) Critical Temperature Jc(A/cm.sup.2) Temperature AnnealingNo. LaBa.sub.2 Cu.sub.3 O.sub.7 -.delta. a b c d e Tc (end) (K.) TCI (K.) (at 77K) (.degree.C.) Time__________________________________________________________________________ (hrs) 1 0.1 20 0 100 100 1.2 89 89 25 960 10 2 0.5 20 0 100 100 1.2 90 90 18 960 10 3 1.0 20 0 100 100 1.2 88 88 15 950 10 4 2.0 20 0 100 100 1.2 91 90 17 950 10 5 3.0 20 0 100 100 1.2 92 92 50 950 10 6 5.0 20 0 100 100 1.2 90 91 55 950 10 7 10.0 20 0 100 100 1.2 86 87 167 950 10 8 15.0 20 0 100 100 1.2 88 89 260 950 10 9 20.0 20 0 100 100 1.2 87 88 390 950 1010 25.0 20 0 100 100 1.2 90 90 355 940 1011 30.0 20 0 100 100 1.2 92 92 270 940 1012 50.0 20 0 100 100 1.2 93 92 280 940 1013 70.0 20 0 100 100 1.2 90 91 250 950 1014 100.0 20 0 100 100 1.2 Fused with -- 950 10 Crucible15 150.0 20 0 100 100 1.2 Fused with 950 10 Crucible16 200.0 20 0 100 100 1.2 Fused with 950 10 Crucible17 10.0 20 20 20 20 1.0 82 83 180 950 518 20.0 20 20 20 20 1.0 86 86 228 950 519 70.0 20 20 20 20 1.0 90 90 230 950 520 10.0 20 100 100 100 1.2 83 84 70 950 1021 20.0 20 100 100 100 1.2 83 83 62 950 1022 70.0 20 100 100 100 1.2 83 84 60 940 1023 10.0 100 0 50 20 1.2 86 87 60 950 1024 20.0 100 0 50 20 1.2 80 81 70 950 1025 70.0 100 0 50 20 1.2 87 88 50 940 1026 10.0 0 0 100 100 1.0 90 90 170 950 1027 20.0 0 0 100 100 1.0 90 90 200 950 1028 70.0 0 0 100 100 1.0 70 90 219 950 1029 10.0 0 0 20 40 -0.7 Insulator 930 1030 20.0 0 0 20 40 -0.7 Insulator 930 1031 70.0 0 0 20 40 -0.7 Insulator 920 1032 10.0 0 0 70 70 -0.5 86 87 201 920 1033 20.0 0 0 70 70 -0.5 88 88 192 930 1034 70.0 0 0 70 70 -0.5 90 90 230 920 1035 0 20 0 100 100 1.2 90 90 25 970 1036 0 20 20 20 20 1.0 Insulator 950 537 0 20 100 100 100 1.2 Insulator 950 1038 0 100 0 50 20 1.2 Insulator 950 1039 0 0 0 100 100 1.0 72 72 950 1540 0 0 0 20 40 -0.7 60 61 930 1541 0 0 0 70 70 -0.5 62 62 920 15*42 0 20 0 100 100 1.2 82 82 11 970 40__________________________________________________________________________

As can be seen in Table 1, the critical current density Jc varies depending on the amount of Ag.sub.2 O added and the heat treatment conditions. The critical current density Jc increases with an increase in the amount of Ag.sub.2 O added if heat treatment is effected under suitable conditions. More specifically, the critical current densities Jc of samples respectively containing 5 wt. %, 10 wt. % and 15 wt. %, per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., of Ag.sub.2 O added thereto were increased to at least 50 A/cm.sup.2, at least 100 A/cm.sup.2 and at least 200 A/cm.sup.2, respectively, while the critical current density Jc of a sample containing 20 wt. %, per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., of Ag.sub.2 O added thereto reached a high level of 390 A/cm.sup.2. Further addition of Ag.sub.2 O in an amount exceeding 20 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. resulted in a decrease in the critical current density Jc, which was, however, maintained at a high level of at least 200 A/cm.sup.2 until the amount of Ag.sub.2 O added reached 70 wt. % per mole LaBa.sub.2 Cu.sub.3 O.sub.7-.delta.. The values of 390 A/cm.sup.2 and 280 A/cm.sup.2 as the critical current densities Jc of Sample Nos. 9 and 12, respectively, are more than 20 times that of Sample No. 42 which is a conventional superconductor prepared using BaCO.sub.3 as the starting Ba material and containing no Ag.sub.2 O added thereto, and more than 10 times that of Sample No. 35 which exhibited the highest critical current density of 25 A/cm.sup.2 among those samples prepared using Ba(OH).sub.2 .multidot.8H.sub.2 O as the starting Ba material but containing no Ag.sub.2 O added thereto. The superconducting transition temperatures of the samples improved in Jc by addition of Ag.sub.2 O were around 90 K., demonstrating that no notable decrease in superconducting transition temperature occurred by addition of Ag.sub.2 O.

Addition of 0.1 wt. % Ag.sub.2 O enabled sintering to be effected at a low temperature and caused no change in Jc as compared with no addition of Ag.sub.2 O. When the amount of Ag.sub.2 O added exceeded 70 wt. % per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., metallic silver precipitated on the surface of a ceramic pellet to fuse with a crucible during heat treatment, with the result that a difficulty was experienced in preparing a sample. Addition of more than 70 wt. % Ag.sub.2 O is not preferable from the economical point of view. It is presumed that a small amount of Ag.sub.2 O may form a solid solution with LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., while most of Ag.sub.2 O precipitates in the form of metallic silver. FIG. 5 is a diagram showing the X-ray diffraction pattern of Sample No. 19 containing 70 wt. %, per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., of Ag.sub.2 O added thereto. In FIG. 5, strong peaks assigned to metallic silver are seen together with peaks assigned to rhombic LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

The critical current density Jc varies depending on heat treatment conditions, particularly on the partial pressures of oxygen respectively in the aforementioned successive segments. Table 2 is a summary of data for the samples respectively containing 10 wt. %, 20 wt. % and 70 wt. %, per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta., of Ag.sub.2 O added thereto, which data were extracted from Table 1.

TABLE 2__________________________________________________________________________ Total Critical Current Pressure Density Jc(A/cm.sup.2) in (at 77K)Partial Pressure Furnace Ag.sub.2 O 10 wt. % Ag.sub.2 O 20 wt. % Ag.sub.2 O 70 wt. %of Oxygen (%) (kg/cm.sup.2) per mol of per mol of per mol ofa b c d e LaBa.sub.2 Cu.sub.3 O.sub.7 -.delta. LaBa.sub.2 Cu.sub.3 O.sub.7 -.delta. LaBa.sub.2 Cu.sub.3 O.sub.7 -.delta.__________________________________________________________________________20 0 100 100 1.2 167 390 25020 20 20 20 1.0 180 228 230 0 0 100 100 1.0 170 200 219 0 0 70 70 -0.5 201 192 23020 100 100 100 1.2 70 62 60100 0 50 20 1.2 60 70 50 0 0 20 40 -0.7 -- -- --__________________________________________________________________________

It will be understandable from Table 2 that even heat-treated ceramics containing the same amount of Ag.sub.2 O added thereto greatly vary in critical current density Jc, depending on the heat treatment conditions. The critical current density Jc is not so much affected by the total pressure in the furnace. A factor having a great influence on the critical current density Jc is the partial pressures of oxygen respectively in the aforementioned successive segments. Samples prepared by heat treatment under conditions involving a partial pressure of oxygen of 0% in both the segments (a) and (b) and partial pressures of oxygen of 20% and 40% in the segments (c) and (d), respectively, were insulators, whereas samples prepared by heat treatment under conditions involving partial pressures of oxygen of at most 20% in the segments (a) and (b) and partial pressures of oxygen of at least 70% in the segments (c) and (d), or partial pressures of oxygen of at least 20% in all of the segments were improved to exhibit a critical current density Jc of 160 A/cm.sup.2 to 390 A/cm.sup.2. Thus, it will be understood that, when the partial pressure of oxygen in the vicinity of a material being heat-treated is controlled in step with successive segments during the course of heat treatment, the critical current density Jc of the heat-treated material can be improved even by shortened hours of heat treatment. The superconducting transition temperatures Tc(end) and TcI are not greatly affected by the partial pressure of oxygen.

Referring to Table 1 again, Sample No. 42 prepared using BaCO.sub.3 as the starting Ba material according to the conventional process will be compared with Sample No. 35 prepared using Ba(OH).sub.2 .multidot.8H.sub.2 O as the starting Ba material under the same heat treatment conditions as in the case of Sample No. 42 except for the annealing time. Although the annealing time was as long as 40 hours in the case of Sample No. 42, Sample No. 35 was superior in superconducting transition temperatures Tc(end) and TcI as well as critical current density Jc to Sample No. 42. This will substantiate the supremacy of Ba(OH).sub.2.8H.sub.2 O as the starting Ba material over BaCO.sub.3.

It will be obvious to those skilled in the art that the process of the present invention can also be widely applied to the preparation of oxide superconductors other than LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and Ag.sub.2 O-added LaBa.sub.2 Cu.sub.3 O.sub.7-.delta..

As described above, according to the present invention, addition of Ag.sub.2 O to the superconducting material LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. can improve the critical current density Jc thereof despite a short heat treatment time. Furthermore, according to the present invention, control of the partial pressure of oxygen in the vicinity of a material being heat-treated in step with successive stages during the course of heat treatment can improve the superconducting characteristics of the resultant superconducting composition.

The superconducting composition of the present invention can be used in superconducting magnets, a wide variety of superconducting devices, and power storage utilizing super conductivity.

The heat treatment apparatus of the present invention can be utilized in heat treatment of various ceramic material compositions requiring control of the partial pressure of oxygen in addition to the preparation of oxide superconductors.

The invention has been described in detail with respect to preferred embodiments, and it will now be apparent from the foregoing to those skilled in the art that changes and modifications may be made without departing from the invention in its broader aspects, and it is the invention, therefore, in the appended claims to cover all such changes and modifications as fall within the true spirit of the invention.

Claims

1. A ceramic superconducting composition consisting essentially of:

an oxide represented by a formula LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and including Ag.sub.2 O, wherein said Ag.sub.2 O in said oxide is present in the range of 10 to 70% by weight per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100.

2. A ceramic superconducting composition as claimed in claim 1, wherein said Ag.sub.2 O in said oxide is present in the range of 20 to 70% by weight per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100.

3. A ceramic superconducting composition as claimed in claim 1, wherein said Ag.sub.2 O in said oxide is present in the range of 20 to 25% by weight per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100.

4. A process for preparing a ceramic superconducting composition comprising the steps of:

a) mixing a ceramic superconducting powder of an oxide represented by a formula LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. with a silver oxide powder to obtain a silver-containing mixture;

b) elevating to a first temperature of from 900.degree. C. to 980.degree. C. said silver-containing mixture at a temperature-elevating rate of 200.degree. C. per hour;

c) sintering said silver-containing mixture at said first temperature;

d) lowering said first temperature to a second temperature of 300.degree. C. said silver-containing mixture at a temperature-lowering rate of 60.degree. C. per hour; and

e) annealing said silver-containing mixture at said second temperature to obtain a ceramic superconducting oxide composition;

while controlling the partial pressure of oxygen in the vicinity of said silver-containing mixture in said respective steps.

5. A process as claimed in claim 4, wherein said ceramic superconducting oxide composition consists essentially of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and Ag.sub.2 O added thereto such that said Ag.sub.2 O in said oxide is present in the range of 10 to 70 percent by weight per mole of said LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100.

6. A process as claimed in claim 5, wherein Ba(OH).sub.2 .multidot.8H.sub.2 O is used as the starting Ba material of said composition.

7. A process as claimed in claim 5, wherein the partial pressures of oxygen respectively in said temperature-elevating step and said sintering step are each at most 20%, while the partial pressures of oxygen respectively in said temperature-lowering step and said annealing step are each at least 70%.

8. A process as claimed in claim 7, wherein the partial pressures of oxygen respectively in said temperature-lowering step and said annealing step are 100%.

9. A process as claimed in claim 8, wherein the partial pressure of oxygen in said sintering step is 0%.

10. A process as claimed in claim 5, wherein the partial pressure of oxygen, respectively, in said temperature-elevating step, said sintering step, said temperature-lowering step, and said annealing step are each 20%.

11. A ceramic superconducting composition consisting essentially of:

an oxide represented by a formula LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and Ag.sub.2 O, wherein the weight ratio of said Ag.sub.2 O to said LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. is in the range of 0.1 to 0.7.

12. A ceramic superconducting composition as claimed in claim 11, wherein the weight ratio is in the range of 0.15 to 0.7.

13. A process for preparing a ceramic superconducting composition comprising the steps of:

a) mixing ceramic superconducting powder and silver oxide powder to form a silver-conducting composition, wherein the content of silver oxide in said composition is within the range of 10 to 70% by weight per mole of said ceramic superconducting powder;

b) elevating to a first temperature of from 900.degree. C. to 980.degree. C. said silver-containing composition at a temperature-elevating rate of 200.degree. C. per hour;

c) sintering said silver-containing composition at said first temperature; and

d) lowering said first temperature to a second temperature of 300.degree. C. said silver-containing composition at a temperature-lowering rate of 60.degree. C. per hour;

e) annealing said silver containing composition at said second temperature and controlling the partial pressure of oxygen in said respective steps such that the partial pressure in said sintering step is not higher than the partial pressure in said other steps.

14. A process as claimed in claim 11, wherein said ceramic superconducting powder consists essentially of LaBa.sub.2 CU.sub.3 O.sub.7-.delta., wherein .delta. is the deviation from the stoichiometerical value of said powder.

15. A process as claimed in claim 4, wherein the partial pressure of oxygen in said temperature-elevating step, said temperature-lowering step, and said annealing step, respectively, are controlled to be more than the partial pressure of oxygen in said sintering step.

16. A ceramic superconducting composition consisting essentially of an oxide represented by the formula LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. and Ag.sub.2 O, wherein .delta. is the deviation from the stoichiometrical value of said composition and said Ag.sub.2 O in said oxide is present at from 10 to 70% by weight per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100, said oxide being prepared by a process comprising the steps of:

a) mixing a ceramic superconducting powder with a silver oxide powder to obtain a silver-containing mixture;

b) elevating to a first temperature of 900.degree. C. to 980.degree. C. said silver-containing mixture at a temperature-elevating rate of 200.degree. C. per hour;

c) sintering said silver-containing mixture at said first temperature;

d) lowering said first temperature to a second temperature of 300.degree. C. said silver-containing mixture at a temperature-lowering rate of 60.degree. C. per hour; and

e) annealing said silver-containing mixture at said second temperature to obtain said ceramic superconducting oxide composition;

while controlling the partial pressure of oxygen in the vicinity of said silver-containing mixture in said respective steps.

17. A ceramic superconducting composition as claimed in claim 16, wherein said respective steps are performed while controlling the partial pressure of oxygen so that the partial pressure of oxygen in said sintering step is not higher than the partial pressure in said other steps.

18. A ceramic superconducting composition as claimed in claim 16, wherein said Ag.sub.2 O in said oxide is present in the range of 20 to 70% by weight per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100.

19. A ceramic superconducting composition as claimed in claim 16, wherein said Ag.sub.2 O in said oxide is present in the range of 20 to 25% by weight per mole of LaBa.sub.2 Cu.sub.3 O.sub.7-.delta. being represented by 100.