Mercury-thallium-barium-calcium-strontium-copper-oxide 1223 superconductor and method of making same

Abstract

Mercury-thallium based superconductors with the formula Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. ; change "their preparing method, in particular characterized in that it" to and a method for preparing them. The new superconductors are prepared by reacting respective ternary oxides, such as Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2, to reduce the formation of an impure phase and by substituting thallium (Ti) a portion of the mercury (Hg) conventionally used in mercury-based superconductors of similar structure, in order to thermally stabilize the superconductor and provide it with a high critical current density characteristic.

Description

BACKGROUND OF THE INVENTION

Superconductivity was first discovered from investigation of mercury (Hg) by H. Kamerlingh-Onnes in 1908. When a metal or alloy is cooled down below a certain temperature which is called its superconducting transition temperature (Tc), superconductivity is caused by extinction of electrical resistance. Such a superconducting phenomenon is not limited to a specific metal, but can be found in most of metals at a sufficiently low temperature, depending on the metal. For example, whereas the critical superconducting temperature of mercury is 4K, that of a certain alloy of tin and niobium is 18K.

As for superconducting material showing such a phenomenon, metal compounds were mainly used before Bednorz and Muller found superconductivity in La.sub.2-x Ba.sub.x CuO.sub.4 in 1986. Since then, copper oxides have been mainly developed for superconductors having high Tc. After that, many kinds of copper-based superconductors have been synthesized at a higher critical temperature than the boiling point of liquid nitrogen (77K). This became a turning point in studying the application of superconductors. The representative examples are YBa.sub.2 Cu.sub.3 O.sub.7, Bi.sub.2 Sr.sub.2 Ca.sub.n-1 Cu.sub.n O.sub.2n+4 and Tl.sub.2 Ba.sub.2 Ca.sub.n-1 Cu.sub.n O.sub.2n+4.

Recently, the mercury-based superconductor HgBa.sub.2 Ca.sub.2 Cu.sub.3 O.sub.8 was developed by Schilling et al in 1993, which has the highest Tc of 133K among the existing superconductors. However, it is difficult to synthesize the mercury-based compounds due to evaporation of mercury during the preparing process. Furthermore, HgBa.sub.2 Ca.sub.2 Cu.sub.3 O.sub.8 is very unstable in the air, and has low critical current density so that study of its application is limited. On the contrary, thallium-based TlBa.sub.2 Ca.sub.2 Cu.sub.3 O.sub.8+.delta., which has similar structure to the mercury-based superconductors is relatively stable in air. However, it has a Tc of 115K which is much lower Tc than mercury-based superconductors.

SUMMARY OF THE INVENTION

The present invention relates to mercury-thallium based superconductors Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. and to a method for preparing them, in particular characterized in that the superconducting composition is prepared by reacting ternary oxides such as Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2 to prevent the formation of an impure phase, and by substituting thallium (Ti) for a portion of mercury (Hg) to thermally stabilize the superconductor and to provide it with a high critical current density characteristic.

BRIEF DESCRIPTION OF THE DRAWINGS

In the drawings:

FIG. 1 is a set of x-ray powder diffraction patterns of an as-synthesized sample of Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta..

FIG. 2 is the schematic representation of the structure for Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta..

FIG. 3 illustrates the zero-field-cooled (ZFC) and field-cooled (FC) magnetic susceptibility of Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. (x=0.50) as a function of temperature.

FIG. 4 illustrates magnetic susceptibilities of argon and oxygen annealed Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. (x.fwdarw.0.50) as a function of temperature.

FIG. 5 illustrates thermogravimetric analysis of Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. (x=0.50) as a function of temperature.

FIG. 6 shows a comparison of magnetic hysteresis loops at 10K for Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. of the present invention and HgBa.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta..

DETAILED DESCRIPTION

The inventors of the present invention have endeavored to develop a thermally stable superconductor which also has a high critical temperature and a high critical current density. Thus, by reacting Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2, which have similar types of structures to the prepared superconductor, the present inventors have reduced the formation of a impure phase such as CaHgO.sub.2 and prepared new mercury-thallium-based superconductors, with high reproducibility. And by substituting thallium for the a portion of the mercury, the present invention has been accomplished to prepare a new mercury-thallium-based superconductors which is thermally more stable and has higher critical current density than a prior art mercury-based superconductor.

The objective of the present invention is to provide new mercury-thallium-based superconductors and their preparing method, characterized in that the new superconductor is thermally stable and has a high critical temperature and a high critical current density.

Hereinafter, the present invention is described in particular.

The present invention relates to a superconductor with the formula Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. (0.1<x<0.9, 0.1<y<0.2).

The present invention relates to a mercury-thallium-based superconductor which is prepared by reacting ternary oxides such as Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2, to prevent the formation of an impure phase, and by substituting thallium for a portion of mercury, to thermally stabilize the superconductor and to provide it with a high critical temperature and a high critical current density. In preparing Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. and Ca.sub.1-y Sr.sub.y CuO.sub.2 are similar to Hg, Tl-1223) of the present invention, the reactants Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2 are similar to Hg, Tl-1223 in their structures, were used, and thus easily form Hg, Tl-1223.

The method of the present invention may be described by formula (1), all the operations carried out in a dry box filled with argon to prevent contact with air. ##EQU1##

Stoichiometric amounts of HgO, Tl.sub.2 O.sub.3, Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2 are mixed well in powder and pressed into pellets, which are then placed in an alumina tube. The alumina tube is put into a quartz tube and sealed to provide an ampule. The quartz ample is slowly heated up to 860.degree..about.880.degree. C. and sintered at that temperature for 10.about.20 hours, and then slowly cooled. The sintered pellets are annealed at 300.degree..about.400.degree. C. for 6.about.10 hours in argon atmosphere to prepare the Hg, Tl-1223 of the present invention.

According to known the method for preparing mercury-based superconductors, the respective oxides are formed into pellets. On the contrary, according to the present invention, the reactants are ternary oxides, so as to reduce the formation of impure phase CaHgO.sub.2 and also to obtain reproducible synthesis of the products.

The present invention is described in more particular by following examples, but is not limited thereto.

EXAMPLE 1

preparation of Hg.sub.0.5 Tl.sub.0.5 Ba.sub.2 (Ca.sub.0.86 Sr.sub.0.14).sub.2 Cu.sub.3 O.sub.8.

357.3 mg HgO, 376.8 mg Tl.sub.2 O.sub.3, 1274.0 mg Ba.sub.2 CuO.sub.3+x and 939.0 mg Ca.sub.1-y Sr.sub.y CuO.sub.2 are mixed and pressed into pellets, which are then placed in an alumina tube of 8 mm inner diameter (a product of MacDanel Company). The alumina tube is put into a quartz tube of 99.9%, 10 mm inner diameter, and sealed.

The quartz ample is slowly heated up to 870.degree. C., sintered at that temperature for 15 hours, and then slowly cooled. The sintered pellets are annealed at 400.degree. C. for 8 hours in an argon atmosphere. The result of x-ray powder diffraction patterns is shown in FIG. 1. Most of the diffraction peaks are well indexed on space group P4/mmm with lattice parameters of a=3.8649.ANG. and c=15.9573.ANG.. As seen in FIG. 2, the prepared Hg, Tl-1223 has the same structure as known Hg-1223, and its critical temperature is about 132K.

EXAMPLE 2

preparation of Hg.sub.0.75 Tl.sub.0.25 Ba.sub.2 (Ca.sub.0.86 Sr.sub.0.14).sub.2 Cu.sub.3 O.sub.8.

Hg, Tl-1223 (x=0.25) is prepared according to the same method as in Example 1, except that 536.1 mg HgO, 188.4 mg Tl.sub.2 O.sub.3, 1274.0 mg Ba.sub.2 CuO.sub.3+x and 939.0 mg Ca.sub.1-y Sr.sub.y CuO.sub.2 are used.

EXAMPLE 3

preparation of Hg.sub.0.25 Tl.sub.0.75 Ba.sub.2 (Ca.sub.0.86 Sr.sub.0.14).sub.2 Cu.sub.3 O.sub.8.

Hg, Tl-1223 (x=0.75) is prepared according to the same method as in Example 1, except that 565.2 mg HgO, 178.7 mg Tl.sub.2 O.sub.3, 1274.0 mg Ba.sub.2 CuO.sub.3+x and 939.0 mg Ca.sub.1-y Sr.sub.y CuO.sub.2 are used.

COMPARATIVE EXAMPLE 1

Hg, Tl-1223 (x=0.25) is prepared according to the same method as in Example 1. The critical temperature of the resulting Hg, Tl-1223 is 128K.

COMPARATIVE EXAMPLE 2

Hg, Tl-1223 (x=0.75) is prepared according to the same method as in Example 1.

The critical temperature of the resulting Hg, Tl-1223 is 126K.

The effects of the present invention are described with reference to FIGS. 3 to 5, as follows:

FIG. 3 displays the temperature dependence of the magnetic susceptibility for Hg, Tl-1223. It can be seen that Hg, Tl-1223 of the present invention is a superconductor with a Tc of 128K.

FIG. 4 displays the temperature dependence of the magnetic susceptibility for Hg, Tl-1223. It can be seen that the Tc of Hg, Tl-1223 increases to 132K after argon-annealing

FIG. 5 displays thermogravimetric analysis of Hg, Tl-1223 as a function of temperature, showing that a stable phase is maintained up to 500.degree. C. without evaporation of mercury.

FIG. 6 displays the magnetic hysteresis loops for Hg, Tl-1223 of the present invention and HgBa.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta. of a prior art superconductors. It can be seen that Hg, Tl-1223 has a much higher critical current density than a prior mercury-based superconductor.

Therefore, Hg, Tl-1223 of the present invention is thermally more stable than a prior mercury-based superconductor, a higher critical current density and also has a high Tc of 132K. Its preparing method is easy, with high reproducibility.

Claims

1. A mercury-thallium-based superconductor with the formula:

Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta.

wherein x is from about 0.25 to about 0.75and y is greater than 0.1 and less than 0.2.

2. A method of preparing a mercury-thallium-based superconductor with the formula:

Hg.sub.1-x Tl.sub.x Ba.sub.2 (Ca.sub.1-y Sr.sub.y).sub.2 Cu.sub.3 O.sub.8+.delta.

wherein x is from about 0.25 to about 0.75 and y is greater than 0.1 and less than 0.2, said method comprising the steps of:

mixing HgO, Tl.sub.2 O.sub.3, Ba.sub.2 CuO.sub.3+x and Ca.sub.1-y Sr.sub.y CuO.sub.2 in powder form;

pressing the resulting powder mixture into pellets;

placing said pellets in an alumina tube;

putting said alumina tube containing said pellets into a quartz tube;

sealing said quartz tube to create an ampule;

sintering said pellets in said ampule at 860.degree..about.880.degree. C.; and

annealing the resulting sintered pellets at 300.degree..about.400.degree. C. in an argon atmosphere.