Oxide superconductor and method for manufacturing the same

Abstract: The present invention provides an oxide superconductor which is expressed in the composition formula (Pb 1-x-y M x (A1) y )(A2)₂(A3) n-1 (Cu) n (O) 2n+3+z (wherein 0 ≦ x ≦ 0.6, 0 ≦ y ≦ 0.6, x+y ≦ 0.6 , n denotes integers of 1 or more, -0.6 ≦z ≦ 0.5, M denotes Cu or Cd, and A1, A2 and A3 denote at least one element of Ba, Sr, and Ca, respectively) and which has a crystal structure stacking rock salt structure based portions and infinite layer structure portions, wherein the rock salt structure based portion has a structure that an atoms layer having 0.5-1.5 oxygen atoms, in case the total atoms number of Pb, M and A1 is one, and an atoms layer having one or less oxygen atoms per one A2 atom, are stacked and the infinite layer structure portion has a structure that an atoms layer having 2 oxygen atoms per one Cu atom and an atoms layer of A3 atoms only, are stacked. Further, the present invention provides a method for manufacturing the above oxide superconductor by heat-treating a raw material of oxide superconductor at a temperature of 800-1200°C under superhigh pressure of 2-8GPa.

Description: The present invention relates to an oxide superconductor which exhibits superconductivity at a temperature of liquid nitrogen or more (77K or more) and a method for manufacturing the same. Oxide superconductors have unique characteristics, which show an electric resistance of zero at a critical temperature (hereinafter referred to as Tc) or less, show perfect diamagnetisms and give Josephson effect, and thereby they have been expected to be applied to a variety of fields, such as cables for power transmission, electric wires for generator, containment materials for nuclear fusion plasma, materials for magnetic levitation train, magnetic shield materials, or high-speed computers. Following to the time when Bednorz and Müller discovered La-Ba-Cu-O series oxide superconductor having Tc of approximately 30K in 1986, there have been reported oxide superconductors for relatively high temperature, such as Y-Ba-Cu-O series oxide superconductor (Tc ≥ 90K), Bi-Sr-Ca-Cu-O series oxide superconductor (Tc ≥ 110K), Tl-Ba-Ca-Cu-O series oxide superconductor (Tc ≥ 125K), Hg-Ba-Ca-Cu-O series oxide superconductor (Tc ≥ 135K). A variety of investigations have recently been performed concerning their preparation processes, physical properties, applications or the others. High Tc values mean that cooling necessary to exhibit superconductivity is easy. Therefore, oxide superconductors of higher Tc values have extremely large advantages in practice, and such novel oxide superconductors have been expected to be discovered. However, although Tl-Ba-Ca-Cu-O series and Hg-Ba-Ca-Cu-O series oxide superconductor have been discovered and relatively high Tc values, they are very hard to handle, since they contain extremely toxic Tl or Hg. And, resources of rare earth elements, such as Y, are maldistributed and they require increased purifying cost. Such conditions have become large obstacles to practical applications of oxide superconductors. M. Hechtl, J. Bernhard and K.F. Renk, Supercond. Sci. Technol. 7 (1994), S. 407-411, Report on the preparation of superconducting samples of the 1212 systems (Pb 0,5 Sr 0,5 )Sr 2 (Y 1-x Ca x )Cu 2 O 7±δ and (Pb 0,5 Ca 0,5 )Sr 2 (Y 1-x Ca x )Ci 2 O 7±δ in an oxidizing atmosphere of normal O 2 pressure. By variation of the Y/Ca ratio an optimum of the temperature at which superconductivity sets in, T ons / c, was found for x = 0,80 in both systems. The present invention has been performed in consideration of the aspects, and it is the object of the present invention to provide a novel oxide superconductor and a method for manufacturing the same, which not only has Tc value of 100K or more but contains neither Tl or Hg being extremely hard to handle nor rare earth elements which are maldistributed and require high purifying cost. The present invention provides an oxide superconductor which is expressed in the composition formula (Pb 1-x-y M x (A1) y )(A2) 2 (A3) n-1 (Cu) n (O) 2n+3+z (wherein 0 ≤ x ≤ 0.6, 0 ≤ y ≤ 0.6, x+y ≤ 0.6, n denotes integers of 1 or more, -0.6 ≤ z ≤ 0.5, M denotes Cu or Cd, and A1, A2 and A3 denote at least one element of Ba, Sr and Ca, respectively) and which has a crystal structure stacking rock salt structure based portions and infinite layer structure portions, wherein the rock salt structure based portion has a structure that an atoms layer having 0.5-1.5 oxygen atoms, in case the total atoms number of Pb, M and A1 is one, and an atoms layer having one or less oxygen atoms per one A2 atom, are stacked, and further the infinite layer structure portion has a structure that an atoms layer having two oxygen atoms per one Cu atom and an atoms layer of A3 atoms only are stacked. Further, the present invention provides a method for manufacturing the above oxide superconductor by heat-treating a raw material of oxide superconductor at a temperature of 800-1200°C under superhigh pressure of 2-8GPa. This invention can be more fully understood from the following detailed description when taken in conjunction with the accompanying drawings, in which: FIG. 1 is a view showing one example of crystal structure of oxide superconductors according to the present invention; FIG. 2 is a graph showing temperature dependence of magnetic susceptibility as to the oxide superconductor of Example 1; FIG. 3 is a graph showing temperature dependence of resistivity as to the oxide superconductor of Example 1; FIG. 4 is an X-ray diffraction pattern of the oxide superconductor of Example 1; FIGS. 5A and 5B are electron beam diffraction patterns as to the oxide superconductors of Example 1; FIG. 6 is a view showing the crystal structure of oxide superconductor of Example 1 according to the present invention; FIG. 7 is a graph showing temperature dependence of magnetic susceptibility as to the oxide superconductor of Example 2; and FIG. 8 is a graph showing temperature dependence of resistivity as to the oxide superconductor of Example 2. The oxide superconductor according to the present invention prescribes Cu or Cd as M in the composition formula of (Pb 1-x-y M x (A1) y )(A2) 2 (A3) n-1 Cu n O 2n+3+z . Thereby, when using Cu as M, it becomes easy to handle and influences on human body becomes reduced, and, when using Cd, better oxide superconductors may be obtained having higher Tc value and volume fraction (the ratio of superconductive phase to the sample made). Further, in the above composition formula, at least one element of Ba, Sr and Ca may be selected, as A1, A2 and A3, respectively, since no oxide superconductors are obtained without these elements. Also, a plurality of elements may be used, since two or more kinds of elements at one site is less sensitive to superconductivity. In the above composition formula, x and y are set to 0 ≤ x ≤ 0.6. When x or y exceeds 0.6, the rock salt structure based portion becomes unstable, and superconductivity is reduced. Also, x+y is set at x+y ≤ 0.6, since, when x+y exceeds 0.6, superconductivity of the oxide superconductor become reduced. Further, in the above composition formula, n is set to integers of one or more, and particularly in case of the oxide superconductor having infinite layer structure, n is preferred to be integers of 2-4 so as to give higher Tc. As to Cu oxides, it is preferred to be the condition giving higher Tc value, i. e. average valences of Cu ion of +2.05 - +2.25. In consideration of this average valence, z is ordinarily preferred to be set to -0.6 ≤ z ≤ 0.5. In the oxide superconductor according to the present invention, the rock salt structure based portion has a structure that an atoms layer having 0.5-1.5 oxygen atoms, in case the total atoms number of Pb, M and A1 is one, and an atoms layer having one or less oxygen atoms per one A2 atom, are stacked. That is to say, in FIG. 1 it has a structure that (Pb, M, A1)- O layer and A2- O layer are stacked. In this structure, even if the position of the alkaline earth element A1 is occupied by either any element of Ba, Sr and Ca or a plurality of these elements, large differences do not created to superconductivity. Also, A2 position tends to be occupied by Sr or Ba, but Ca could occur partially as a solid solution. In every cases, Tc value and volume fraction are not largely affected. The reasons why, in (Pb, M, A1)- O layer, oxygen atoms is prescribed to 0.5-1.5, in case the total atoms of Pb, M and A1 is one and further, in A2- O layer, oxygen atoms per one A2 atom is prescribed to one or less is to maintain Cu valence of infinite layer portion within +2.05 - +2.25, where superconductivity are exhibited. Further, changes in oxygen amount (z) are created by increase or decrease in oxygen amount of (Pb, M, A1)- O layer and A2- O layer. In the oxygen superconductor according to the present invention, the infinite layer structure portion has a structure that an atoms layer having 2 oxygen atoms per one Cu atom and an atoms layer of A3 atoms only are stacked. That is to say, in FIG. 1, the portion has a structure that Cu-O 2 layer and A3 layer are stacked. The process for preparing the oxygen superconductor according to the present invention is characterized by effecting heat-treatment on a raw material of oxide superconductor at a temperature of 800-1200°C under superhigh pressure of 2-8GPa. Thus, the pressure of heat-treatment is set at 2-8GPa. The pressure below 2GPa is too low to obtain the oxygen superconductor according to the present invention, and, when the pressure exceeds 8GPa, special pressure generation techniques to obtain high pressure are required and it is not practical for industrial applications in terms of equipment and operation costs. And, temperatures of heat treatment is set at 800-1200°C. The temperature below 800°C is too low to obtain the oxygen superconductor according to the present invention, and the temperature above 1200°C is too high for the raw material to be dissolved. Hereinafter, some examples according to the present invention will be concretely described with reference to the drawings. (Example 1) Each raw material powder of SrCO 3 and CuO having a purity of 99.9% or more is weighed at molar ratio of 1 : 1 to mix. The mixed powder was calcined at 970°C for 10 hours in the air to obtain the calcined material and be ground. The calcination and grinding were repeated several times, and SrCuO 2 was made as the precursor. On the other hand, each raw material powder of CaCO 2 and CuO having a purity of 99.9% or more is weighed at a molar ratio of 2 : 1 to mix. The mixed powder is calcined at 970°C for 10 hours in the air, as shown above, to obtain the calcined material and be ground. The calcination and grinding were repeated several times, and Ca 2 CuO 3 was made as the precursor. Next, the resulting SrCuO 2 and Ca 2 CuO 3 , as well as raw material powders of PbO and CuO having a purity of 99.9% or more are mixed at a molar ratio of Pb : Sr : Ca : Cu = 0.5 : 2 : 2 : 3.5 to obtain a mixed powder. The mixed powder was filled into a gold capsule and further added KClO 4 as a oxidant in order to control the oxygen amount of oxide superconductor, and then the gold capsule was sealed. This gold capsule was located inside a hexagonal cubic anvil type superhigh pressure generator, and the gold capsule was heat-treated at 900°C for 30 minutes under a pressure of 5GPa. The heat-treatment was performed by forming a thin NaCl layer outside of the gold capsule, inserting the gold capsule into a graphite sleeve (heater), applying an electric current during impression of pressure. After the heat-treatment, the gold capsule was taken out from the generator, and also the oxide superconductor was taken out from the capsule. Temperature dependencies as to magnetic susceptibility of the obtained oxide superconductor were investigated. The result is shown in FIG. 2. Measurements of magnetic susceptibility were performed through two modes, i. e., zero magnetic field cooling (ZFC) that measurements are performed during gradual increase in temperature under impression of 1Oe magnetic field, followed by cooling the oxide superconductor until 4.2K in the zero magnetic field; and magnetic field cooling (FC) that the oxide superconductor is cooled under 1Oe magnetic field. As will be understood from FIG. 2, the temperature which shows diamagnetism (Tc) was 115K. Also, volume fraction at 5K was estimated to be 26% from FC data, which was relatively high value. Next, temperature dependencies as to electric resistivity of the obtained oxide superconductor were investigated. The result is shown in FIG. 3. Measurements of electric resistivity were performed through ordinary four-terminal process. As will be understood from FIG. 3, the resistivity decreases as the temperature decreases, just as is the metal, and at approximately 115K decreases rapidly, and then the resistance becomes zero at 104K. Also, the oxide superconductor powder was investigated through an X-ray diffraction and a high-resolution transmission electron microscope, and it was insured that main phase of the oxide superconductor had the composition of (Pb 0.5 Cu 0.5 ) Sr 2 Ca 2 Cu 3 O 9+z . X-ray diffraction pattern of the oxide superconductor powder is shown in FIG. 4. In FIGS. 5A and 5B, there are shown electron beam diffraction patterns of the oxide superconductor. FIG. 5A shows a diffraction pattern irradiating a electron beam from [001] direction, and FIG. 5B shows a pattern irradiating from [110] direction. From these diffraction pattern, the crystal structure unit cell is found to be a tetragonal system having a-axial length of 0.382nm and c-axial length of 1.55nm. FIG. 6 shows the crystal structure of the oxide superconductor of Example 1. In this crystal structure, the infinite layer portion corresponds to the case n = 3, and oxygens at the rock salt structure based portion are partially lost, not shown in FIG. 6, so that the average valence of Cu becomes between +2.05 - +2.25, where superconductivity are exhibited. (Example 2) The resulted precursors SrCuO 2 and Ca 2 CuO 3 in FIG. 1 as well as raw material powders of PbO and CdO having a purity of 99.9% or more are mixed at a molar ratio of Pb : Cd : Sr : Ca : Cu = 0.5 : 0.5 : 2 : 2 : 3 to obtain a mixed powder. The mixed powder was heat-treated under superhigh pressure to obtain the oxide superconductor in a similar manner as Example 1. Temperature dependencies as to magnetic susceptibility of the obtained oxide superconductor were investigated in a similar manner Example 1. The result is shown in FIG. 7. As will be understood from FIG. 7, the temperature which shows diamagnetism (Tc) was 121K. Also, volume fraction at 5K was estimated to be 32% from FC data, which was relatively high value. Further, temperature dependencies as to electric resistivity of the obtained oxide superconductor were investigated in a similar manner as Example 1, and the result is shown in FIG. 8. As will be understood from FIG. 8, the electric resistivity decreases as the temperature decreases, just as is the metal, and at approximately 121K decreases rapidly, and then the resistance becomes zero at 109K. Further, the oxide superconductor powder was investigated through the X-ray diffraction and the high-resolution transmission electron microscope, and it was insured that main phase of the oxide superconductor had the composition of (Pb 0.5 Cd 0.5 ) Sr 2 Ca 2 Cu 3 O 9+z . And, the infinite layer portion corresponds to n = 3 similarly to Example 1. (Example 3) By varying preparation conditions (pressure, temperature), various oxide superconductors were made which compositions of (Pb 1-x-y M x (A1) y )(A2) 2 (A3) n-1 (Cu) n (O) 2n+3+z , i. e., A1, A2 and A3 element, number of infinite layer, and x and y value, were changed variously. Concerning to each oxide superconductor, the critical temperature Tc and volume fraction were investigated. The result as well as preparation conditions and the composition are shown in the following Table 1-4. And, Table 1 and 2 show the case that the element M is Cu, and Table 3 and 4 show the case that the element M is Cd. As will be apparent from Table 1-4, all the oxide superconductors which made under the pressure and temperature condition prescribed according to the present invention have high Tc value of 100K or more. On the contrary, oxide superconductors made beyond the range of the pressure and temperature condition prescribed according to the present invention (sample no. 4, 8, 9, 25, 29, 47, 51, 52, 63, 67) were all non-superconductive phase. And, when Cd is used as the element M, there is a trend that the oxide superconductors having higher Tc and volume fraction than that used Cu are obtained. C-axial length of the oxide superconductor according to the present invention changes in response to the infinite layer number n. The c-axial length is expressed by the equation; c=0.53 + 0.34n(nm), and 1.55nm is equivalent to n=3. Since the c-axial length of the infinite layer structure unit cell is approximately 0.34nm, the c-axial length becomes c=1.55 + 0.34(nm) in case the infinite layer number n is 4. In this case also, it was insured that the oxide superconductors had Tc value of 100K or more. Thus, the c-axial length becomes longer as the infinite layer number increases. Further, the a-axial length is approximately constant at 0.382±0.01(nm). As mentioned above, the oxide superconductor according to the present invention may be expressed by the composition formula of (Pb 1-x-y M x (A1) y )(A2) 2 (A3) n-1 (Cu) n (O) 2n+3+z ; has a crystal structure stacking both rock salt structure based portions, each of which has a structure that an atoms layer having 0.5-1.5 oxygen atoms, in case the total atoms number of Pb, M and A1 is one, and an atoms layer having one or less oxygen atoms per one A2 atom are stacked, and infinite layer structure portions, each of which has a structure that an atoms layer having two oxygen atoms per one Cu atom and an atoms layer of A3 atoms only, are stacked; and exhibits Tc value of 100K or more. Therefore, liquid nitrogen may be used as its coolant. Also, the oxide superconductor according to the present invention have advantages that neither Tl or Hg being extremely hard to handle nor rare earth elements which are maldistributed and requires high purifying cost are contained. Furthermore, the process for preparing the above oxide superconductor according to the present invention may efficiently obtain the oxide superconductor having the above characteristics, since the raw material of oxide superconductor is heat-treated at a temperature of 800-1200°C under superhigh pressure of 2-8GPa to prepare the above oxide superconductor.

Claims: An oxide superconductor characterized by: having the composition formula (Pb 1-x-y M x (A1) y )(A2) 2 (A3) n-1 (Cu) n (O) 2n+3+z (wherein 0 ≤ x ≤ 0.6, 0 ≤ y ≤ 0.6, x+y ≤ 0.6, n denotes integers of 1 or more, -0.6 ≤ z ≤ 0.5, M denotes Cu or Cd, and A1, A2 and A3 denote at least one element of Ba, Sr, and Ca, respectively); and having a crystal structure stacking rock salt structure based portions and infinite layer structure portions, wherein said rock salt structure based portion has a structure that an atoms layer having 0.5-1.5 oxygen atoms, in case the total atom number of Pb, M and A1 is one, and an atoms layer having one or less oxygen atoms per one A2 atom, are stacked, and said infinite layer structure portion has a structure which atoms layer having two oxygen atoms per one Cu atom and an atoms layer of A3 atoms only, are stacked. An oxide superconductor according to claim 1, characterized in that said M is Cu, said A2 is Sr or Ba, said A3 is Ca, and n is integers of 2-4. An oxide superconductor according to claim 1, characterized in that said M is Cd, said A2 is Sr or Ba, said A3 is Ca, and n is integers of 2-4. An oxide superconductor according to claim 1, characterized in that an average valence of Cu ion ranges + 2.05 - +2.25. A method for manufacturing an oxide superconductor comprising the steps of heating-treating a raw material of an oxide superconductor at 800-1200°C under superhigh pressure of 2-8 GPA, characterized by comprising the step of preparing an oxide superconductor having the composition formula (PB 1-x-y M x (A1) y )(A2) 2 (A3) n-1 (Cu) n (O) 2n+3+z (wherein 0 ≤ x ≤ 0.6, 0 ≤ y ≤ 0.6, x+y ≤ 0.6, n denotes integers of 1 or more, -0.6 ≤ z ≤ 0.5, M denotes Cu or Cd, and A1, A2 and A3 denote at lease one element of Ba, Sr, and Ca, respectively) and having a crystal structure stacking rock salt structure based portions and infinite layer structure portions, wherein said rock salt structure based portion has a structure that an atoms layer having 0.5-1.5 oxygen atoms, in case the total atom number of Pb, M and A1 is one, and an atoms layer having one or less oxygen atoms per one A2 atom, are stacked and said infinite layer structure portion has a structure which an atoms layer having two oxygen atoms per one Cu atom and an atoms layer of A3 atoms only, are stacked. A method according to claim 5, characterized in that said M is Cu, said A2 is Sr or Ba, said A3 is Ca, and n is integers of 2-4. A method according to claim 5, characterized in that said M is Cd, said A2 is Sr or Ba, said A3 is Ca, and n is integers of 2-4. A method according to claim 5, characterized in that an average valence of Cu ion ranges +2.05 - +2.25.

Inventors: ADACHI SEIJI, TAMURA TOSHIYUKI, WU XIAO-JING, YAMAUCHI HISAO, ADACHI, SEIJI, TAMURA, TOSHIYUKI, WU, XIAO-JING, YAMAUCHI, HISAO, ADACHI, SEIJI, C/O SUPERCONDUCTIVITY RES. LAB., Tamura, Toshiyuki, c/o Superconductivity Res. Lab., Wu, Xiao-Jing, c/o Superconductivity Res. Lab., YAMAUCHI, HISAO, C/O SUPERCONDUCTIVITY RES. LAB.
Applicants: FURUKAWA ELECTRIC CO LTD, INT SUPERCONDUCTIVITY TECH, MATSUSHITA ELECTRIC IND CO LTD, INTERNATIONAL SUPERCONDUCTIVITY TECHNOLOGY CENTER, MATSUSHITA ELECTRIC INDUSTRIAL CO., LTD., THE FURUKAWA ELECTRIC CO., LTD.
Application year: 1995
Main classification: C04B35
IPC codes: C04B35, C01G1, H01B13, C01G21