Patent Publication Number: US-6219901-B1

Title: Oxide superconductor precursors

Description:
This is a divisional of copending application Ser. No. 08/102,561 filed on Aug. 5,1993. 
     This application is a continuation-in-part application of co-pending application U.S. Ser. No. 07/881,675 filed May 12, 1992, entitled “Strongly-Linked Oxide Superconductor and a Method of Its Manufacture”. 
    
    
     FIELD OF THE INVENTION 
     The present invention relates to novel precursor materials for the preparation of high T c  oxide superconductors and superconducting composites. The invention further relates to the use of the novel precursor materials in the preparation of oxide superconductors and superconducting composites. 
     BACKGROUND OF THE INVENTION 
     The discovery of high transition temperature superconducting oxides over the past six years triggered an international race to develop high temperature superconducting (HTS) materials. For many applications, in particular electrical power generation, the required HTS materials must operate at high current densities in magnetic fields, and possess adequate robustness, flexibility and critical current tolerance of strain. The stringent performance requirements of the HTS materials has demanded the development of new processing materials and techniques which impart improved superconducting and mechanical properties to the material. 
     Any improvements in material or process that can beneficially affect the superconducting and mechanical properties of the HTS material are highly desirable. 
     SUMMARY OF THE INVENTION 
     The object of the present invention is to provide novel composite materials useful in the preparation of oxide superconducting composites. The novel composite of the present invention exhibits reduced segregation of copper into the matrix metal phase and preferential growth of oxide superconductor phase, both of which have a beneficial effect on the superconducting properties of the oxide superconducting composite. 
     It is another object of the present invention, to provide a method for preparing composite materials as precursors and intermediates to oxide superconducting composites. 
     It is yet another object of the present invention to provide a method for preparing an oxide superconductor composite to improve the superconducting characteristics of the composite. 
     In one aspect of the invention, a composite of the invention includes a primary alloy phase containing constituent elements of a desired oxide superconductor and a secondary phase containing copper. The secondary phase is supported by the primary alloy phase. 
     “Alloy” is used herein in the conventional sense to mean an intimate mixture of phases or solid solution of two or more elements. An alloy can be prepared by milling, cooling from a melt or any other conventional means. 
     In a preferred embodiment, the constituent elements of the primary alloy phase and the copper of the secondary phase, in combination, are present in an amount sufficient to form the desired oxide superconductor. Excess or deficiency of a particular element is defined by comparison to the ideal copper cation stoichiometry of the desired oxide superconductor. In some embodiments, the elements may be present in the stoichiometric proportions of the desired oxide superconductor. In other embodiments, there may be a stoichiometric excess or deficiency of any constituent element to accommodate the processing conditions used to form the desired oxide superconductor. In preferred embodiments, copper is present in stoichiometric excess in the range of 10% to 30% with respect to the ideal copper cation stoichiometry of the desired oxide superconductor. 
     In preferred embodiments, a noble metal may also be present in the primary alloy phase and/or the secondary phase. Noble metals may include, among others, silver, gold, palladium and platinum. 
     The primary alloy phase supports the secondary phase. In one preferred embodiment, the support may be accomplished by disposing the secondary phase within the primary alloy phase. By “disposed within”, as that term is used herein, it is meant that the secondary phase is embedded within the matrix material or substantially completely surrounded by the matrix material. The secondary phase preferably is in the form of a wire, rod, foil or particle. 
     In another preferred embodiment, the support is accomplished by contactingly surrounding at least a portion of an outer periphery of the primary alloy phase with the secondary phase. By “contactingly surrounding”, as that term is used within, it is meant that at least one surface of the secondary phase is in contact with an outer periphery of the primary alloy phase. The secondary phase preferably is in the form of a wire, rod, foil or particle. 
     In one embodiment of the present invention, substantially all of the constituent element, copper, is in the secondary phase. In another embodiment of the present invention, a portion of the constituent element, copper, is the secondary phase and the balance of the copper needed to form an oxide superconductor is in the primary alloy phase. 
     In another aspect of the present invention, a composite of the invention includes a primary alloy phase containing constituent elements of a desired oxide superconductor, a secondary phase containing copper, the secondary phase supported by the primary alloy phase, and a matrix material for supporting a primary alloy phase and secondary phase disposed therein. 
     By “matrix”, as that term is used herein, it is meant a material or homogeneous mixture of materials which supports and/or binds a substance disposed within or around the matrix. 
     In preferred embodiments, the matrix material is preferably a noble metal. The primary alloy phase and the secondary phase may also additionally comprise a noble metal. A noble metal is a material that is inert to chemical reaction and oxidation under the processing conditions used to form an oxide superconductor. Silver is a preferred noble metal. 
     In yet another aspect of the invention, an oxide composite includes a primary oxide phase comprising a sub-oxide of a desired oxide superconductor and a secondary silver phase disposed therein. By “sub-oxide”, as that term is used herein, it is meant one or more oxides selected from the group consisting of simple, binary and higher oxides of the constituent elements of a desired oxide superconductor. 
     In yet another aspect of the invention, an oxide composite includes a primary oxide phase comprising a sub-oxide of a desired oxide superconductor, a secondary silver phase disposed therein and a matrix material for supporting a primary oxide phase and secondary silver phase therein. 
     In yet another aspect of the invention, an oxide superconductor is prepared by oxidation of composite including a primary alloy phase comprising an alloy of constituent elements of a desired oxide superconductor and a secondary phase comprising copper, the secondary phase supported by the primary alloy phase. 
     In yet another aspect of the invention, an oxide superconductor is prepared by oxidizing a composite including a primary alloy phase comprising an alloy of constituent elements of a desired oxide superconductor, a secondary phase comprising copper, the secondary phase supported by the primary alloy phase and a matrix material for supporting the primary alloy phase and secondary phase disposed therein. 
     In yet another aspect of the invention, a metal oxide/silver composite is prepared. A composite comprising a primary alloy phase comprising the constituent elements of a desired oxide superconductor and silver and a secondary phase comprising copper, the secondary phase supported by the primary alloy phase is prepared. The composite is oxidized under conditions sufficient to oxidize the constituent elements of a desired oxide superconductor and under conditions which promote the diffusion of the silver of the primary alloy phase into the region of the secondary phase and under conditions to promote the diffuision of the copper of the secondary phase into the region of the primary alloy phase, so that a pure silver phase occupying substantially the secondary phase is formed. 
     In another aspect of the invention, an oxide superconductor is prepared. A composite is prepared which includes a primary alloy phase comprising silver and the constituent elements of a desired oxide superconductor and a secondary phase comprising copper. The secondary phase supported by the primary alloy phase. The composite is oxidized under conditions sufficient to form an oxide superconductor. 
     In another aspect of the invention, an oxide superconductor is prepared. A composite is prepared which includes a primary alloy phase comprising silver and the constituent elements of a desired oxide superconductor, a secondary phase comprising copper and a matrix material. The secondary phase is supported by the primary alloy phase and the matrix material supports the primary alloy phase and the secondary phase disposed therein. The composite is oxidized under conditions sufficient to form an oxide superconductor. 
    
    
     BRIEF DESCRIPTION OF THE DRAWING 
     In the Drawing, 
     FIGS.  1 ( a )-( d ) are cross-sectional views of several embodiments of the composite of the present invention; 
     FIG. 2 is a flow diagram of the preparation of the composite of FIG. 1; 
     FIG. 3 is an optical photomicrograph of a cross-section of one embodiment of the present invention; 
     FIG. 4 is an optical photomicrograph of a cross-section of one embodiment of the present invention; 
     FIG. 5 is an optical photomicrograph of a cross-section of a metal oxide composite prepared from a precursor composite of the prior art; and 
     FIG. 6 is a graph of critical current density v. texturing strain, illustrating an aspect of the method of the present invention. 
    
    
     DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT 
     The composite can take on many different geometric forms. For example, the primary alloy may be in the shape of a tape or a wire and the secondary form can be wires coaxially aligned within the primary alloy phase as shown in FIG.  1 ( a ). A cross-sectional view of a composite  10  transverse to its longest dimension shows aligned copper wires  12  (secondary phase) disposed within a primary alloy phase  14 . The copper wires  12  are coaxially aligned within the composite  10  and are of small dimension. There may be between 1 and 1000 copper wires disposed within the primary alloy phase. 
     The secondary phase may also be in the form of a foil which surrounds an inner wire or tape of primary alloy phase. FIG.  1 ( b ) shows a cross-sectional view of a composite  20  transverse to its longest dimension, in which a copper foil  22  (secondary phase) surrounds a primary alloy phase  14 . The copper foil  22  surrounds at least a portion of an outer surface  24  of the primary alloy phase. The foil  22  is sufficiently contacted to the alloy surface to permit subsequent reaction between the phases, if desired. Alternatively, a foil  22  of the secondary phase could be rolled with a sheet  26  of primary alloy phase  14  to give a helices configuration as shown in FIG.  1 ( c ). 
     The secondary phase may be in the form of particles disposed throughout the primary alloy phase. FIG.  1 ( d ) shows a cross-sectional view of a composite  30  which contains copper particles  32  (secondary phase) disposed within a primary alloy phase  14 . The copper particles  32  have a particle size in the range of 100 μm or less and occupy an atomic fraction in the range of 0.05 to 0.65. The atomic fraction is dependent upon the desired oxide superconductor. 
     The primary alloy phase  14  may contain constituent elements of any oxide superconductor. For instance, yttrium (Y) and barium (Ba) for the Y—Ba—Cu—O family of oxide superconductors; bismuth (Bi), lead (Pb), strontium (Sr) and calcium (Ca) for the Bi—Sr—Ca—Cu—O family of oxide superconductors; thallium (Tl), Pb, Sr and Ca for the Tl—Sr—Ca—Cu—O family of oxide superconductors; and mercury (Hg), Pb, Sr and Ca for the Hg—Sr—Ca—Cu—O family of oxide superconductors. It may be preferable to have copper in stoichiometric excess in the range of 10% to 30% with respect to the cation stoichiometry of the desired oxide superconductor. Variations in the proportions and constituents of the elements comprising each oxide superconductor, as are well known in the art, are also within the scope and spirit of the invention. 
     The composite of the present invention can be prepared in any form, such as tapes, rods, ingots or sheets. The secondary phase may be evenly distributed throughout the primary alloy phase so that reaction time for the formation of the oxide superconductor can be minimized. Alternatively, the secondary phase may be grouped in a particular region, such as near the outer periphery of the primary phase or located in the center of the primary phase. 
     It is within the scope of the present invention for the constituent elements of the desired oxide superconductor to contain some, but not all, of the copper which makes up the desired oxide superconductor. The balance of the copper is found in the secondary phase. It is also within the scope of the invention for the alloy matrix  14  to contain additional elements other than the constituent elements of an oxide superconductor. For example, the alloy may contain a noble metal, such as silver. 
     In yet another embodiment, a matrix material supports the primary alloy phase and the secondary phase which is supported therein. It is contemplated that a plurality of primary alloy phase/secondary phase regions can be disposed within the matrix material. Matrix material include, but are in no way limited to, noble metals such as silver, gold, palladium and platinum. 
     The composites of the present invention may be prepared in the following manner. 
     EXAMPLE 1 
     A primary alloy phase is prepared by blending powders of the constituent elements of the desired oxide superconductor and silver. The blended powders are copper-deficient or may contain no copper, if desired. Silver comprises 70-80% vol of the blend. The resulting blend is then mechanically alloyed, as described, for example, in U.S. Pat. Nos. 4,962,084 and 5,034,373, herein incorporated by reference. The mechanically alloyed powder is fed into an extrusion die through which a plurality of copper wires is concurrently introduced. A composite wire is obtained having a primary alloy phase consisting of silver and copper-deficient, constituent elements of the desired oxide superconductor and a secondary phase of copper wires running coaxially along the length of the extruded wire. 
     EXAMPLE 2 
     A primary alloy phase is prepared, as described in Example 1 or using any conventional alloying technique, containing the elements Pb, Bi, Sr, Ca, Cu and Ag in the atomic ratio of 0.34:1.74:1.92:2.05:3.07:0 to 0.34:1.74:1.92:2.05:3.07:14.5. The alloy is heated to a temperature in the range of 450 to 700° C. in an inert atmosphere for 10 seconds or more to obtain a composite having copper regions disposed within the primary alloy phase. 
     EXAMPLE 3 
     The process diagram in FIG. 2 illustrates the main elements of the process. The process begins with the mechanical alloying of metallic elements to form a homogeneous copper-deficient alloy powder  40  (primary alloy phase), as described above for Example 1. The alloy powder  40  is packed into a silver or copper can  42  (secondary phase) containing either a copper foil lining or strands of copper wire. FIG. 2 illustrates the process for an embodiment utilizing copper wires coaxially aligned within the silver or copper can  42 . The silver or copper can  42  containing the powder alloy  40  and copper  42  is then sealed and extruded into a hexagonal rod  46 . Cut pieces of the rod are stacked into a multi-rod bundle that is again packed into a silver or copper can  47  and extruded into a hexagonal rod. This process is repeated several times. In the final step, the can is extruded through a die  48  into a rectangular or round wire  46 . Tapes between 200 and 3,000,000 filaments can be readily made using multiple stacking. FIG. 3 is an optical photomicrograph showing a cross-section of a multifilament wire  51  of the invention containing a primary alloy phase  52 , a secondary copper phase  53  and a silver matrix material  54 . 
     Another embodiment of the present invention includes an oxide composite which includes a primary oxide phase comprised of fully dense suboxides of a desired oxide superconductor and a secondary silver phase disposed within the primary oxide phase. In another embodiment, the composite includes a primary oxide phase and a secondary silver phase and a matrix material for supporting the primary oxide phase and secondary silver phase disposed therein. FIG. 4 is an optical photomicrograph of a cross-section of a wire  60  of this embodiment of the present invention having a primary alloy phase  62 , a secondary silver phase  64  and a matrix material (here, silver)  66 . Note that the composite is fully dense, that is, there are no visible porosity (gaps or voids) at grain boundaries (within phases) or at interfaces between phases. These microstructures are typical of composites prepared from oxidation of a precursor alloy and can be compared with composites prepared from powders of the sub-oxides, which are typically much less dense and have porosity within the phase and at phase interfaces. 
     The embodiment of FIG. 4 can be prepared as follows. 
     EXAMPLE 4 
     A multifilament composite is prepared according to Example 3. The composite is then oxidized under the conditions of 320 to 420° C. with oxygen pressures of 800 to 2000 psi (O 2 ) for 200 to 600 h, in particular, 420° C. for more than 200 h at 1600 psi (O 2 ). The process occurs as follows. Calcium and strontium are quickly oxidized to the corresponding metal oxides; bismuth and lead do not alloy significantly with copper and hence there is no significant migration of Ca, Pb, Sr or Bi into the copper secondary phase. The copper migrates towards the higher oxygen activity, i.e., out of the secondary phase and into the region of the primary alloy phase, thereby creating a void in the secondary phase. The void is displaced by silver due to the very high surface energy associated with the void. 
     EXAMPLE 5 
     A multifilament composite is prepared according to Example 3, with the following changes. The alloy powder  40  is alloyed with sufficient amount of copper to form a desired oxide superconductor and the copper wires  42  are replaced by silver wires. The assembled composite is oxidized under conditions sufficient to oxidize the alloy powder to suboxides. Typical oxidation conditions are 320° C. to 420° C. at 800 to 2000 PSi O 2  for 200 to 600 h. 
     The precursor composite and the oxide composite of the present invention have several advantages. The composites exhibit reduced diffusion of copper into the matrix material upon oxidation of the composites to form an oxide superconductor. This can be demonstrated by comparison of the oxide composites in FIGS. 4 and 5. FIG. 4 represents an oxide composite which has been prepared from the oxidation according to the method of the invention of a precursor composite having a primary oxide phase supporting a copper wires (secondary phase) in a silver matrix FIG. 5 represents an oxide composite which has been prepared from a precursor composite without a secondary copper phase (copper is present in the primary alloy phase). Intrusion of the metal oxides, typically mostly copper oxide, although oxides of other metals can also form, into the silver matrix occurs to varying extent in both composites. However, metal oxide intrusion (which appears as fine tendrils  68  of metal oxide) is severely restricted in FIG. 4 compared to the two-dimensional front  70  of intruded metal oxide shown in FIG.  5 . The two-dimensional “halo” of metal oxide surrounding the sub-oxide phase of the composite represents a much larger proportion of the constituent elements that the linear tendrils of FIG.  4 . The oxide intrusion into the silver matrix remains upon further heat treatment to form an oxide superconductor. 
     Further, the concentration of silver in the secondary phase of the oxide composites of the present invention provides an interface capable of preferential growth of the oxide superconductor. There has been suggestions in the prior art that silver/oxide interfaces promote the oriented growth of oxide superconductor grains, leading to texturing and improved critical transport characteristics (see, Feng et al. in  Appl. Phys. Lett ., 1993, hereby incorporated by reference). 
     The compositions disclosed above can be used in the preparation of oxide superconducting composites. The composition may include the superconducting oxide phase including, but not limited to Bi 2−y Pb 4 Sr 2 Ca 2 Cu 3+z O x , where x is sufficient to provide T c ≧90 K, and 0≦y≦0.6 and 0≦z≦1.0, Bi 2−y Pb 4 Sr 2 Ca 2 Cu 3+z O x , where x is sufficient to provide T c ≧77 K, and 0≦y≦0.6 and 0≦z≦0.3 and A n Ba 2n Cu a(3n+1) O x , where A=(Re 1−y Ca y ), n=(1, 2, 3 . . . ∞), a=(1.0-1.3) and 0≦y≦0.2 and x is sufficient to provide T c ≧65 K Re here is a rare earth or yttrium. It may be preferable to have excess copper in the oxide superconductor in the range of 10 to 30% excess based on the ideal copper cation stoichiometry of the oxide superconductor. Such compositions include, but are not limited to compositions having the following cation stoichiometries: Bi 2−y Pb y Sr 2 Ca 2 Cu 3.5-3.7 ; Bi 2−y Pb y Sr 2 Ca 1 Cu 2.3-2.6 ; and A 1 Ba 2 Cu 4.6-5.2 . 
     The preparation of oxide superconducting composites using the composites and oxide composites of the present invention are described. 
     EXAMPLE 6 
     A primary alloy phase is prepared by blending the elements of Pb, Bi, Sr, Ca and Ag in the atomic ratio of 0.34:1.74:1.92:2.05:14.5. The resulting blend is then mechanically alloyed, as described, for example, in U.S. Pat. No. 5,034,373, herein incorporated by reference. 
     Thirty three fine copper wires (0.5 mm in diameter) are coaxially arranged within a silver billet 0.615 inches OD×0.552 inches ID×5.0 inches long (matrix material) and the alloyed powder containing Pb, Bi, Sr, Ca and Ag is packed into the billet and around the copper wires. The material within the silver billet has a final composition of 0.34 Pb:1.74 Bi:1.92 Sr:2.05 Ca:3.07 Cu:14.5 Ag. The silver billet was extruded through a die to provide a composite wire having a silver matrix and plurality of primary alloy phase regions, each region supporting a secondary phase of copper wires. 
     A plurality of wires prepared as described in the preceding paragraph are bundled together and coextruded to obtain a multifilament wire. An optical photomicrograph of a typical multifilament wire prepared from the composite of the present invention is shown in FIG.  3 . 
     The multifilament wire is then oxidized at 420° C. for 288 h in 100 atm oxygen. Under these oxidizing conditions, the copper diffuses out of the secondary phase and into the primary alloy phase. Concurrently, the silver of the primary alloy phase migrates towards the regions of the secondary phase to be concentrated in the secondary phase, thereby forming a metal oxide/silver composite. The oxide composite sample is further heat treated in 0.075 atm O 2  for a total time of 7 to 15 h at a temperature of 780° C. with intermediate deformations through rolling of 75% to 82% strain. The temperature was increased to 831° C. for a further 10 to 60 h in 0.075 atm O 2  and then deformed a further 16 to 20% strain for a total strain in the range of 80 to 85%. A final heat treatment at 830° C. for 60 h and then 811° C. for 180 h provides a Bi 2−y Pb y Sr 2 Ca 2 Cu 3 O x  oxide superconductor, where y is 0≦y≦0.6. The critical current densities of samples prepared according to this method are given in Table 1. 
     EXAMPLE 7 
     A precursor alloy is prepared and processed in the manner described in Example 6 above, with the following exception. Copper is mechanically alloyed with the other constituent elements of the oxide superconductor. No copper secondary phase is used. The elements of Pb, Bi, Sr, Ca, Cu and Ag in the atomic ratio of 0.34:1.74:1.92:2.05:3.07:14.5. The resulting blend is then mechanically alloyed. The precursor alloy is processed as described in Example 1. A Bi 2−y Pb y Sr 2 Ca 2 Cu 3 O x  oxide superconductor is obtained, where 0≦y≦0.6. The critical current densities of wire samples prepared according to this method are given in Table 1. 
     EXAMPLE 8 
     A precursor alloy is prepared by blending the elements of Pb, Bi, Sr, Ca and Ag in the atomic ratio of 0.34:1.74:1.92:2.05:14.5. Thirty three fine copper wires (0.5 mm in diameter) are coaxially arranged within a silver billet the alloyed powder containing Pb, Bi, Sr, Ca and Ag is packed into the billet and around the copper wires. The material within the silver billet has a final composition of 0.34 Pb:1.74 Bi:1.92 Sr:2.05 Ca:3.70 Cu:14.5 Ag. The precursor composite is processed and thermally treated as described in Example 6. The critical current densities of wire samples prepared according to this method are given in Table 1. 
     EXAMPLE 9 
     A precursor alloy is prepared by blending the elements of Pb, Bi, Sr, Ca, Cu and Ag in the atomic ratio of 0.34:1.74:1.92:2.05:3.52:14.5. The alloyed powder containing Pb, Bi, Sr, Ca, Cu and Ag is packed into a silver billet. The material within the silver billet has a final composition of 0.34 Pb:1.74 Bi:1.92 Sr:2.05 Ca:3.52 Cu:14.5 Ag. The precursor composite is processed and thermally treated as described in Example 6. The critical current densities of wire samples prepared according to this method are given in Table 1. 
     
       
         
           
               
             
               
                 TABLE 1 
               
             
            
               
                   
               
               
                 Comparative Critical Current Densities for Examples 6-9 
               
            
           
           
               
               
               
               
            
               
                   
                 total 
                 t (hour) a   
                   
               
            
           
           
               
               
               
               
               
               
               
            
               
                   
                 No. 
                 strain (%) 
                 1 
                 2 
                 3 
                 J c  (A/cm 2 )  
               
               
                   
                   
               
               
                   
                 6 
                 80 
                 20 
                 60 
                 180 
                 8770 
               
               
                   
                 6 
                 85 
                 20 
                 60 
                 180 
                 9160 
               
               
                   
                 7 
                 80 
                 20 
                 60 
                 180 
                 5100 
               
               
                   
                 7 
                 85 
                 20 
                 60 
                 180 
                 6440 
               
               
                   
                 8 
                 85 
                 20 
                 60 
                 120 
                 7160 
               
               
                   
                 8 
                 85 
                 20 
                 60 
                 120 
                 5410 
               
               
                   
                 9 
                 85 
                 20 
                 60 
                 120 
                 3830  
               
               
                   
                   
               
               
                   
                   a 1 = heat treatment at 831° C. followed by deformation; 2 = heat treatment at 831° C. 3 = heat treatment at 811° C. followed.  
               
            
           
         
       
     
     Table 1 clearly shows that excess copper levels in the oxide superconductor composite, and the presence of a secondary copper phase contribute to higher critical current densities in the sample. What is further clear is that these process parameters are process independent in that the parameters, alone and in combination, improve J c . Further visual examination of the oxide superconducting samples prepared from the composite of the present invention show reduced segregation of copper into the silver matrix. This is supported by comparison of oxide composites of FIGS. 3 and 4. 
     The nature of the deformation and anneal conditions can also have an effect on the final superconducting properties of the composite as shown in the example below. 
     EXAMPLE 10 
     A multifilamentary composite wire is prepared as follows. 
     A precursor alloy is prepared by blending the elements of Pb, Bi, Sr, Ca and Ag in the atomic ratio of 0.34:1.74:1.92:2.05:14.5. The resulting blend is then mechanically alloyed, as described, in Examples above. The alloyed powder containing Pb, Bi, Sr, Ca and Ag is packed into the billet and around the copper wires. The material within the silver billet has a final composition of 0.34 Pb:1.74 Bi:1.92 Sr:2.05 Ca:3.80 Cu:14.5 Ag. The silver billet was extruded through a die to provide a composite wire with a hexagonal cross-section. A plurality of wires thus prepared are bundled together and coextruded to obtain a multifilament wire and extruded to provide a precursor tape or wire. 
     Following precursor tape manufacture, the alloy filaments are oxidized to form fine grained, dispersed sub-oxide phases by diffusing oxygen through the silver matrix, exploiting silver&#39;s high permeability to atomic oxygen. 
     Following oxidation, the precursor oxide filaments are reacted by thermal treatment(s) to form highly aspected, superconducting oxide grains with the c-directions orthogonal to their large surfaces. The reaction path for Bi 2−y Pb y Sr 2 Ca 2 Cu 3+z O x  (Bi-2223) involves the well known initial formation of Bi-2212 and “0011” reactant (compositionally CaCuO 2 ) from the suboxide phases, reaction (1), followed by conversion to Bi-2223, reactions (2), via an intercalation mechanism that reproduces the texture of the Bi 2−y Pb y Sr 1 Ca 2 Cu 2+z O x  (Bi-2212) phase assemblage in the Bi-2223 phase assemblage formed. 
     
       
         (2−y)BiO 1.5 +PbO+2SrO+2CaO+3CuO→Bi 2−y Pb y Sr 2 CaCu 2 O x +CaCuO 2  Bi 2−y Pb y Sr 2 CaCu 2 O x +CaCuO 2 →Bi 2−y Pb y Sr 2 Ca 2 CU 3 O x   
       
     
     Both the Bi-2212 and Bi-2223 phases are textured by deformation processes such as rolling or uniaxial pressing. The oxide composite sample is further heat treated in 0.075 atm O 2  for a total time of 7 to 15 h at a temperature of 780° C. with intermediate deformations through rolling of 75% to 85% strain. The temperature was increased to 830° C. for a further 20 h in 0.075 atm O 2  and then deformed a further 16 to 25% strain and heated treated for 60 hours at 830° C. in 7.5% O 2  and then finally heat treated at 811° C. for 180 h. 
     The deformation used to texture the superconducting phase also fractures the oxides into discrete particles. The superconducting phase is therefore sintered by a final thermal treatment to form the interconnected structure inside each filament required for supercurrent transport through the multifilament composite. 
     The oxide Jc dependencies on text strain are illustrated in FIG. 5, for three thermal processing variations. It is evident that Jc typically increases with increasing texturing strain to a maximum in the range of 82% to 89% strain, followed by a rapid decrease. The increase in Jc as strain increases is due to improved texture, and the decrease is due to damage in the filaments from strain localization. 
     Thermal process variations improve Jc by enhancing texturing strain efficacy as seen by the overall upward shift of the Jc v. strain relations for three thermal process variations. The optimal texturing strains in the range of 82 to 89% are small in comparison to the total strain (&gt;99%) required to fabricate a multifilament tape. These total texturing strains are achieved by one or more deformation step wherein a deformation step is one or more applications of force to be the material between thermal treatments. The bulk of the deformation required for making high Jc multifilament wires in the process can therefore be done with the precursor filaments in the ductile metallic state, rather than in the more brittle oxide state. 
     The transport properties attained with high-filament-count precursor composite processed tapes are presented in Table 2. 
     
       
         
           
               
             
               
                 TABLE 2 
               
             
            
               
                   
               
               
                 Transport properties of 259 filament, Bi-2223 - silver 
               
               
                 composite tapes made from precursors composites 
               
            
           
           
               
               
               
            
               
                 Length 
                 Temperature 
                 Oxide Jc 1   
               
               
                 (m) 
                 (K.) 
                 (A/cm 2 )  
               
               
                   
               
            
           
           
               
               
               
            
               
                 0.03 
                 77 
                 17,700 
               
               
                 0.03 
                 4.2 
                 71,000 
               
               
                 8 
                 77 
                 8,000  
               
               
                   
               
               
                   1 Jc is measured with the 1 μV/cm criterion (DC) by the four point probe method.  
               
            
           
         
       
     
     The 77 K short length oxide Jc level in Table 2 exceeds the best levels reported for any other filament count process. Further more, these tapes were textured by scalable processes such as rolling, allowing extension of the process to long lengths. 
     Other embodiments of the invention will be apparent to those skilled in the art from a consideration of the specification or practice of the invention disclosed herein. It is intended that the specification an examples be considered as exemplary only, with the true scope and spirit of the invention being indicated by the following claims.