USH1399H - Process for transforming pure Y2 BaCuO5 into a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions - Google Patents

Process for transforming pure Y2 BaCuO5 into a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions Download PDF

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USH1399H
USH1399H US08/086,583 US8658393A USH1399H US H1399 H USH1399 H US H1399H US 8658393 A US8658393 A US 8658393A US H1399 H USH1399 H US H1399H
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Gregory Kozlowski
William E. Endres
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United States Department of the Air Force
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    • H—ELECTRICITY
    • H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10N60/00—Superconducting devices
    • H10N60/01—Manufacture or treatment
    • H10N60/0268—Manufacture or treatment of devices comprising copper oxide

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  • the present invention relates generally to ceramic superconductors, and more particularly to a process for easily making a superconducting matrix of YBa 2 Cu 3 O 7-x with fine and homogeneously dispersed Y 2 BaCuO 5 inclusions.
  • a rare earth oxide superconductor such as YBa 2 Cu 3 O 7-x (also referred to as a 1-2-3 phase; both nomenclatures are used interchangeably in this description) has a predetermined direction in the crystals of the 1-2-3 phase in which an electric current readily flows. The current tends to hardly flow among crystals aligned in different directions. Further, the grain boundaries can act either as poor superconductors or as insulating layers. Because of this, none of the polycrystal rare earth superconductors exhibit a high critical current density.
  • the prior art has attempted a variety of methods for preparing a crystal structure where crystals of the 1-2-3 phase are aligned and grain boundaries are suppressed.
  • the conventional method has been to solidify a melt of ceramic material in one direction under a temperature gradient to obtain an aligned ceramic material having a density higher than that obtainable by a sintering method.
  • the 1-2-3 phase melts incongruently at its peritectic temperature (the temperature at which part of the material is in a solid phase and part in a liquid phase) of about 1015° C.
  • Y 2 BaCuO 5 crystals also referred to as a 2-1-1 phase; both nomenclatures are used interchangeably in this description
  • a liquid phase rich in barium and copper Accordingly, when this melt is cooled, a dense 1-2-3 material is formed with 2-1-1 inclusions. These inclusions are large in size and inhomogeneously distributed, which prevents good current density.
  • the present state of the art for producing 1-2-3 material with fine 2-1-1 inclusions involves mixing 1-2-3 powders with 2-1-1 powders or platinum.
  • the powders are heated to >1200° C. and splat-quenched.
  • Splat-quenching is cooling by quickly squeezing the material between two copper plates.
  • the material is ground into powders and pressed into pellets.
  • the pellets then undergo melt-processing where they are heated to a temperature where a melt or liquid begins to form. This temperature will generally be slightly above the peritectic point. This temperature is held for a short period (about 12 minutes), after which the pellets are quickly cooled to just below the peritectic point and further cooled at a slow rate.
  • the material After slow-cooling to about 925° C., the material is cooled to room temperature at about 240° /hour. Finally, the pellets undergo an oxygenation process for 24 hours at 450° C. Unfortunately, the whole process is very laborious, typically taking 4-5 days to complete.
  • the fine and homogeneously dispersed 2-1-1 inclusions provide increased flux pinning for higher current densities.
  • the present invention provides a process for easily making a superconducting matrix of YBa 2 Cu 3 O 7-x with fine and homogeneously dispersed Y 2 BaCuO 5 inclusions.
  • the unique discovery of the present invention is that, first, a sample of YBa 2 Cu 3 O 7-x touching a sample of Y 2 BaCuO 5 will, when heated to above its peritectic temperature, melt and flow by capillary action into the Y 2 BaCuO 5 sample and react to form the desired superconducting matrix of YBa 2 Cu 3 O 7-x with fine and homogeneously dispersed Y 2 BaCuO 5 inclusions and, second, that the temperature to which the samples are heated and the time duration they are held at that temperature during the capillary flow step are critical to successfully producing small inclusions under one micron.
  • the present invention is directed to a method for making a ceramic superconductor, comprising the steps of providing a supply of Y 2 BaCuO 5 , providing a supply of YBa 2 Cu 3 O 7-x , placing the two supplies in contact with each other, next placing the two supplies into a furnace at a temperature above the peritectic temperature of YBa 2 Cu 3 O 7-x for a period of less than about fifteen minutes so that the supply of YBa 2 Cu 3 O 7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action into the supply of Y 2 BaCuO 5 , and next cooling the resulting material to a temperature lower than the peritectic temperature of YBa 2 Cu 3 O 7-x and holding that temperature for a period of time to promote growth of YBa 2 Cu 3 O 7-x .
  • the starting density of the supply of Y 2 BaCuO 5 may be in the range of 35-43% of its theoretical maximum density.
  • the present invention is also directed to substituting a supply of BaCuO 2 +CuO for the YBa 2 Cu 3 O 7-x and the two supplies first heated up to just above the eutectic temperature of the BaCuO 2 +CuO and holding that temperature for a period of time sufficient for congruent melting of the BaCuO 2 +CuO, and, second, heating the two supplies up to a temperature of just above the peritectic temperature of YBa 2 Cu 3 O 7-x to ensure complete melting and so that the resulting melt begins to be absorbed by capillary action into the supply of Y 2 BaCuO 5 .
  • the cooling step for this process may comprise quickly cooling the resulting material to the peritectic temperature of YBa 2 Cu 3 O 7-x , then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours.
  • the cooling step may also comprise quickly cooling the resulting material to about 960° C. and holding that temperature for a period of about twenty-four hours.
  • the present invention is further directed to substituting Y 2 O 3 for the Y 2 BaCuO 5 .
  • the present invention is yet further directed to a method for making a ceramic superconductor, comprising the steps of providing a supply of Y 2 BaCuO 5 , mixing into the supply of Y 2 BaCuO 5 an amount by weight of the combined supplies of 5 to 30 percent of YBa 2 Cu 3 O 7-x , next placing the combined supplies of Y 2 BaCuO 5 and YBa 2 Cu 3 O 7-x into a furnace at a temperature above the peritectic temperature of YBa 2 Cu 3 O 7-x for a period of less than about fifteen minutes so that the supply of YBa 2 Cu 3 O 7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action throughout the Y 2 BaCuO 5 , and next cooling the resulting material to a temperature lower than the peritectic temperature of YBa 2 Cu 3 O 7-x and holding that temperature for a period of time to promote growth of YBa 2 Cu 3 O 7-x .
  • BaCuO 2 +CuO may be substituted for the YBa 2 Cu 3 O 7-x and the two supplies, first, slowly heated to just above the eutectic temperature of the BaCuO 2 +CuO and then held at that temperature for a period of time sufficient for congruent melting of the BaCuO 2 +CuO and, second, the two supplied then heated up to a temperature of just above the peritectic temperature of YBa 2 Cu 3 O 7-x to ensure complete melting and so that the resulting melt begins to be absorbed by capillary action into the supply of Y 2 BaCuO 5 .
  • the invention is still further directed to a method for making a ceramic superconductor, comprising the steps of providing a supply of RE 2 BaCuO 5 , wherein RE is defined as at least one member selected from the group consisting of Y, La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb and Lu, providing a supply of REBa 2 Cu 3 O 7-x , placing the two supplies in contact with each other, next placing the two supplies into a furnace at a temperature above the peritectic temperature of the REBa 2 Cu 3 O 7-x for a period of less than about fifteen minutes so that the supply of REBa 2 Cu 3 O 7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action into the supply of RE 2 BaCuO 5 , and next cooling the resulting material to a temperature lower than the peritectic temperature of REBa 2 Cu 3 O 7-x and holding that temperatures for a period of time to promote growth of REBa 2 Cu 3 O 7
  • Cooling the resulting material after melting may comprise quickly cooling the resulting material to the peritectic temperature of YBa 2 Cu 3 O 7-x , then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours. Cooling the resulting material after melting may also comprise quickly cooling the resulting material to about 960° C. and then holding that temperature for a period of about twenty-four hours.
  • 2-1-1 and 1-2-3 material are made by compacting powders of the materials into desired shapes, such as disks or bars. The samples are then sintered at 940° C. for 24 hours. This sintering step is not necessary, but results in a final material that better maintains its physical shape. After sintering, the 2-1-1 and 1-2-3 samples are placed together so that they touch, such as by placing the 1-2-3 sample on top of the 2-1-1 sample. The combined sample is then inserted inside a furnace or oven at about 1100° C., which is above the peritectic temperature (about 1015°) of 1-2-3, and held for about 12 minutes. It is critical that the holding period be no longer than about 15 minutes.
  • the combined sample is then quickly cooled to 1015° C. (the peritectic temperature of 1-2-3) and then slowly cooled to 960° C., held for 24 or more hours, then allowed to cool to room temperature.
  • the liquid that results from the 1-2-3 that melts above 1015° C. is primarily BaCuO 2 and CuO and flows by capillary action into the 2-1-1 sample.
  • the resulting liquid reacts with the 2-1-1 sample, transforming it into a superconducting 1-2-3 matrix with fine and homogeneously dispersed 2-1-1 inclusions according to the following reaction.
  • the first alternative cooling step after a rapid drop (typically as fast as the furnace will allow, about 3 minutes for an 85° C. drop) to the peritectic temperature of the 1-2-3, the combined sample was slowly cooled (typically about 1° C./hour) to 960° C., held for about 24 or more hours to promote the growth of the 1-2-3 phase in the original 2-1-1 sample, and then allowed to cool to room temperature.
  • the second alternative cooling step the combined sample was quickly cooled to 960° C. from 1100° C., then held for about 24 or more hours to promote the growth of the 1-2-3 phase in the original 2-1-1 sample, and then allowed to cool to room temperature.
  • the starting density of the 2-1-1 sample can be chosen to achieve a final preferred weight percent of 2-1-1 inside the 1-2-3 matrix of 20-30%. This range of final weight percentages achieves the best flux pinning and highest current densities. To achieve this final resulting range of weight percentages, the starting density of the 2-1-1 sample should be in the range of 35-43% of its theoretical maximum density. A more dense starting material provides a greater capillary force, but less volume for absorbing the liquid. A less dense starting material provides a greater volume for absorbing liquid, but a lower capillary force. The range of 35-43% will produce the best results.
  • 1-2-3 and 2-1-1 material may not be required.
  • a small amount (5-30% by weight) of 1-2-3 material could be mixed with 2-1-1 material in powder form and there would still be a capillary flow of liquid into the 2-1-1 material and transformation of the 2-1-1 to 1-2-3.
  • a starting sample of 1-2-3 material is not necessarily needed.
  • the starting sample could instead be composed of BaCuO 2 +CuO.
  • BaCuO 2 and CuO can be obtained in powdered form and pressed and sintered into pellets the same as YBa 2 Cu 3 O 7-x .
  • the starting sample would need to be first heated (at about 200° C./hour) to just above the eutectic temperature of the BaCuO 2 +CuO, about 920° C., for a period of time sufficient for congruent melting of the BaCuO 2 +CuO, about 18 minutes, then heated at a rate of about 75° C./hour to just above the peritectic temperature of YBa 2 Cu 3 O 7-x , about 1035° C., held for 1 minute, followed by a cooling step of quickly cooling to 960° C., holding for 24 hours or more, and then allowing to cool to room temperature.
  • An alternative cooling step would be to quickly drop from the 1035° C. temperature to 1015° C., then slowly cool to 960° C., hold that temperature for 24 or more hours, and then allow to cool to room temperature.
  • the Y 2 BaCuO 5 can be replaced with Y 2 O 3 to absorb and react with the resulting liquid from the melted 1-2-3 (or melted BaCuO 2 and CuO) to form a new 1-2-3 matrix.
  • the disclosed method need not be limited to yttrium-based superconductors, but may be extended to include all rare earth oxide superconductors.
  • the equations for the samples are written as REBa 2 Cu 3 O 7-x and as RE 2 BaCuO 5 , where RE is defined as at least one member selected from the group consisting of Y, La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb and Lu.
  • x in O 7-x is very small.
  • the value of the subscript for oxygen should preferably be exactly 7 to achieve a perfect stoichiometric ratio, but that is very difficult to achieve and those with skill in the art have long recognized the practice of using a value of 7-x to indicate a value preferably very close to 7.
  • a "y”, a delta ( ⁇ ) or a gamma ( ⁇ ) is sometimes used in place of x. Occasionally, a solitary "y" is used for the amount of oxygen in place of "7-y".
  • the disclosed new method for making a superconducting matrix of YBa 2 Cu 3 O 7-x with fine and homogeneously dispersed Y 2 BaCuO 5 inclusions successfully demonstrates the value of using capillary absorption to achieve a good homogeneous distribution of one material in another, even where the material being absorbed is not the final material for which a good homogeneous distribution is desired but will, after further processing, become the matrix itself, and the value of precise control of the processing times and temperatures to achieve a final material having the best possible dimensions and other properties.
  • the disclosed method is specialized, its teachings will find application in other areas where homogeneous distribution of one material into another is difficult to achieve.

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Abstract

A new process for more easily making a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions smaller than one micron compacts powders of YBa2 Cu3 O7-x and Y2 BaCuO5 into samples which are first sintered for improved mechanical stability and then placed into contact with each other. The samples are placed into a furnace above the peritectic temperature of the YBa2 Cu3 O7-x and held at that temperature for less than about fifteen minutes so that the YBa2 Cu3 O7-x begins to melt and be absorbed by capillary action into the Y2 BaCuO5 sample. The combined sample is cooled to a temperature below the peritectic temperature by a variety of alternative cooling cycles where it is transformed by a reaction into a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5. BaCuO2 +CuO may be substituted for the YBa2 Cu3 O7-x and Y2 O.sub. 3 substituted for the Y2 BaCuO5 as starting components.

Description

RIGHTS OF THE GOVERNMENT
The invention described herein may be manufactured and used by or for the Government of the United States for all governmental purposes without the payment of any royalty.
BACKGROUND OF THE INVENTION
The present invention relates generally to ceramic superconductors, and more particularly to a process for easily making a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions.
As described in U.S. Pat. No. 5,084,436 to Morimoto et al., which is incorporated by reference, a rare earth oxide superconductor such as YBa2 Cu3 O7-x (also referred to as a 1-2-3 phase; both nomenclatures are used interchangeably in this description) has a predetermined direction in the crystals of the 1-2-3 phase in which an electric current readily flows. The current tends to hardly flow among crystals aligned in different directions. Further, the grain boundaries can act either as poor superconductors or as insulating layers. Because of this, none of the polycrystal rare earth superconductors exhibit a high critical current density.
As described in Morimoto et al., to obtain a material having a high critical current density, the prior art has attempted a variety of methods for preparing a crystal structure where crystals of the 1-2-3 phase are aligned and grain boundaries are suppressed. The conventional method has been to solidify a melt of ceramic material in one direction under a temperature gradient to obtain an aligned ceramic material having a density higher than that obtainable by a sintering method. Unfortunately, the 1-2-3 phase melts incongruently at its peritectic temperature (the temperature at which part of the material is in a solid phase and part in a liquid phase) of about 1015° C. to form Y2 BaCuO5 crystals (also referred to as a 2-1-1 phase; both nomenclatures are used interchangeably in this description) and a liquid phase rich in barium and copper. Accordingly, when this melt is cooled, a dense 1-2-3 material is formed with 2-1-1 inclusions. These inclusions are large in size and inhomogeneously distributed, which prevents good current density.
Morimoto et al. reported that although the 2-1-1 crystal particle inclusions show no superconductivity, they do not hinder the flow of electric current and give no substantial adverse effects to the superconducting properties as long as they are independent from each other. It has been since discovered that fine, homogeneously distributed, 2-1-1 inclusions actually help the superconducting material get good flux-pinning which results in higher current densities.
The present state of the art for producing 1-2-3 material with fine 2-1-1 inclusions involves mixing 1-2-3 powders with 2-1-1 powders or platinum. The powders are heated to >1200° C. and splat-quenched. Splat-quenching is cooling by quickly squeezing the material between two copper plates. After splat-quenching, the material is ground into powders and pressed into pellets. The pellets then undergo melt-processing where they are heated to a temperature where a melt or liquid begins to form. This temperature will generally be slightly above the peritectic point. This temperature is held for a short period (about 12 minutes), after which the pellets are quickly cooled to just below the peritectic point and further cooled at a slow rate. After slow-cooling to about 925° C., the material is cooled to room temperature at about 240° /hour. Finally, the pellets undergo an oxygenation process for 24 hours at 450° C. Unfortunately, the whole process is very laborious, typically taking 4-5 days to complete.
Thus it is seen that there is a need for an easier method for making 1-2-3 material with fine and homogeneously dispersed 2-1-1 inclusions.
It is, therefore, a principal object of the present invention to provide a method for easily making a superconducting matrix of YBa2 Cu3 O7-x (1-2-3) with fine and homogeneously dispersed Y2 BaCuO5 (2-1-1) inclusions. The fine and homogeneously dispersed 2-1-1 inclusions provide increased flux pinning for higher current densities.
It is a feature of the present invention that it avoids the splat-quench step of the prior art melt-processing procedure.
It is an advantage of the present invention that it can produce finely distributed 2-1-1 inclusions smaller than one micron.
It is another advantage of the present invention that it can be used to easily produce very large pieces of superconducting material, such as bars, with fine and homogeneous distribution of 2-1-1 inclusions. It can also be used to easily produce superconducting magnets, superconducting leads such as downleads for large magnets, superconducting generators, actuators and bearings.
These and other objects, features and advantages of the present invention will become apparent as the description of certain representative embodiments proceeds.
SUMMARY OF THE INVENTION
The present invention provides a process for easily making a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions. The unique discovery of the present invention is that, first, a sample of YBa2 Cu3 O7-x touching a sample of Y2 BaCuO5 will, when heated to above its peritectic temperature, melt and flow by capillary action into the Y2 BaCuO5 sample and react to form the desired superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions and, second, that the temperature to which the samples are heated and the time duration they are held at that temperature during the capillary flow step are critical to successfully producing small inclusions under one micron.
Accordingly, the present invention is directed to a method for making a ceramic superconductor, comprising the steps of providing a supply of Y2 BaCuO5, providing a supply of YBa2 Cu3 O7-x, placing the two supplies in contact with each other, next placing the two supplies into a furnace at a temperature above the peritectic temperature of YBa2 Cu3 O7-x for a period of less than about fifteen minutes so that the supply of YBa2 Cu3 O7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action into the supply of Y2 BaCuO5, and next cooling the resulting material to a temperature lower than the peritectic temperature of YBa2 Cu3 O7-x and holding that temperature for a period of time to promote growth of YBa2 Cu3 O7-x. The initial furnace temperature above the peritectic temperature may be about 1100° C. Cooling the resulting material after melting may comprise quickly cooling the resulting material to the peritectic temperature of YBa2 Cu3 O7-x, then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours. Cooling the resulting material after melting may also comprise quickly cooling the resulting material to about 960° C. and then holding that temperature for a period of about twenty-four hours. The starting density of the supply of Y2 BaCuO5 may be in the range of 35-43% of its theoretical maximum density.
The present invention is also directed to substituting a supply of BaCuO2 +CuO for the YBa2 Cu3 O7-x and the two supplies first heated up to just above the eutectic temperature of the BaCuO2 +CuO and holding that temperature for a period of time sufficient for congruent melting of the BaCuO2 +CuO, and, second, heating the two supplies up to a temperature of just above the peritectic temperature of YBa2 Cu3 O7-x to ensure complete melting and so that the resulting melt begins to be absorbed by capillary action into the supply of Y2 BaCuO5. The cooling step for this process may comprise quickly cooling the resulting material to the peritectic temperature of YBa2 Cu3 O7-x, then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours. The cooling step may also comprise quickly cooling the resulting material to about 960° C. and holding that temperature for a period of about twenty-four hours.
The present invention is further directed to substituting Y2 O3 for the Y2 BaCuO5.
The present invention is yet further directed to a method for making a ceramic superconductor, comprising the steps of providing a supply of Y2 BaCuO5, mixing into the supply of Y2 BaCuO5 an amount by weight of the combined supplies of 5 to 30 percent of YBa2 Cu3 O7-x, next placing the combined supplies of Y2 BaCuO5 and YBa2 Cu3 O7-x into a furnace at a temperature above the peritectic temperature of YBa2 Cu3 O7-x for a period of less than about fifteen minutes so that the supply of YBa2 Cu3 O7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action throughout the Y2 BaCuO5, and next cooling the resulting material to a temperature lower than the peritectic temperature of YBa2 Cu3 O7-x and holding that temperature for a period of time to promote growth of YBa2 Cu3 O7-x. BaCuO2 +CuO may be substituted for the YBa2 Cu3 O7-x and the two supplies, first, slowly heated to just above the eutectic temperature of the BaCuO2 +CuO and then held at that temperature for a period of time sufficient for congruent melting of the BaCuO2 +CuO and, second, the two supplied then heated up to a temperature of just above the peritectic temperature of YBa2 Cu3 O7-x to ensure complete melting and so that the resulting melt begins to be absorbed by capillary action into the supply of Y2 BaCuO5.
The invention is still further directed to a method for making a ceramic superconductor, comprising the steps of providing a supply of RE2 BaCuO5, wherein RE is defined as at least one member selected from the group consisting of Y, La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb and Lu, providing a supply of REBa2 Cu3 O7-x, placing the two supplies in contact with each other, next placing the two supplies into a furnace at a temperature above the peritectic temperature of the REBa2 Cu3 O7-x for a period of less than about fifteen minutes so that the supply of REBa2 Cu3 O7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action into the supply of RE2 BaCuO5, and next cooling the resulting material to a temperature lower than the peritectic temperature of REBa2 Cu3 O7-x and holding that temperatures for a period of time to promote growth of REBa2 Cu3 O7-x. Cooling the resulting material after melting may comprise quickly cooling the resulting material to the peritectic temperature of YBa2 Cu3 O7-x, then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours. Cooling the resulting material after melting may also comprise quickly cooling the resulting material to about 960° C. and then holding that temperature for a period of about twenty-four hours.
DETAILED DESCRIPTION
Separate samples, or supplies, of 2-1-1 and 1-2-3 material are made by compacting powders of the materials into desired shapes, such as disks or bars. The samples are then sintered at 940° C. for 24 hours. This sintering step is not necessary, but results in a final material that better maintains its physical shape. After sintering, the 2-1-1 and 1-2-3 samples are placed together so that they touch, such as by placing the 1-2-3 sample on top of the 2-1-1 sample. The combined sample is then inserted inside a furnace or oven at about 1100° C., which is above the peritectic temperature (about 1015°) of 1-2-3, and held for about 12 minutes. It is critical that the holding period be no longer than about 15 minutes. The combined sample is then quickly cooled to 1015° C. (the peritectic temperature of 1-2-3) and then slowly cooled to 960° C., held for 24 or more hours, then allowed to cool to room temperature. The liquid that results from the 1-2-3 that melts above 1015° C. is primarily BaCuO2 and CuO and flows by capillary action into the 2-1-1 sample. When the combined sample is cooled to a temperature below the peritectic temperature of the 1-2-3, the resulting liquid reacts with the 2-1-1 sample, transforming it into a superconducting 1-2-3 matrix with fine and homogeneously dispersed 2-1-1 inclusions according to the following reaction.
Y.sub.2 BaCuO.sub.5 +liquid(3BaCuO.sub.2 +2CuO)→αYBa.sub.2 Cu.sub.3 O.sub.7-x +βY.sub.2 BaCuO.sub.5 (inclusions)
where α and β values are dependent on the completeness of the reaction.
Two rates of cooling and final temperatures have worked well in practice. As described, in the first alternative cooling step, after a rapid drop (typically as fast as the furnace will allow, about 3 minutes for an 85° C. drop) to the peritectic temperature of the 1-2-3, the combined sample was slowly cooled (typically about 1° C./hour) to 960° C., held for about 24 or more hours to promote the growth of the 1-2-3 phase in the original 2-1-1 sample, and then allowed to cool to room temperature. In the second alternative cooling step, the combined sample was quickly cooled to 960° C. from 1100° C., then held for about 24 or more hours to promote the growth of the 1-2-3 phase in the original 2-1-1 sample, and then allowed to cool to room temperature.
The reason that it is critical that the holding period during which the two samples are heated above the peritectic temperature be no longer than about fifteen minutes is that longer times produce 2-1-1 inclusions 5 microns and larger in size. By limiting the temperature and time as described, resulting homogeneously distributed 2-1-1 inclusions smaller than one micron have been achieved.
The starting density of the 2-1-1 sample can be chosen to achieve a final preferred weight percent of 2-1-1 inside the 1-2-3 matrix of 20-30%. This range of final weight percentages achieves the best flux pinning and highest current densities. To achieve this final resulting range of weight percentages, the starting density of the 2-1-1 sample should be in the range of 35-43% of its theoretical maximum density. A more dense starting material provides a greater capillary force, but less volume for absorbing the liquid. A less dense starting material provides a greater volume for absorbing liquid, but a lower capillary force. The range of 35-43% will produce the best results.
Those with skill in the art of the invention will see that separate pieces of 1-2-3 and 2-1-1 material may not be required. For example, a small amount (5-30% by weight) of 1-2-3 material could be mixed with 2-1-1 material in powder form and there would still be a capillary flow of liquid into the 2-1-1 material and transformation of the 2-1-1 to 1-2-3.
Those will skill in the art of the invention will also see that smaller, experimental-size samples will quickly heat and quickly cool inside a furnace. Those with skill in the art will therefore see that the described temperatures may also be understood as applying to the internal temperatures of larger samples.
Those with skill in the art will further see that different elements, such as silver, can be added to the 2-1-1 sample at the beginning of the process to improve mechanical properties.
Those with skill in the art will still further see that a starting sample of 1-2-3 material is not necessarily needed. The starting sample could instead be composed of BaCuO2 +CuO. BaCuO2 and CuO can be obtained in powdered form and pressed and sintered into pellets the same as YBa2 Cu3 O7-x. The starting sample would need to be first heated (at about 200° C./hour) to just above the eutectic temperature of the BaCuO2 +CuO, about 920° C., for a period of time sufficient for congruent melting of the BaCuO2 +CuO, about 18 minutes, then heated at a rate of about 75° C./hour to just above the peritectic temperature of YBa2 Cu3 O7-x, about 1035° C., held for 1 minute, followed by a cooling step of quickly cooling to 960° C., holding for 24 hours or more, and then allowing to cool to room temperature. An alternative cooling step would be to quickly drop from the 1035° C. temperature to 1015° C., then slowly cool to 960° C., hold that temperature for 24 or more hours, and then allow to cool to room temperature.
Similarly, the Y2 BaCuO5 can be replaced with Y2 O3 to absorb and react with the resulting liquid from the melted 1-2-3 (or melted BaCuO2 and CuO) to form a new 1-2-3 matrix.
Those with skill in the art will yet further see that the disclosed method need not be limited to yttrium-based superconductors, but may be extended to include all rare earth oxide superconductors. In that case, the equations for the samples are written as REBa2 Cu3 O7-x and as RE2 BaCuO5, where RE is defined as at least one member selected from the group consisting of Y, La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb and Lu.
Those with skill in the art will recognize that the value of x in O7-x is very small. The value of the subscript for oxygen should preferably be exactly 7 to achieve a perfect stoichiometric ratio, but that is very difficult to achieve and those with skill in the art have long recognized the practice of using a value of 7-x to indicate a value preferably very close to 7. A "y", a delta (Δ) or a gamma (δ) is sometimes used in place of x. Occasionally, a solitary "y" is used for the amount of oxygen in place of "7-y".
The disclosed new method for making a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions successfully demonstrates the value of using capillary absorption to achieve a good homogeneous distribution of one material in another, even where the material being absorbed is not the final material for which a good homogeneous distribution is desired but will, after further processing, become the matrix itself, and the value of precise control of the processing times and temperatures to achieve a final material having the best possible dimensions and other properties. Although the disclosed method is specialized, its teachings will find application in other areas where homogeneous distribution of one material into another is difficult to achieve.
It is understood that various modifications to the invention as described may be made, as might occur to one with skill in the field of the invention, within the scope of the claims. Therefore, all embodiments contemplated have not been shown in complete detail. Other embodiments may be developed without departing from the spirit of the invention or from the scope of the claims.

Claims (9)

We claim:
1. A method for making a ceramic superconductor, comprising the steps of:
(a) providing a supply of Y2 BaCuO5 ;
(b) providing a supply of YBa2 Cu3 O7-x ;
(c) placing the two supplies in contact with each other;
(d) next placing the two supplies into a furnace at a temperature above the peritectic temperature of YBa2 Cu3 O7-x for a period of less than about fifteen minutes so that the supply of YBa2 Cu3 O7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action into the supply of Y2 BaCuO5 ; and,
(e) next cooling the resulting material to a temperature lower than the peritectic temperature of YBa2 Cu3 O7-x and holding that temperature for a period of time to promote growth of YBa2 Cu3 O7-x.
2. The method for making a ceramic superconductor according to claim 1, wherein the temperature above the peritectic temperature in step (d) is about 1100° C.
3. The method for making a ceramic superconductor according to claim 1, wherein step (e) is characterized as next quickly cooling the resulting material to the peritectic temperature of Y2 BaCuO7-x, then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours.
4. The method for making ceramic superconductor according to claim 1, wherein step (e) comprises quickly cooling the resulting material to about 960° C. and then holding that temperature for a period of about twenty-four hours.
5. The method for making a ceramic superconductor according to claim 1, wherein the starting density of the supply of Y2 BaCuO5 is in the range of 35-43% of its theoretical maximum density.
6. A method for making a ceramic superconductor, comprising the steps of:
(a) providing a supply of Y2 BaCuO5 ;
(b) mixing into the supply of Y2 BaCuO5 an amount by weight of the combined supplies of 5 to 30 percent of YBa2 Cu3 O7-x ;
(c) next placing the combined supplies of Y2 BaCuO5 and YBa2 Cu3 O7-x into a furnace at a temperature above the peritectic temperature of YBa2 Cu3 O7-x for a period of less than about fifteen minutes so that the supply of YBa2 Cu3 O7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action throughout the Y2 BaCuO5 ; and,
(e) next cooling the resulting material to a temperature lower than the peritectic temperature of YBa2 Cu3 O7-x and holding that temperature for a period of time to promote growth of YBa2 Cu3 O7-x.
7. A method for making a ceramic superconductor, comprising the steps of:
(a) providing a supply of RE2 BaCuO5, wherein RE is defined as at least one member selected from the group consisting of Y, La, Nd, Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb and Lu;
(b) providing a supply of REBa2 Cu3 O7-x ;
(c) placing the two supplies in contact with each other;
(d) next placing the two supplies into a furnace at a temperature above the peritectic temperature of REBa2 Cu3 O7-x for a period of less than about fifteen minutes so that the supply of REBa2 Cu3 O7-x begins to melt and so that the resulting melt begins to be absorbed by capillary action into the supply of RE2 BaCuO5 ; and,
(e) next cooling the resulting material to a temperature lower than the peritectic temperature of the REBa2 Cu3 O7-x and holding that temperature for a period of time to promote growth of REBa2 Cu3 O7-x.
8. The method for making a ceramic superconductor according to claim 7, wherein step (e) comprises next quickly cooling the resulting material to the peritectic temperature of REBa2 Cu3 O7-x, then slowly cooling the resulting material to 960° C. and then holding that temperature for a period of about twenty-four hours.
9. The method for making a ceramic superconductor according to claim 7, wherein step (e) comprises quickly cooling the resulting material to about 960° C. and then holding that temperature for a period of about twenty-four hours.
US08/086,583 1993-07-06 1993-07-06 Process for transforming pure Y2 BaCuO5 into a superconducting matrix of YBa2 Cu3 O7-x with fine and homogeneously dispersed Y2 BaCuO5 inclusions Abandoned USH1399H (en)

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