Method of preparing metal oxide crystal

Abstract: In a method of preparing a crystal of a metal oxide, the growth of said crystal is performed in a liquid phase having a composition which is different from the metal oxide and which comprises components constituting the metal oxide. The liquid phase contains a solid phase, at a position different from the position at which the crystal of the metal oxide is to grow, and having a composition different from that of the metal oxide and which supplys components constituting the metal oxide to the liquid phase.

Description: This invention relates to a method of preparing a metal oxide crystal and, more specifically, to a method for the growth of a metal oxide crystal. Known methods for the preparation of superconducting metal oxides of a Y-series 123 structure include a flux method, a melt solidification method, a flowing zone (FZ) method, a unidirectional solidification method and a crystal pulling method. In the flux method, the growth of the metal oxide crystal is performed by lowering the temperature of a relatively homogeneous solution. An improvement of the flux method is suggested in Physica C, 190 , 64 (1991), in which peritectic reaction and diffusion in a liquid phase are utilized. The flux method has a problem because it is impossible to continuously grow the desired crystal to a large crystal. The melt solidification method is a method including the steps of heating a desired metal oxide or a precursor thereof at above the peritectic temperature thereof to form a mixed phase in which a solid phase formed by decomposition and a liquid phase coexist, and then cooling the mixed phase to form the desired crystal of the metal oxide (Jpn. J. Appl. Phys. 28 , 1125 (1989); Advances in Superconductivity II, Springer-Verlead, Tokyo, p. 285). While a relatively large crystal can be obtained by this method, it is impossible to continuously prepare the desired crystal without inclusions. In the unidirectional solidification method, a small width portion of a raw material in the form of a bar is heated above its peritectic temperature while displacing the heating portion from one end thereof to the other end. While this method permits the continuous preparation of the crystal, it is difficult to form a single phase because the composition of the heating portion varies with the displacement of the high temperature liquefied region. In particular, the desired crystal is apt to be contaminated by a different crystal phase produced by the peritectic reaction. The FZ method includes heating a small width portion of a raw material in the form of a bar at a higher temperature than that adopted in the above unidirectional solidification method while displacing the heating portion from one end thereof to the other end. This method has a problem because it is difficult to prepare a large crystal. Further, this method is not applicable to the preparation of a Y-series 123 metal oxide crystal, because at such a high temperature, the fused mass begins flowing. The crystal pulling method includes the steps of providing a solution of the desired crystals in a suitable solvent, immersing a bar of a seed crystal, having a lower temperature than that of the solution, in the solution to form deposits of the desired crystal on the immersed region of the bar, and gradually pulling up the bar to permit the crystal to grow. With this method, however, it is difficult to form a Y-series 123 metal oxide crystal. Further, this method, which uses the primary crystallization temperature, has a problem because the solution has a high viscosity. The present invention has been made with the foregoing problems of the conventional methods in view. In accordance with the present invention there is provided a method of preparing a crystal of a metal oxide, characterized in that the growth of the crystal is performed in a liquid phase having a composition which is different from the metal oxide and which comprises components constituting the metal oxide, that the liquid phase contains a solid phase at a position different from the position at which the crystal of the metal oxide grows, and that the solid phase has a composition different from that of the metal oxide and supplies components constituting the metal oxide to the liquid phase. The method of the present invention can be applied to the preparation of various metal oxides including those whose crystals are decomposed to solids and liquids when fused. Both single crystals and polycrystals can be prepared. Superconductive oxides are particularly preferably produced according to the method of the present invention. Illustrative of suitable metal oxides to be produced by the method of the present invention are Y-series 123 metal oxides, especially superconductive Y-series metal oxides. The term "Y-series 123 metal oxide" used in the present specification and claims is intended to refer to a metal oxide having the formula: AB 2 Cu 3 O 7-x wherein A stands for a rare earth element such as Y, B stands for an alkaline earth metal such as Ba and x is a number of 0-1. The solid phase to be used in the method of the present invention is preferably a Y-series 211 metal oxide. The term "Y-series 211 metal oxide" used in the present specification and claims is intended to refer to a metal oxide having the formula: A 2 BCuO 5-x wherein A, B and x have the same meaning as above. When, for example, YBa 2 Cu 3 O 7-x , of Y-series 123 metal oxide is to be prepared using Y 2 BaCuO 5 of Y-series 211 metal oxide as the solid phase, the mixed phase (solid phase-containing liquid phase) is preferably obtained by blending the Y-series 211 metal oxide with at least two members selected from a Cu oxide, a Ba oxide and a BaCu oxide to form an admixture, the admixture being subsequently heated at a temperature sufficient to precipitate the primary crystals of the Y-series 123 metal oxide, preferably at a temperature above the incongruent melting point of YBa 2 Cu 3 O 7-x crystal. In this case, it is necessary that about 3 moles of Ba and about 5 moles of Cu should be present per mole of the Y-series 211 metal oxide, in order to form the Y-series 123 metal oxide by reaction thereof. However, Cu can be present in an excess amount. Thus, the preferred molar ratio of Ba:Cu for the preparation of the liquid phase is 3:5 to 3:8. In the mixed phase, the amount of the liquid phase, i.e. the total amount of the at least two members selected from the Cu oxide, Ba oxide and CuBa oxide, is preferably 2-10 parts by weight per part by weight of the solid phase, i.e. the Y-series 211 metal oxide. In one preferred embodiment, the growth of the crystal is performed using a seed crystal. The seed crystal is generally an axially elongated body, such as a bar, and is slowly pulled up at a rate of 0.01-10 mm per hour. In the case of the production of a Y-series 123 metal oxide crystal, the pulling speed is preferably 0.1-0.3 mm per hour. The pulling is preferably carried out while rotating the seed crystal bar about the axis thereof at such a rotational speed and in such a rotational direction as to permit the growth of the crystal. As the seed crystal, it is preferred that a metal oxide having corrosion resistance to the liquid phase be used. In the case of the production of a Y-series 123 metal oxide crystal, a bar formed of SmBa 2 CU 3 O 7-x crystal, magnesia single crystal and YBa 2 Cu 3 O 7-x crystal is suitably used. The use of SmBa 2 Cu 3 O 7-x seed crystal is particularly preferred for reasons of its crystal structure and high decomposition melting temperature. In the foregoing descriptions with regard to the solid phase, liquid phase and seed crystal, it goes without saying that Y and Ba can be partly or entirely replaced by another rare earth element and another alkaline earth metal, respectively. Preferred embodiments of the present invention will be described below with reference to the accompanying drawings, in which: Fig. 1 is a cross-sectional, elevational view diagrammatically showing an apparatus useful for carrying out the method of the present invention; Fig. 2 is a schematic illustration of a grown crystal obtained in Example 1 according to the method of the present invention; and Fig. 3 is a schematic illustration of a grown crystal obtained in Example 2 according to the method of the present invention. In practicing the invention, a solid phase-containing liquid phase is first prepared. Thus, raw materials are placed in a crucible formed of a material which does not react with the raw materials and which does not adversely affect the properties of the desired metal oxide crystal, such as yttria, magnesia, alumina or stabilized zirconia. The contents in the crucible are then heated at a temperature sufficient to precipitate a crystal of the desired metal oxide. The heating may be effected in any known manner such as with a high frequency induction heating oven or an electric oven. A seed crystal is then contacted with the liquid phase while controlling the temperature of the liquid phase so as to cause the crystal of the desired metal oxide to deposit on the seed crystal. For reasons of stable growth of the desired crystal, it is preferred that such a temperature gradient that the temperature increases in the direction along which the crystal grows be formed in at least the vicinity of the crystal growth boundary. The growth of the crystal is accelerated by maintaining the surfaces at which the crystal of the metal oxide grows at a temperature lower than a temperature at which the crystal of the metal oxide is equilibriously stable. By using a single crystal as the seed crystal and by controlling the crystal orientation of the seed crystal, it is possible to permit the crystal of the metal oxide to grow in a specific direction of the crystal axis. In the initial stage of the crystal growth, the crystals obtained often have crystal faces whose orientations differ from each other. In such a case, it is possible to selectively grow the specific crystal face by removing undesirable crystals to retain only the desired crystal. It is preferred that the seed crystal bar be axially pulled up while rotating same about the axis thereof. The rotational speed is preferably 10-200 revolutions per minute. In this case, it is also preferred that the rotational speed of the seed crystal bar is reduced with the growth of the crystal of the metal oxide. When the crystal size is not able to be directly measured, the rotational speed of the seed crystal bar may be controlled according to the weight of the crystal of the metal oxide which is monitored with a load cell. It is preferred that the rotational direction of the elongated body is alternately reversed at suitable intervals, since a single crystal free of contamination with impurities or other defects is obtainable. The switching interval varies with the rotational speed and the like conditions but, generally, the rotational direction is shifted at intervals of 5 minutes to 5 hours, preferably 30 minute to 2 hours. The interval may be changed during the growth of the crystal, if desired. It is important that the surface at which the crystal of the desired metal oxide grows should be spaced apart from the solid phase contained in the liquid phase, since otherwise the solid phase would be caught by the growing crystal. For the purpose of preventing the contact of the solid phase with the growing crystal, the use of a partition wall therebetween or selection of raw materials so as to create a large difference in density between the smaller density liquid phase and the larger density solid phase is recommendable. Preferably, the position at which the crystal of the metal oxide grows is a top surface of the liquid phase and wherein the solid phase is present at the bottom of the liquid phase. In this case, the position at which the crystal of the metal oxide grows is preferably maintained at a temperature not higher than that of the solid phase. The growth of the crystal of the metal oxide may be performed under any atmosphere such as air. However, the use of an atmosphere with a low oxygen partial pressure is preferable since it is easy to prepare a large single crystal of a tetragonal system. The low oxygen partial pressure atmosphere may be obtained, for example, by feeding a stream of argon to the oven within which the crystal growth is performed. The grown crystal product is desirably taken out of the oven very slowly and carefully so as not to damage the product by thermal shock. The following examples will further illustrate the present invention. Example 1 YBa 2 Cu 3 O 7-x crystal of Y-series 123 metal oxide was prepared using an apparatus illustrated in Fig. 1. Designated as 1 is a yttria crucible having an inside diameter of 30 mm and a height of 50 mm. The crucible 1 is disposed in a high frequency induction oven having an induction coil 7 with a platinum susceptor 6 being interposed between the crucible 1 and the coil 7. Provided in the bottom of the crucible 1 is a solid phase (precipitate) 2 of Y 2 BaCuO 5 (Y-series 211 metal oxide) above which a liquid phase 3 is formed. The reference numeral 5 designates a seed crystal bar of SmBa 2 Cu 3 O 7-x crystal. Crystal 4 of the Y-series 123 metal oxide is being grown at the end portion of the seed crystal bar 5. In commencing the production of the Y-series 123 metal oxide crystal, barium carbonate and copper oxide were mixed with each other with a molar ratio of Ba/Cu of 3:5. This mixture was calcined at 880 °C for 40 hours to obtain a calcined mixture. In the crucible 1 was placed 1 part by weight of Y 2 BaCuO 5 serving as the solid phase 2, to which was then added 4 parts by weight of the above calcined mixture as a precursor of the liquid phase 3. The crucible 1 was placed inside of the platinum susceptor 6 and the contents in the crucible was heated to about 1,000 °C by energization of the induction coil 6 so that there was formed the liquid phase 3 above the solid phase 2. In this case, the heating was performed so as to establish a temperature gradient of 10 °C/cm in the vertical direction of the crucible with an upper portion thereof having a lower temperature than a lower portion thereof. While keeping the solid phase 2 in the precipitated state and maintaining the surface of the liquid phase 3 at a temperature in the range of 1,010-960 °C, the seed crystal bar 5 was immersed in the liquid phase 3 and then continuously pulled up at a rate of 0.2 mm per hour while being rotated at 90 revolutions per minute (rpm), whereby the crystal of YBa 2 Cu 3 O 7-x was allowed to deposit on the seed crystal bar and to grow, as schematically shown in Fig. 1. Thereafter, the seed crystal bar 5 having the grown crystal was taken out of the crucible. This product was as illustrated in Fig. 2. The grown crystal of YBa 2 Cu 3 O 7-x is designated as 21. Example 2 Example 1 was repeated in the same manner as described except that the rotational speed of the seed crystal bar was changed with the growth of the crystal, which was monitored by a load cell, and that the process was performed under a stream of argon. Thus, the rotational speed was initially maintained at 120 rpm for 33 hours from the start of the crystal growth. At this stage, the growing crystal face was a square with a side length of 3 mm. Thereafter, the rotational speed was reduced to 100 rpm and maintained at that speed for 20 hours, whereby the growing crystal face was enlarged to a square of a side length of 5 mm. The rotational speed was then further reduced to 80 rpm and maintained at that speed for 10 hours, to obtain a crystal whose growing face was a square with a side length of 7 mm. The resulting single crystal was taken out of the oven at a speed of 12 mm per hour. Throughout the crystal growth, the seed crystal bar was pulled up at a rate of 0.2 mm per hour and the rotational direction was alternately inverted at intervals of 1 hour. The YBa 2 Cu 3 O 7-x thus prepared was a large single crystal of a tetragonal system and had a shape as shown in Fig. 3, in which the reference numerals 31 and 32 designate the YBa 2 Cu 3 O 7-x single crystal and SmBa 2 Cu 3 O 7-x seed crystal bar, respectively. Examples 3 and 4 Example 2 was performed in the same manner as described except that the SmBa 2 Cu 3 O 7-x seed crystal bar was replaced by a MgO single crystal bar (Example 3) and a YBa 2 Cu 3 O 7-x single crystal bar (Example 4), thereby to obtain crystals of YBa 2 Cu 3 O 7-x similar to that obtained in Example 2.

Claims: A method of preparing a crystal of a metal oxide, characterized in that the growth of said crystal is performed in a liquid phase having a composition which is different from said metal oxide and which comprises components constituting said metal oxide, said liquid phase containing a solid phase at a position different from the position at which the crystal of said metal oxide grows, said solid phase having a composition different from that of said metal oxide and supplying components constituting said metal oxide to said liquid phase. A method as set forth in claim 1, wherein the growth of the crystal of said metal oxide is performed using an axially elongated body of a seed crystal while rotating said elongated body about the axis thereof. A method as set forth in claim 2, wherein said seed crystal has corrosion resistance to said liquid phase. A method as set forth in claim 2 or claim 3, wherein said seed crystal is selected from SmBa 2 Cu 3 O 7-x crystal, magnesia single crystal and YBa 2 Cu 3 O 7-x crystal. A method as set forth in any one of claims 2-4, wherein said elongated body is axially moved upward during the growth of the crystal of said metal oxide and wherein the orientation of said seed crystal relative to the axis of said elongated body is controlled. A method as set forth in any one of Claims 2-5, wherein the rotational direction of said elongated body is periodically reversed. A method as set forth in any one of Claims 2-6, wherein the rotational speed of said elongated body is reduced with the growth of the crystal of said metal oxide. A method as set forth in any one of Claims 2-7, wherein the rotational speed of said elongated body is controlled according to the weight of the crystal of said metal oxide which is monitored with a load cell. A method as set forth in any preceding claim, wherein the crystal of said metal oxide is decomposed to solid and liquid when fused. A method as set forth in any preceding claim, wherein said metal oxide is a superconductive metal oxide. A method as set forth in any preceding claim, wherein said superconductive metal oxide is a Y-series 123 metal oxide. A method as set forth in Claim 11, wherein said solid phase is a Y-series 211 metal oxide. A method as set forth in Claim 12, wherein said solid phase-containing liquid phase is obtained by blending said Y-series 211 metal oxide with at least two members selected from a Cu oxide, a Ba oxide and a BaCu oxide to form an admixture, said admixture being heated at a temperature sufficient to precipitate a crystal of said Y-series 123 metal oxide. A method as set forth in Claim 13, wherein the ratio of the weight of said Y-series 211 metal oxide to the total weight of said at least two members is 1:2 to 10:1. A method as set forth in any preceding claim, wherein said position at which the crystal of said metal oxide grows is maintained at a temperature not higher than that of said solid phase. A method as set forth in any preceding claim, wherein said position at which the crystal of said metal oxide grows is a top surface of said liquid phase and wherein said solid phase is present at the bottom of the liquid phase. A method as set forth in any preceding claim, wherein said position at which the crystal of said metal oxide grows is maintained at such a temperature that the crystal of said metal oxide is kept stable. A method as set forth in any preceding claim, wherein the growth of the crystal of said metal oxide is performed in an oven which is maintained in an atmosphere having a low oxygen partial pressure so as to obtain a single crystal of a tetragonal system. A method as set forth in any preceding claim, wherein the crystal of said metal oxide is a single crystal or a polycrystal.

Inventors: ISHIGE KENGO, IZUMI TERUO, NAKAMURA YUICHI, OHTSU KANSHI, SHIOHARA YUH, TAGAMI MINORU, TANAKA SHOJI, YAMADA YASUJI, ISHIGE, KENGO, IZUMI, TERUO, NAKAMURA, YUICHI, OHTSU, KANSHI, SHIOHARA, YUH, TAGAMI, MINORU, TANAKA, SHOJI, YAMADA, YASUJI, Ishige, Kengo, c/o Superconductivity Res. Lab., Izumi, Teruo, c/o Superconductivity Res. Lab. of, Nakamura, Yuichi, c/o Superconductivity Res. Lab., Ohtsu, Kanshi, c/o Superconductivity Res. Lab. of, Shiohara, Yuh, c/o Superconductivity Res. Lab., Tagami, Minoru, c/o Superconductivity Res. Lab., TANAKA, SHOJI, C/O SUPERCONDUCTIVITY RES. LAB., Yamada, Yasuji, c/o Superconductivity Res. Lab. of
Applicants: ASAHI GLASS CO LTD, INT SUPERCONDUCTIVITY TECH, ISHIKAWAJIMA HARIMA HEAVY IND, KYUSHU ELECTRIC POWER, RAILWAY TECHNICAL RES INST, SUMITOMO METAL IND, ASAHI GLASS COMPANY LTD., INTERNATIONAL SUPERCONDUCTIVITY TECHNOLOGY CENTER, ISHIKAWAJIMA-HARIMA JUKOGYO KABUSHIKI KAISHA, KYUSHU ELECTRIC POWER CO., INC, RAILWAY TECHNICAL RESEARCH INSTITUTE, SUMITOMO METAL INDUSTRIES, LTD.
Application year: 1993
Main classification: C30B15
IPC codes: C30B15, C01G3, C30B29, H01L39, C01G1, H01B13