JPH07245211A - Superconducting magnet and its manufacture - Google Patents
Superconducting magnet and its manufactureInfo
- Publication number
- JPH07245211A JPH07245211A JP5828394A JP5828394A JPH07245211A JP H07245211 A JPH07245211 A JP H07245211A JP 5828394 A JP5828394 A JP 5828394A JP 5828394 A JP5828394 A JP 5828394A JP H07245211 A JPH07245211 A JP H07245211A
- Authority
- JP
- Japan
- Prior art keywords
- coil
- phase
- spiral
- superconducting magnet
- superconducting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/04—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing coils
- H01F41/048—Superconductive coils
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F6/00—Superconducting magnets; Superconducting coils
- H01F6/06—Coils, e.g. winding, insulating, terminating or casing arrangements therefor
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は実質的にＲＥＢａ2 Ｃｕ
3 Ｏ7-X （０≦ｘ≦０．３）（ＲＥはＹ，Ｌａ，Ｎｄ，
Ｓｍ，Ｅｕ，Ｇｄ，Ｄｙ，Ｈｏ，Ｅｒ，Ｔｍ，Ｙｂ，Ｌ
ｕのいずれかの元素またはこれらの組み合わせ）とＲＥ
2 ＢａＣｕＯ5 とからなる酸化物超伝導材料を用いた超
伝導マグネットおよびその製造方法に関するものであ
る。FIELD OF THE INVENTION The present invention is essentially of REBa 2 Cu.
3 O 7-X (0 ≦ x ≦ 0.3) (RE is Y, La, Nd,
Sm, Eu, Gd, Dy, Ho, Er, Tm, Yb, L
u any element or combination thereof) and RE
The present invention relates to a superconducting magnet using an oxide superconducting material composed of 2 BaCuO 5 and a method for manufacturing the same.
【０００２】[0002]
【従来の技術】現在超伝導マグネットとして実用化にな
っているのは、Ｎｂ−Ｔｉ系の超伝導線材をコイルに巻
いたものが中心である。他にはＮｂ3 ＳｎやＶ3 Ｇａ系
の超伝導材料が線材化され、コイル化することによって
高磁界用超伝導マグネットとして用いられている。これ
らの金属系超伝導マグネットは臨界温度が低いため液体
ヘリウム等により極低温に冷却する必要がある。超伝導
マグネットは磁場発生装置として優れた特性を持ちなが
ら、この極低温での冷却の必要性から幅広く普及される
に到っていない。2. Description of the Related Art At present, what has been put into practical use as a superconducting magnet is mainly one in which a Nb-Ti based superconducting wire is wound around a coil. In addition, Nb 3 Sn or V 3 Ga-based superconducting material is formed into a wire and used as a coil for forming a high magnetic field superconducting magnet. Since these metallic superconducting magnets have a low critical temperature, it is necessary to cool them to an extremely low temperature with liquid helium or the like. Superconducting magnets have excellent characteristics as a magnetic field generator, but have not been widely used because of the need for cooling at this extremely low temperature.
【０００３】一方、酸化物高温超伝導体の発見以後、安
価で取扱いが容易な液体窒素により冷却し使用できる７
７Ｋ以上の臨界温度を有する酸化物超伝導物質を用いた
マグネットの研究開発が盛んに行われている。現在主流
となっているのは、Ｂｉ系材料をＡｇのシース中に詰
め、これをテープ状に加工することによって、配向した
超伝導材料を含む銀シーステープ材を作製し、コイルに
巻く方法である。しかしながら、このようなテープ材は
７７Ｋにおいて十分な臨界電流密度（Ｊｃ）が得られて
おらず、実用には至っていない。On the other hand, after the discovery of the oxide high temperature superconductor, it can be cooled and used by liquid nitrogen which is inexpensive and easy to handle.
Research and development of a magnet using an oxide superconducting material having a critical temperature of 7 K or higher has been actively conducted. The current mainstream method is to pack a Bi-based material in an Ag sheath and process it into a tape to prepare a silver sheath tape material containing an oriented superconducting material, and wind it into a coil. is there. However, such a tape material has not obtained a critical current density (Jc) at 77K and has not been put to practical use.
【０００４】このような、酸化物超伝導体を線材化した
後、コイル化する一般的なマグネット作製方法に対し、
酸化物超伝導体の短所である脆さにともなう難加工性を
考慮して、塑性変形加工せずに、熱処理によってコイル
形状の焼結体を作製しマグネットとして用いることも検
討されている（特開昭６３−２６１８０８号公報）。し
かしながら、焼結体（特にＹ系）は基本的に多くの粒界
を含み、これが超伝導の弱結合となり高い臨界電流密度
を得ることはできない。そのため、焼結体によるマグネ
ットでは、超伝導状態を維持しながら高磁場を発生する
ことは困難な状況にある（特開昭６３−２６１８０８号
公報）。In contrast to a general method for manufacturing a magnet, in which an oxide superconductor is formed into a wire and then formed into a coil,
Considering the difficult workability due to fragility, which is a disadvantage of oxide superconductors, it is also considered to produce a coil-shaped sintered body by heat treatment and use it as a magnet without performing plastic deformation (special characteristics). (Kaisho 63-261808). However, the sintered body (particularly the Y system) basically contains many grain boundaries, which become weak bonds of superconductivity and cannot obtain a high critical current density. Therefore, it is difficult for a magnet made of a sintered body to generate a high magnetic field while maintaining a superconducting state (Japanese Patent Laid-Open No. 63-261808).
【０００５】現在のところ、７７Ｋにおいて高磁場中に
おいても高いＪｃを有するマグネットの材料として使用
可能なバルク材料は、単結晶状のＲＥＢａ2 Ｃｕ3 Ｏ
7-X 中にＲＥ2 ＢａＣｕＯ5 が微細分散した材料（いわ
ゆるＱＭＧ材料）のみである。ＱＭＧ材料は現在Ｐｔ添
加法やＳｅｅｄｉｎｇにより大型の単結晶材料の製造が
可能になってきている。At present, a bulk material that can be used as a material for a magnet having a high Jc even at a high magnetic field at 77K is single crystal REBa 2 Cu 3 O.
It is only a material (so-called QMG material) in which RE 2 BaCuO 5 is finely dispersed in 7-X . For the QMG material, it is now possible to manufacture a large single crystal material by the Pt addition method or seeding.
【０００６】[0006]
【発明が解決しようとする課題】ＱＭＧ材料を用いたマ
グネットは実開平４−１５８１１号においてはじめて考
案された。これは円筒形のＱＭＧ超伝導体に切れ込み加
工することによりソレノイド状のコイルを形成するもの
である。マグネットの発生する磁界は、通電電流とコイ
ル定数の積で与えられる。コイル定数は巻き数や巻き方
によって変化し、臨界密度以下で使用する時は、巻き数
等を大きくしコイル定数を大きくすることによって、低
い通電電流で大きな磁界が得られることになる。実開平
４−１５８１１号公報中の図からもわかるように、この
ようなソレノイド状のマグネットは、形状付与の観点か
ら、線径を小さくし巻き数を増加させてコイル定数を大
きくすることは難しい。そこで円筒に切れ込み加工した
ソレノイド型コイルではなく、ＱＭＧ材を用いたコイル
定数の大きい新しいタイプのマグネットおよびその製造
法の開発が課題となっていた。A magnet using a QMG material was first devised in Japanese Utility Model Laid-Open No. 4-15811. This is to form a solenoidal coil by cutting into a cylindrical QMG superconductor. The magnetic field generated by the magnet is given by the product of the energizing current and the coil constant. The coil constant varies depending on the number of windings and the winding method. When used below the critical density, a large magnetic field can be obtained with a low energizing current by increasing the number of windings and increasing the coil constant. As can be seen from the drawing in Japanese Utility Model Laid-Open No. 4-15811, it is difficult to reduce the wire diameter, increase the number of turns, and increase the coil constant in such a solenoid magnet from the viewpoint of imparting a shape. . Therefore, it has been an issue to develop a new type magnet having a large coil constant using a QMG material and a manufacturing method thereof, instead of a solenoid type coil cut into a cylinder.
【０００７】[0007]
【課題を解決するための手段】本発明は前記課題を解決
するものであって、単結晶状のＲＥＢａ2 Ｃｕ3 Ｏ7-X
相（ＲＥはＹを含む希土類元素およびそれらの組み合わ
せ）中にＲＥ2 ＢａＣｕＯ5 が微細分散した組織を有
し、渦巻状のコイル形状を有することを特徴とする超伝
導マグネットである。またここにおいて、ＲＥＢａ2 Ｃ
ｕ3 Ｏ7-X 相の結晶方位のｃ軸の方向が４０度以内に揃
っており、かつ微量のＰｔまたはＲｈの少なくとも一方
を含有すること、前記ｃ軸が渦巻を構成する平面の法線
に対して２０度以内に揃っていること、渦巻の内側の線
の断面積が外側の線の断面積に比べて大きくなっている
こと、渦巻を構成する超伝導体の隙間の少なくとも一部
に樹脂が存在することによって補強されていることも特
徴とする。SUMMARY OF THE INVENTION The present invention is to solve the above-mentioned problems, and is a single crystal form of REBa 2 Cu 3 O 7-X.
The superconducting magnet has a structure in which RE 2 BaCuO 5 is finely dispersed in a phase (RE is a rare earth element containing Y and a combination thereof), and has a spiral coil shape. Also here, REBa 2 C
The direction of the c-axis of the crystal orientation of the u 3 O 7-X phase is aligned within 40 degrees, and at least one of Pt and Rh is contained in a minute amount, and the c-axis is a normal to a plane forming a spiral. Within 20 degrees, the cross-sectional area of the inner line of the spiral is larger than the cross-sectional area of the outer line, and at least part of the gap of the superconductor forming the spiral is It is also characterized by being reinforced by the presence of resin.
【０００８】また本発明は前記した渦巻状のコイルが複
数積層されていることを特徴とする超伝導マグネットで
ある。またここにおいて、隣接する層の渦巻の方向（右
巻きまたは左巻き）が交互になっていること、積層され
たそれぞれの渦巻状のコイルの端部間が高電気伝導率を
有する金属により接続されているかあるいは積層された
それぞれの渦巻状のコイルの端部間がコイル導体のＴｆ
（ＲＥＢａ2 Ｃｕ3 Ｏ7-X 相の生成温度）より低いＴｆ
を有する超伝導体であるＲＥＢａ2 Ｃｕ3 Ｏ7-X 相によ
り接続されていること、中央部分の渦巻状のコイルの層
の厚さが端部の渦巻状のコイルの層の厚さより厚くなっ
ていること、各渦巻状のコイルの層間の少なくとも一部
に樹脂が存在することによって補強されていることも特
徴とする。Further, the present invention is a superconducting magnet, characterized in that a plurality of the above-mentioned spiral coils are laminated. Further, here, the spiral directions (right-handed or left-handed) of the adjacent layers are alternated, and the ends of each of the stacked spiral coils are connected by a metal having high electrical conductivity. Tf of the coil conductor is between the ends of each spiral coil which is or is laminated.
Tf lower than (REBa 2 Cu 3 O 7-X phase formation temperature)
Are connected by the REBa 2 Cu 3 O 7-X phase, which is a superconductor having, and the thickness of the spiral coil layer in the central portion is larger than that of the spiral coil layer at the end. It is also characterized by being reinforced by the presence of resin in at least a part of the layers of each spiral coil.
【０００９】またさらに前記の１または複数の渦巻状コ
イルによって形成されたコイルの始端と終端とを単結晶
状のＲＥＢａ2 Ｃｕ3 Ｏ7-X 相中にＲＥ2 ＢａＣｕＯ5
が微細分散した組織を有する酸化物超伝導材料を用いて
接続することによって超伝導体からなる閉回路を構成
し、かつ電流導入端子および超伝導スイッチからなるこ
とを特徴とする超伝導マグネットである。Further, the starting end and the terminating end of the coil formed by the above-mentioned one or a plurality of spiral coils are put into a REBa 2 Cu 3 O 7-X phase of RE 2 BaCuO 5
Is a superconducting magnet characterized in that a closed circuit composed of a superconductor is formed by connecting using an oxide superconducting material having a finely dispersed structure, and that it comprises a current introducing terminal and a superconducting switch. .
【００１０】また本発明は単結晶状のＲＥＢａ2 Ｃｕ3
Ｏ7-X 相中にＲＥ2 ＢａＣｕＯ5 が微細分散した組織を
有する酸化物超伝導材料から板状に切り出した後に切れ
目を入れることにより渦巻状のコイル形状に加工するこ
とを特徴とする超伝導マグネットの製造方法である。ま
たここにおいて板状超伝導体を接着剤により支持台に固
定した後、ウォータージェットカッティングにより渦巻
加工することも特徴とする。またあるいは、ＲＥ，Ｂ
ａ，Ｃｕの酸化物を含む前駆体から成形体を作製し、成
形体を渦巻状のコイル形状に加工した後、これを２１１
相と液相からなる半溶融状態に加熱し、その後酸化性雰
囲気中で徐冷することで単結晶状のＲＥＢａ2 Ｃｕ3 Ｏ
7-X 相中にＲＥ2 ＢａＣｕＯ5 が微細分散した組織を有
する超伝導材料を形成せしめることを特徴とする超伝導
マグネットの製造方法である。またここにおいて渦巻状
の成形体の上に渦巻状成形体を覆うように前駆体を配置
し、これらを２１１相と液相からなる半溶融状態に加熱
し、次に種結晶により結晶方位を制御し、酸化性雰囲気
中で徐冷することも特徴とする。The present invention also relates to single crystal REBa 2 Cu 3
A superconducting material characterized by being processed into a spiral coil shape by cutting a plate-shaped oxide superconducting material having a structure in which RE 2 BaCuO 5 is finely dispersed in an O 7-X phase and then making a cut. It is a method of manufacturing a magnet. Further, it is also characterized in that the plate-shaped superconductor is fixed to the support base with an adhesive and then spirally processed by water jet cutting. Alternatively, RE, B
After forming a molded body from a precursor containing an oxide of a and Cu and processing the molded body into a spiral coil shape,
Single crystal REBa 2 Cu 3 O by heating to a semi-molten state consisting of liquid phase and liquid phase and then slowly cooling in an oxidizing atmosphere
A method of manufacturing a superconducting magnet, which comprises forming a superconducting material having a structure in which RE 2 BaCuO 5 is finely dispersed in a 7-X phase. Further, here, the precursor is placed on the spirally formed body so as to cover the spirally formed body, these are heated to a semi-molten state composed of a 211 phase and a liquid phase, and then the crystal orientation is controlled by a seed crystal. However, it is also characterized by slow cooling in an oxidizing atmosphere.
【００１１】また上記の方法により作製された渦巻状の
コイルを渦巻の方向（右巻きまたは左巻き）が交互にな
るように積層し、各コイルを電気的に接続することを特
徴とする超伝導マグネットの製造方法である。ここにお
いて積層されたコイル全体が超伝導体になるように、コ
イル導体のＴｆより低いＴｆを有する超伝導相であるＲ
ＥＢａ2 Ｃｕ3 Ｏ7-X 相によりそれぞれの渦巻状のコイ
ルの端部間を接続することも特徴とする。また前記のい
ずれかの方法によって形成されたコイルの始端と終端と
を単結晶状のＲＥＢａ2 Ｃｕ3 Ｏ7-X 相中にＲＥ2 Ｂａ
ＣｕＯ5 が微細分散した組織を有する超伝導材料により
接続することを特徴とする超伝導マグネットの製造方法
である。A superconducting magnet characterized in that the spiral coils produced by the above method are laminated so that the spiral directions (right-handed or left-handed) are alternated, and the respective coils are electrically connected. Is a manufacturing method. R is a superconducting phase having a Tf lower than the Tf of the coil conductor so that the entire coil laminated here becomes a superconductor.
It is also characterized in that the ends of the spiral coils are connected by the EBa 2 Cu 3 O 7-X phase. The RE 2 a beginning and end of a coil formed by any of the methods of the in the single crystalline REBa 2 Cu 3 O 7-X phase Ba
This is a method for manufacturing a superconducting magnet, characterized in that the superconducting material has a structure in which CuO 5 is finely dispersed.
【００１２】[0012]
【作用】本発明の超伝導用マグネットに使用する材料は
単結晶状のＲＥＢａ2 Ｃｕ3 Ｏ7-X 相中にＲＥ2 ＢａＣ
ｕＯ5 が微細分散した組織を有するものである。ここで
単結晶状というのは完璧な単結晶でなく小傾角粒界など
実用に差支えない欠陥を有するものも包含するという意
味である。ＲＥＢａ2 Ｃｕ3 Ｏ7-X 相（１２３相）およ
びＲＥ2 ＢａＣｕＯ5 相（２１１相）におけるＲＥは
Ｙ，Ｌａ，Ｎｄ，Ｓｍ，Ｅｕ，Ｇｄ，Ｄｙ，Ｈｏ，Ｅ
ｒ，Ｔｍ，Ｙｂ，Ｌｕからなる希土類元素およびそれら
の組み合わせで、ＬａとＮｄを含む１２３相は１：２：
３の化学量論組成からはずれ、ＲＥのサイトにＢａが一
部置換した状態になることもある。また２１１相におい
てもＬａ，ＮｄはＹ，Ｓｍ，Ｅｕ，Ｇｄ，Ｄｙ，Ｈｏ，
Ｅｒ，Ｔｍ，Ｙｂ，Ｌｕとは幾分異なり、金属元素の比
が非化学量論的組成であったり結晶構造が異なっている
ことが知られている。The material used for the superconducting magnet of the present invention is RE 2 BaC in the single crystal REBa 2 Cu 3 O 7-X phase.
uO 5 has a finely dispersed structure. Here, the term "single crystal" is meant to include not only a perfect single crystal but also a crystal having a defect such as a small tilt grain boundary that does not impair practical use. RE in the REBa 2 Cu 3 O 7-X phase (123 phase) and RE 2 BaCuO 5 phase (211 phase) is Y, La, Nd, Sm, Eu, Gd, Dy, Ho, E.
The rare earth element consisting of r, Tm, Yb, and Lu, and the combination thereof, the 123 phase containing La and Nd is 1: 2 :.
There is a case where the site of RE deviates from the stoichiometric composition of 3 and Ba is partially replaced. Also in the 211 phase, La and Nd are Y, Sm, Eu, Gd, Dy, Ho,
It is known that, unlike Er, Tm, Yb, and Lu, the ratio of the metal elements is a non-stoichiometric composition or the crystal structure is different.
【００１３】また１２３相は２１１相とＢａとＣｕとの
複合酸化物からなる液相との包晶反応、 ２１１相＋液相（ＢａとＣｕの複合酸化物）→１２３相 によりできる。そしてこの包晶反応により１２３相がで
きる温度（Ｔｆ：１２３相生成温度）はほぼＲＥ元素の
イオン半径に関連し、イオン半径の減少に伴いＴｆも低
くなる。The 123 phase can be formed by a peritectic reaction between the 211 phase and a liquid phase composed of a complex oxide of Ba and Cu, and a 211 phase + liquid phase (complex oxide of Ba and Cu) → 123 phase. The temperature at which the 123 phase is formed by this peritectic reaction (Tf: 123 phase formation temperature) is almost related to the ionic radius of the RE element, and Tf decreases as the ionic radius decreases.
【００１４】単結晶状の１２３相中に２１１相が微細分
散したＱＭＧ材料は１２３相が結晶成長する際、未反応
の２１１粒が１２３相中に取り残されるためにできる。
すなわち、ＱＭＧ材料は、 ２１１相＋液相（ＢａとＣｕの複合酸化物）→１２３相
＋２１１相 で示される反応によりできる。The QMG material in which the 211 phase is finely dispersed in the single crystal 123 phase can be formed because unreacted 211 grains are left in the 123 phase when the 123 phase crystal grows.
That is, the QMG material can be formed by the reaction represented by 211 phase + liquid phase (composite oxide of Ba and Cu) → 123 phase + 211 phase.
【００１５】ＱＭＧ材料中の２１１相の微細分散は、Ｊ
ｃ向上の観点から極めて重要である。ＰｔまたはＲｈの
少なくとも一方を微量添加することで、半溶融状態（２
１１相と液相からなる状態）での２１１相の粒成長を抑
制し、結果的にＱＭＧ材料中の２１１相を微細化する。
添加量は微細化効果が現れる量および材料コストの観点
からＰｔで０．２〜２．０ｗｔ％、Ｒｈで０．０１〜
０．５ｗｔ％が望ましい。添加されたＰｔまたはＲｈは
１２３相中に一部固溶する。また固溶できなかった元素
はＢａやＣｕとの複合酸化物を形成し材料中に点在する
ことになる。The fine dispersion of the 211 phase in the QMG material is J
It is extremely important from the viewpoint of improving c. By adding a trace amount of at least one of Pt and Rh, a semi-molten state (2
The grain growth of the 211 phase in the state of 11 phases and the liquid phase is suppressed, and as a result, the 211 phase in the QMG material is miniaturized.
The amount of Pt added is 0.2 to 2.0 wt.
0.5 wt% is desirable. The added Pt or Rh partially forms a solid solution in the 123 phase. In addition, the elements that cannot be solid-solved form a complex oxide with Ba or Cu and are scattered in the material.
【００１６】本発明の超電導マグネットはある平面内に
多数渦巻状（蚊取線香状）に巻いた形状にＱＭＧ材を加
工し、細線化を図りコイル定数の大きなマグネットを作
製する。またはさらに渦巻状ＱＭＧ材を積層することに
よって、ソレノイド型のコイルでは困難であったコイル
定数（または巻き数）の大きいマグネットを作製するこ
とができる。In the superconducting magnet of the present invention, a QMG material is processed into a spiral shape (mosquito coil shape) wound in a certain plane, and a magnet having a large coil constant is manufactured by thinning. Alternatively, by further stacking the spiral QMG material, it is possible to manufacture a magnet having a large coil constant (or the number of turns), which was difficult with a solenoid coil.
【００１７】具体的には、まずコイルを構成する超伝導
体は磁場中においても高い臨界電流密度（Ｊｃ）を有す
る必要がある。この条件を満たすには、超伝導的に弱結
合となる大傾角粒界を含まない単結晶状の１２３相であ
る必要がある。さらに高いＪｃ特性を有するためには磁
束の動きを止めるためのピンニングセンターが必要とな
る。このピンニングセンターとして機能するものが微細
分散した２１１相であり、より細かく多数分散している
ことが望ましい。先に述べたようにＰｔやＲｈはこの２
１１相の微細化を促進する働きがある。また２１１相は
劈開しやすい１２３相中に微細分散することによって、
超伝導体を機械的に強化しバルク材料として成り立たす
重要な働きをもしている。Specifically, first, the superconductor forming the coil must have a high critical current density (Jc) even in a magnetic field. In order to satisfy this condition, it is necessary that the 123 phase is a single crystal state that does not include a large tilt grain boundary that is weakly superconductive. In order to have higher Jc characteristics, a pinning center for stopping the movement of magnetic flux is required. It is the 211 phase that is finely dispersed that functions as this pinning center, and it is desirable that a large number of finely dispersed 211 phases are dispersed. As mentioned above, Pt and Rh
It has the function of promoting the refinement of the 11-phase. In addition, the 211 phase is finely dispersed in the 123 phase that is easily cleaved,
It also plays an important role in mechanically strengthening the superconductor and establishing it as a bulk material.
【００１８】このような超伝導導体（ＱＭＧ材料）を図
１に（ａ）平面図、（ｂ）側面図を示したように渦巻加
工したコイル１にすることによってコイル定数の大きい
マグネットが比較的容易にできる。図１では比較的コイ
ル内径が小さい物を一例として示したが、内径の比較的
大きな渦巻形状の物についても全く同様に考えることが
できる。内径が比較的大きな物はコイルの巻き数が減少
し発生磁場が減少するが、その一方でより均一で広い磁
場空間が得られる利点がある。また、コイルの発生磁界
が約２０ｋガウス以下の場合、ボアに鉄芯を入れること
により特性が改善されることは、銅コイルと鉄芯からな
る電磁石の例からも明らかである。また、図１にはほぼ
同心円状のコイル形状を示したが、楕円状や四角や六角
等の形状の物についても全く同様に考えられることは明
らかである。By using such a superconducting conductor (QMG material) as a coiled coil 1 as shown in the plan view (a) and side view (b) of FIG. You can easily. In FIG. 1, a coil having a relatively small inner diameter is shown as an example, but a spiral coil having a relatively large inner diameter can be considered in the same manner. An object having a relatively large inner diameter reduces the number of coil turns and reduces the generated magnetic field, but on the other hand, there is an advantage that a more uniform and wider magnetic field space can be obtained. Further, when the magnetic field generated by the coil is about 20 kGauss or less, it is clear from the example of the electromagnet including the copper coil and the iron core that the characteristics are improved by inserting the iron core into the bore. Further, although FIG. 1 shows a substantially concentric coil shape, it is obvious that an elliptical shape, a square shape, a hexagonal shape and the like can be considered in exactly the same manner.
【００１９】ＱＭＧ材料中には大傾角粒界はないが数度
の小傾角粒界を伴う結晶方位の揺らぎがある。この揺ら
ぎは結晶の成長方向に依存し、ａ軸方向に成長した部分
は比較的大きな揺らぎの分布を有し、数ミリ角の領域で
約±６度、比較的広い領域について調べたものは３６度
程度との報告がある（Ｐｒｏｃｅｅｄｉｎｇｓ ｏｆ５
ｔｈ Ｕ．Ｓ．−Ｊａｐａｎ ｗｏｒｋｓｈｏｐ ｏｎ
ｈｉｇｈ Ｔｃｓｕｐｅｒｃｏｎｄｕｃｔｏｒ およ
び Ａｄｖａｎｃｅｓ ｉｎ Ｓｕｐｅｒｃｏｎｄｕｃ
ｔｉｖｉｔｙ ＩＩ，Ｓｐｒｉｎｇｅｒ−Ｖｅｒｌａｇ
Ｔｏｋｙｏ １９９０）。ここで述べる単結晶状の１
２３相はこのような小傾角粒界を伴っている。There is no large tilt grain boundary in the QMG material, but there is fluctuation of the crystal orientation accompanied by a small tilt grain boundary of several degrees. This fluctuation depends on the crystal growth direction, and the part grown in the a-axis direction has a relatively large distribution of fluctuations, which is about ± 6 degrees in a region of several millimeters square, and is 36 in a comparatively wide region. There is a report about the degree (Proceedings of 5
th U. S. -Japan workshop on
high Tcsuperconductor and Advances in Superconduc
uniformity II, Springer-Verlag
Tokyo 1990). Single crystal 1 described here
The 23rd phase is accompanied by such a low-angle grain boundary.
【００２０】次に１２３相の結晶構造は２次元的であ
り、ａ−ｂ面で劈開しやすい性質を持っている。したが
ってａ−ｂ面でクラックが発生し易く、現在このような
クラックを完全に無くすことはできていない。このクラ
ックが超伝導電流の流れに悪影響を与えないようにする
ためには、クラックと電流が平行、すなわち図２のよう
に結晶のｃ軸が電流２と絶えず垂直になっていることが
理想である。しかしながらコイル導体中には、ｃ軸の方
位に４０度程度の揺らぎがあるため、ある平面内に渦巻
状にコイルを巻いたときのその平面の法線Ｎに対し図２
に示すようにｃ軸の方向３は±２０度以内であることが
望まれる。Next, the crystal structure of the 123 phase is two-dimensional and has a property of easily cleaving in the ab plane. Therefore, cracks are likely to occur on the ab plane, and such cracks cannot be completely eliminated at present. In order to prevent this crack from adversely affecting the flow of superconducting current, it is ideal that the crack and the current are parallel, that is, the c axis of the crystal is constantly perpendicular to the current 2 as shown in FIG. is there. However, since there is a fluctuation of about 40 degrees in the c-axis direction in the coil conductor, when the coil is spirally wound in a plane, the normal line N to that plane is compared with FIG.
It is desired that the c-axis direction 3 be within ± 20 degrees as shown in FIG.
【００２１】また、コイルに通電し励磁した場合コイル
の内側の導体は、外側の導体に対してより大きな磁界に
曝されることになる。またＪｃは磁場の増加に伴い減少
するのが一般的である。したがって、同じ断面積を有す
るコイルに通電した場合、内側の導体が先に臨界状態に
達し、超伝導が壊れコイル自身を損傷することになる。
したがって、Ｊｃの磁場特性に合わせ、より内側の導体
の断面積がより太くなっていることが望ましい。When the coil is energized and excited, the conductor inside the coil is exposed to a larger magnetic field than the conductor outside the coil. Further, Jc generally decreases as the magnetic field increases. Therefore, when a coil having the same cross-sectional area is energized, the inner conductor reaches a critical state first, causing superconductivity to break and the coil itself to be damaged.
Therefore, it is desirable that the inner conductor has a thicker cross-sectional area according to the magnetic field characteristics of Jc.
【００２２】またさらに、磁場を発生している超伝導導
体は電磁相互作用により内側から外側へ向かう力（ロー
レンツ力）を受ける。この力が導体の強度を超えた場
合、導体を破壊する。そこでコイルの破壊を防ぐために
は、導体同士を機械的に結合し補強することが必要であ
る。そのためには、隣合う導体の隙間を非超伝導物質に
より埋め、導体同士を固定することが有効である。この
とき導体を結合する非超伝導物質は、導体と近い熱膨張
係数を有することが望ましい。熱硬化性の樹脂などはこ
の一例といえる。Furthermore, the superconducting conductor generating the magnetic field receives a force (Lorentz force) from the inside to the outside due to electromagnetic interaction. If this force exceeds the strength of the conductor, it destroys the conductor. Therefore, in order to prevent the breakage of the coil, it is necessary to mechanically connect and reinforce the conductors. For that purpose, it is effective to fix the conductors by filling the gap between the adjacent conductors with a non-superconducting material. At this time, it is desirable that the non-superconducting material that binds the conductor has a thermal expansion coefficient close to that of the conductor. A thermosetting resin or the like is one example of this.
【００２３】続いて、上記渦巻状コイルを積層して端部
間と接続し、それぞれの渦巻状コイルが発生する磁場が
互いに強め合うように通電することによって、より強い
磁場を発生するマグネットができる。同数の渦巻状コイ
ルを積層するさい、各渦巻状コイルの隙間を小さくしな
るべく互いに近づけた方がより高い最高発生磁場が得ら
れる。このためには図３のように渦巻の方向が同じにな
るよう積層し電流２を内側から外側（または外側から内
側）になるように揃え、コイル１間を導体４で接続する
方法が考えられる。しかし、図４に（ａ）積層前、
（ｂ）積層後を示したように渦巻コイル１の渦の方向
（右巻きまたは左巻き）を交互に逆にして積層し、かつ
コイル１の内と外の端を交互に接続することによって図
３では必要であったコイルをつなぐ導体が不要となり、
その厚さの分コイルを密に積層できる。図４（ａ）にお
いて５が接続部分である。Subsequently, the above-mentioned spiral coils are laminated and connected between the end portions, and current is applied so that the magnetic fields generated by the respective spiral coils reinforce each other, whereby a magnet that generates a stronger magnetic field can be formed. . When stacking the same number of spiral coils, it is possible to obtain a higher maximum generated magnetic field by reducing the gap between the spiral coils and making them close to each other. For this purpose, as shown in FIG. 3, a method of stacking so that the spiral directions are the same, aligning the currents 2 from the inside to the outside (or from the outside to the inside), and connecting the coils 1 with the conductors 4 is considered. . However, in FIG.
(B) As shown after stacking, the spiral coil 1 is stacked by alternately reversing the direction of the vortex (right-handed or left-handed) and connecting the inner and outer ends of the coil 1 alternately. Then, the conductor that connects the required coil is no longer necessary,
The coils can be densely stacked by the thickness. In FIG. 4A, 5 is a connecting portion.
【００２４】積層された渦巻コイルの中央部に位置する
コイルは、端に位置するコイルに比べ高い磁場に曝され
ることになる。したがって、同じ断面積を有する積層コ
イルに通電した場合、中央部のコイルが先に臨界状態に
達し、超伝導が壊れコイル自身を損傷することになる。
したがって、Ｊｃの磁場特性に合わせ、より中央部のコ
イルの断面積がより太くなっていることが理想的であ
る。そのためには中央部分の渦巻コイルの層の厚さが端
部の渦巻コイルの層の厚さより厚くなっていることが望
ましい。The coil located at the center of the stacked spiral coils is exposed to a higher magnetic field than the coils located at the ends. Therefore, when a laminated coil having the same cross-sectional area is energized, the central coil reaches a critical state first, causing superconductivity to break and the coil itself to be damaged.
Therefore, it is ideal that the cross-sectional area of the coil in the central portion is larger according to the magnetic field characteristics of Jc. For that purpose, it is desirable that the thickness of the spiral coil layer at the central portion is larger than the thickness of the spiral coil layer at the end portion.
【００２５】積層を行った場合、上記のように各渦巻コ
イルの端部間を接続する必要があるが、ＱＭＧ材を冷却
し通電した状態において、この接続部での発熱を零また
は極力小さくすることが望ましい。発熱が大きい場合、
消費電力や冷媒の消耗が大きくなるだけではなく熱が超
伝導導体の超伝導特性を低下させ、さらにはクエンチを
引き起こし導体自身を焼損させてしまう。このような要
請から接続には、接触抵抗の低い電極を形成し、電気伝
導度の大きい金属により接続する必要がある。When laminating is performed, it is necessary to connect between the ends of each spiral coil as described above, but when the QMG material is cooled and energized, the heat generation at this connection is reduced to zero or as small as possible. Is desirable. If the fever is high,
Not only the power consumption and the consumption of the refrigerant increase, but also the heat deteriorates the superconducting property of the superconducting conductor, which causes quenching and burns the conductor itself. In order to meet these requirements, it is necessary to form electrodes with low contact resistance and connect with a metal having high electrical conductivity.
【００２６】接続部の発熱を完全に零にするには、接続
部の電流の経路がすべて超伝導体である必要がある。さ
らに始端と終端とを単結晶状のＱＭＧ材料により接続す
ることによってマグネット全体を単結晶になるように
し、この超伝導体からなる閉回路に電流導入端子および
超伝導スイッチを取り付けることによって永久電流モー
ドで動作するマグネットができる。In order to completely eliminate the heat generation at the connection portion, it is necessary that all the current paths of the connection portion are superconductors. Furthermore, by connecting the start end and the end with a single crystal QMG material, the whole magnet is made into a single crystal, and by attaching a current introducing terminal and a superconducting switch to a closed circuit made of this superconductor, a permanent current mode is obtained. You can have a magnet that works with.
【００２７】本発明の超伝導マグネットの製造方法であ
るが、コイル形状を得るには、大別して二通りの方法が
ある。一つは結晶化させた後にコイル形状を付与する方
法（ＧＦ法）で、もう一つは前駆体をコイル形状に加工
した後結晶化させる方法（ＦＧ法）である。Regarding the method of manufacturing the superconducting magnet of the present invention, there are roughly two methods for obtaining the coil shape. One is a method of giving a coil shape after crystallization (GF method), and the other is a method of processing a precursor into a coil shape and then crystallizing it (FG method).
【００２８】ＧＦ法の例を示すと、従来の技術である改
良型ＱＭＧ法等により円柱状のバルク材料を作製する
（Ａｄｖａｎｃｅｓ ｉｎ Ｓｕｐｅｒｃｏｎｄｕｃｔ
ｉｖｉｔｙ ＩＩＩ，Ｓｐｒｉｎｇｅｒ−Ｖｅｒｌａｇ
Ｔｏｋｙｏ １９９２）。これを所定の厚さにスライ
スし円盤状に加工する。このスライス加工には、ダイヤ
モンド粉末を埋め込んだブレード等による切断加工が適
している。次に円盤状ＱＭＧ材料は渦巻状に加工され
る。渦巻加工に関しては小型のダイヤモンドポイントに
よる加工も可能であるが、ウォータージェットカッティ
ング（高圧の水を細いノズルから吹き出して切断加工す
る方法）などの加工性に優れた方法が望ましい。ウォー
タージェットカッティングを用いる場合、水中に硬い粉
末（ざくろ石の粉末等）を混ぜて行うアブレージョンと
呼ばれる方法が適している。また水圧による衝撃により
材料が割れるのを防ぐため、変形しにくい台に材料を樹
脂等で固定して加工することが望ましい。また材料は水
と反応する可能性があり加工後はすばやく乾燥させるこ
とが望ましい。As an example of the GF method, a columnar bulk material is manufactured by an improved QMG method which is a conventional technique (Advances in Superconduct).
Ivity III, Springer-Verlag
Tokyo 1992). This is sliced into a predetermined thickness and processed into a disk shape. For this slicing, cutting with a blade or the like having diamond powder embedded therein is suitable. Next, the disk-shaped QMG material is processed into a spiral shape. As for the spiral processing, processing with a small diamond point is also possible, but a method having excellent workability such as water jet cutting (a method of blowing high-pressure water through a thin nozzle to perform cutting) is desirable. When using water jet cutting, a method called ablation, which is performed by mixing hard powder (garnet powder, etc.) into water, is suitable. Further, in order to prevent the material from cracking due to impact due to water pressure, it is desirable to fix the material to a table that is difficult to deform with a resin or the like for processing. Also, the material may react with water and it is desirable to dry it quickly after processing.
【００２９】次にＦＧ法の例を示すと、まずＲＥ，Ｂ
ａ，Ｃｕの酸化物を２１１相：１２３相が所定の比にな
るように混合する。このときＰｔ，Ｒｈを添加すると最
終組織の２１１が微細化する。この混合粉末を金型等に
より加工成形し前駆体を作製する。この前駆体は圧粉体
であるため結晶化したＱＭＧ材とは異なりドリルや鋸を
用い加工が容易にできる。例えば図５のように、切れ込
み７を入れて円柱状の前駆体６を糸鋸によりコイル状に
加工することができる。このとき図６の（ａ）全体図、
（ｂ）一部を拡大した平面図に示したように一部切り残
した部分８をつくることで半溶融時の変形を少なくする
ことができる。Next, an example of the FG method will be described. First, RE, B
The oxides of a and Cu are mixed so that the 211 phase: 123 phase has a predetermined ratio. At this time, if Pt and Rh are added, the final structure 211 becomes fine. This mixed powder is processed and molded with a mold or the like to prepare a precursor. Since this precursor is a green compact, it can be easily processed using a drill or a saw, unlike the crystallized QMG material. For example, as shown in FIG. 5, the cylindrical precursor 6 can be processed into a coil shape by making a notch 7 with a saw. At this time, (a) overall view of FIG.
(B) As shown in a partially enlarged plan view, by forming a part 8 left uncut, it is possible to reduce deformation during semi-melting.
【００３０】加工された前駆体６は図７のように他のＲ
Ｅ組成を有する前駆体９，１０，１１と重ねられ炉内に
配置される。このとき、コイルの隙間に雰囲気が出入り
できるようになっていることが結晶成長の観点から望ま
しい。前駆体９は、コイル状前駆体が多くの切れ込みを
有することから、種結晶から成長する結晶が外側のコイ
ルにまで最短距離で届くように、コイル状前駆体６の上
部を覆っていることが望ましい。また前駆体９は結晶成
長の観点から、コイル状前駆体６のＲＥ組成のＴｆ以上
のＲＥ組成からなっていることが望ましい。The processed precursor 6 has another R as shown in FIG.
The precursors 9, 10, and 11 having the E composition are stacked and placed in the furnace. At this time, it is desirable from the viewpoint of crystal growth that the atmosphere can enter and leave the gap between the coils. Since the coiled precursor has many notches, the precursor 9 may cover the upper part of the coiled precursor 6 so that the crystal growing from the seed crystal reaches the outer coil in the shortest distance. desirable. From the viewpoint of crystal growth, the precursor 9 preferably has an RE composition that is equal to or higher than Tf of the RE composition of the coiled precursor 6.
【００３１】また前駆体１０はコイル状前駆体６のＲＥ
組成のＴｆより低いＴｆのＲＥ組成であり、前駆体１１
はコイル状前駆体６のＲＥ組成のＴｆより高いＴｆのＲ
Ｅ組成であることが望ましい。半溶融状態で長時間に保
持するためには支持材２０との反応を最小限にしかつ種
結晶以外からの結晶成長を抑制する必要がある。冷却過
程において前駆体１１はＴｆが高いため比較的すばやく
結晶化し支持材２０との反応を防止する。前駆体１０は
Ｔｆが低いため前駆体１１からの結晶成長を防止する。The precursor 10 is the RE of the coiled precursor 6.
The RE composition has a Tf lower than the composition Tf, and the precursor 11
Is the R of Tf higher than the Tf of the RE composition of the coiled precursor 6.
It is desirable that the composition is E. In order to maintain the semi-molten state for a long time, it is necessary to minimize the reaction with the support material 20 and suppress the crystal growth from other than the seed crystal. In the cooling process, the precursor 11 has a high Tf and crystallizes relatively quickly to prevent the reaction with the support material 20. Since the precursor 10 has a low Tf, it prevents crystal growth from the precursor 11.
【００３２】Ｓｅｅｄｉｎｇは前駆体６のＴｆ以上、種
結晶のＴｆ以下で行われる。このとき種結晶はより大き
い方が効率的であり望ましい。前駆体９はコイル状前駆
体６と同じＲＥ組成であっても良い。種結晶から成長し
たＱＭＧ結晶は前駆体９を結晶化しさらにコイル状前駆
体６を結晶化し、コイル状のＱＭＧ結晶ができる。Seeding is performed above the Tf of the precursor 6 and below the Tf of the seed crystal. At this time, a larger seed crystal is more efficient and desirable. The precursor 9 may have the same RE composition as the coiled precursor 6. The QMG crystal grown from the seed crystal crystallizes the precursor 9 and further crystallizes the coiled precursor 6 to form a coiled QMG crystal.
【００３３】コイル状結晶は室温まで冷却された後、ダ
イヤモンドブレード等により所定の厚さにスライスされ
る。このとき図６に示したような切り残した部分がある
ものはスライスするさい機械的ダメージが少ない。切り
残した部分を設けない場合、樹脂等により導体間を補強
した後スライス加工することが望ましい。The coiled crystal is cooled to room temperature and then sliced to a predetermined thickness with a diamond blade or the like. At this time, when there is a portion left uncut as shown in FIG. 6, mechanical damage is small when slicing. When the uncut portion is not provided, it is desirable to slicing after reinforcing the space between the conductors with resin or the like.
【００３４】ＦＧ法の利点はコイル加工が成形体（圧粉
体）に対して行われるため、高価な加工装置を必要とせ
ず、安価な工具により容易に作製されることにある。ま
た、結晶成長後にコイル形状（バネ形状）を有している
ために、機械的歪を緩和し、ひび割れが入りにくいこと
などがある。The advantage of the FG method is that since the coil processing is performed on the molded body (compacted powder), it does not require an expensive processing apparatus and can be easily manufactured by an inexpensive tool. Further, since it has a coil shape (spring shape) after crystal growth, mechanical strain is relaxed, and cracks are less likely to occur.
【００３５】上記のようにＧＦ法やＦＧ法により作製さ
れた渦巻状導体に通電するには、電極を設ける必要があ
る。電極の接触抵抗はより小さいことが望ましい。電極
作製の一例をあげると、所定の位置にＡｇペーストを塗
布した後７００℃から超伝導体の分解温度以下の温度域
に昇温した後降温する。この降温の際に、酸素富化処理
をかね酸化性雰囲気（望ましくは純酸素中）で徐冷する
ことは、プロセスの効率上望ましい。このようにして電
極を有する渦巻状のＱＭＧ超伝導コイルができる。To energize the spiral conductor produced by the GF method or the FG method as described above, it is necessary to provide an electrode. It is desirable that the contact resistance of the electrodes be smaller. As an example of electrode production, after applying Ag paste at a predetermined position, the temperature is raised from 700 ° C. to a temperature range below the decomposition temperature of the superconductor and then lowered. It is desirable from the standpoint of process efficiency to gradually cool the oxygen enrichment treatment in an oxidizing atmosphere (preferably in pure oxygen) at the time of this temperature decrease. In this way, a spiral QMG superconducting coil having electrodes can be obtained.
【００３６】このような渦巻状コイルは取扱いにおける
外力やローレンツ力に耐えるため機械的に補強する必要
がある。補強には隣合う導体間を結合させることが有効
である。補強の一例としては熱硬化樹脂など、硬化時の
体積変化の少ない接着剤や熱膨張率がＱＭＧ材に近いも
のが望ましい。また積層されたマグネットに関しても上
記の理由から各層間を固定（補強）することが望まし
い。Such a spiral coil must be mechanically reinforced in order to withstand external force and Lorentz force during handling. For reinforcement, it is effective to connect adjacent conductors. As an example of the reinforcement, an adhesive such as a thermosetting resin that has a small volume change during curing or a material having a thermal expansion coefficient close to that of a QMG material is desirable. It is also desirable to fix (reinforce) the layers between the laminated magnets for the above reasons.
【００３７】また、各層を超伝導体で接続するには、各
層の結晶方位を合わせる必要がある。結晶方位がほぼ合
った状態で互いの接続位置を決定する。コイル接続部分
１２を図８（ａ）のように加工し、くぼみ１４の部分に
超伝導体のＴｆ（Ｔｆｃ）より低いＴｆ（Ｔｆｚ）のＲ
Ｅ組成の前駆体１３を図８（ａ）のように配置する。こ
れを前駆体１３が半溶融状態になりかつコイルが分解し
ない温度Ｔ（Ｔｆｃ＞Ｔ＞Ｔｆｚ）にまで加熱する。そ
の後Ｔｆｚ近傍で徐冷することによって互いに向き合う
各層から図８（ｂ）およびこれの部分拡大図（ｃ）のよ
うに前駆体１３は１２３相の結晶１６が成長し（図では
中心部分に結晶成長の残り部分がある）超伝導体１５と
なり、これにより接続された多層コイルができる。In order to connect each layer with a superconductor, it is necessary to match the crystal orientation of each layer. The mutual connection positions are determined in a state where the crystal orientations are substantially matched. The coil connecting portion 12 is processed as shown in FIG. 8A, and R of Tf (Tfz) lower than Tf (Tfc) of the superconductor is formed in the recess 14 portion.
The precursor 13 having the E composition is arranged as shown in FIG. This is heated to a temperature T (Tfc>T> Tfz) where the precursor 13 becomes a semi-molten state and the coil does not decompose. Then, by gradually cooling in the vicinity of Tfz, a 123-phase crystal 16 is grown as a precursor 13 from the respective layers facing each other as shown in FIG. 8B and a partially enlarged view of FIG. 8B. (There is the remaining part of the above) to become a superconductor 15, which forms a connected multilayer coil.
【００３８】またさらに１または複数の渦巻状コイルに
よって形成されたコイルの始端と終端とを結ぶ超伝導体
を上記と同様に、導体中のくぼみに前駆体１３を配置し
熱処理することで、各層の接続およびコイルの始端と終
端が超伝導体で接続された、超伝導の閉ループを有する
マグネットができる。Further, as in the above case, the precursor 13 is placed in the recess in the conductor and heat-treated in the same manner as described above for the superconductor connecting the starting end and the terminating end of the coil formed by one or a plurality of spiral coils. A magnet having a closed loop of superconducting, in which the superconducting material is connected and the beginning and end of the coil are connected by a superconductor.
【００３９】[0039]
実施例１ 市販されている純度９９．９％の各試薬Ｙ2 Ｏ3 ，Ｂａ
Ｏ2 ，ＣｕＯをＹ：Ｂａ：Ｃｕの金属元素のモル比が１
３：１７：２４（すなわち最終組織の１２３相：２１１
相のモル比が７：３）になるように混合した。さらに白
金を０．５重量％添加した。混合粉は一旦８００℃で８
時間仮焼され、さらに粉砕された。仮焼粉砕粉は内径８
５ｍｍの円筒状金型により厚さ約１８ｍｍの円盤状に成
形された。また上記Ｙ系成形体と同様の方法により厚さ
４ｍｍのＳｍ系およびＹｂ系円盤状成形体を作製した。Example 1 Commercially available reagents Y 2 O 3 and Ba each having a purity of 99.9%
O 2 and CuO have a molar ratio of the metal elements Y: Ba: Cu of 1
3:17:24 (ie 123 phases of final tissue: 211
The phases were mixed in a molar ratio of 7: 3). Further, 0.5% by weight of platinum was added. Mix powder once at 800 ℃ 8
It was calcined for hours and then crushed. Calcinated pulverized powder has an inner diameter of 8
It was molded into a disk shape having a thickness of about 18 mm by a 5 mm cylindrical mold. In addition, a Sm-based and Yb-based disk-shaped molded product having a thickness of 4 mm was produced by the same method as that for the Y-based molded product.
【００４０】これらをＡｌ2 Ｏ3 の支持材の上にＳｍ
系，Ｙｂ系，Ｙ系の順番で下から重ね炉内に配置した。
これらの前駆体は大気中において１１５０℃まで８時間
で昇温、３０分保持された後、１０３０℃まで１時間で
降温し１時間保持した。その間予め作製しておいたＳｍ
系の種結晶（ＱＭＧ結晶）を用いＳｅｅｄｉｎｇを行っ
た。種結晶の方位はｃ軸が円盤状の前駆体の法線になる
ように、劈開面を前駆体の上にのせた。その後１００５
〜９８０℃まで１００時間かけて冷却しＹ系ＱＭＧ結晶
の成長を行った。さらに室温まで約１５時間かけて冷却
し、円筒形の単結晶状のＹ系ＱＭＧ結晶を得た。These are Sm on an Al 2 O 3 support material.
System, Yb system, and Y system in this order from the bottom in the stacking furnace.
These precursors were heated to 1150 ° C. in the air for 8 hours and held for 30 minutes, then cooled to 1030 ° C. for 1 hour and held for 1 hour. In the meantime, Sm that was made in advance
Seeding was performed using a seed crystal (QMG crystal) of the system. As for the orientation of the seed crystal, the cleavage plane was placed on the precursor so that the c-axis was the normal to the disk-shaped precursor. Then 1005
The Y-based QMG crystal was grown by cooling to ~ 980 ° C over 100 hours. The mixture was further cooled to room temperature over about 15 hours to obtain a cylindrical single crystal Y-based QMG crystal.
【００４１】この結晶をダイヤモンドブレードを用い切
断（スライス）することによって厚さ４．５ｍｍの円盤
状ＱＭＧ材を得た。これを厚さ８ｍｍの素焼きの板に膠
により固定した。そして、予めウォータージェットカッ
ティングのノズルが図１（ａ）に示した渦巻の形状の輪
郭線を動くようにプログラムし、ノズル移動速度を約５
０ｍｍ／ｍｉｎに設定し、素焼きの板もろとも渦巻状に
カッティングした。このときざくろ石の粉末を水ととも
に噴出させるアブレージョンと呼ばれる方法を用いた。This crystal was cut (sliced) with a diamond blade to obtain a disk-shaped QMG material having a thickness of 4.5 mm. This was fixed to an 8 mm thick unglazed plate with glue. Then, the water jet cutting nozzle is programmed in advance so as to move along the contour line of the spiral shape shown in FIG. 1A, and the nozzle moving speed is set to about 5
It was set to 0 mm / min, and the unglazed plate was cut into a spiral shape. At this time, a method called ablation in which garnet powder was ejected together with water was used.
【００４２】渦巻加工の後、膠を加熱することでコイル
状ＱＭＧ結晶は素焼きの板から外された。膠を十分除去
した後、図９のようにコイル１の両端にＡｇペースト１
８を塗布し、さらに８５０℃に加熱した。８５０℃で１
０分保持した後、続いて酸素を炉内に流し６５０℃から
３５０℃まで５０時間かけて冷却し酸素富化処理を行っ
た。室温に冷却した後、エポキシ樹脂１７（商品名：ア
ラルダイト）を用いて図９のように補強した。After the spiral processing, the coil-shaped QMG crystal was removed from the bisque-fired plate by heating the glue. After sufficiently removing the glue, the Ag paste 1 is applied to both ends of the coil 1 as shown in FIG.
8 was applied and further heated to 850 ° C. 1 at 850 ° C
After holding for 0 minutes, oxygen was then flown into the furnace and cooled from 650 ° C. to 350 ° C. over 50 hours to perform oxygen enrichment treatment. After cooling to room temperature, it was reinforced with an epoxy resin 17 (trade name: Araldite) as shown in FIG.
【００４３】このようにして、線の断面積が約３．５ｍ
ｍ（幅）×４．５ｍｍ（厚さ）の８回巻きのコイルを作
製した。そして、このコイルのＡｇ電極に超音波半田を
用い銅製の電流端子を接続した。これを液体窒素温度
（約７７Ｋ）に冷却し５５０Ａの電流を流したところ、
中心部で０．８５ｋガウスの磁場を発生することに成功
した。In this way, the cross-sectional area of the wire is about 3.5 m.
An eight-turn coil measuring m (width) × 4.5 mm (thickness) was produced. Then, a current terminal made of copper was connected to the Ag electrode of this coil using ultrasonic solder. When this was cooled to liquid nitrogen temperature (about 77K) and a current of 550A was applied,
We succeeded in generating a magnetic field of 0.85k Gauss at the center.
【００４４】実施例２ 市販されている純度９９．９％の各試薬Ｙ2 Ｏ3 ，Ｂａ
Ｏ2 ，ＣｕＯをＹ：Ｂａ：Ｃｕの金属元素のモル比が２
５：３５：４９（すなわち最終組織の１２３相：２１１
相のモル比が７５：２５）になるように混合した。さら
にＲｈを０．２重量％添加した。混合粉は一旦８３０℃
で８時間仮焼され、さらに粉砕された。仮焼粉砕粉は内
径８５ｍｍの円筒状金型により厚さ約２５ｍｍの円盤状
に成形された。また上記Ｙ系成形体と同様の方法により
厚さ４ｍｍのＳｍ系とＤｙおよびＹｂ系円盤状成形体を
作製した。さらにＹ系成形体については、等方静水圧プ
レスにより圧縮加工された。このＹ系前駆体は図６のよ
うな一部がつながった渦巻形状に加工された。この加工
はまずドリルにより穴開け加工を行い、しかる後にこの
穴に糸鋸の刃を貫通させコイル状に切れ込みを入れるこ
とにより行った。Example 2 Commercially available reagents of purity 99.9% Y 2 O 3 and Ba
O 2 and CuO have a molar ratio of Y: Ba: Cu of metallic elements of 2
5:35:49 (ie 123 phases of final structure: 211
The phases were mixed in a molar ratio of 75:25). Further, 0.2% by weight of Rh was added. Mixed powder once 830 ℃
It was calcined for 8 hours and further crushed. The calcined pulverized powder was formed into a disk shape having a thickness of about 25 mm by a cylindrical mold having an inner diameter of 85 mm. A Sm-based, Dy, and Yb-based disk-shaped molded product having a thickness of 4 mm was produced by the same method as that for the Y-based molded product. Further, the Y-based compact was compressed by an isotropic hydrostatic press. This Y-based precursor was processed into a spiral shape in which a part is connected as shown in FIG. This processing was performed by first making a hole with a drill, and then making a slit in a coil shape by penetrating the hole with a blade of a thread saw.
【００４５】これらの前駆体は図７に示すようにＡｌ2
Ｏ3 の支持材２０の上にＳｍ系，Ｙｂ系，Ｙ系，Ｄｙ系
の順番で下から重ね炉内に配置した。このとき、雰囲気
がコイルの内部全体に行き渡るようにＹｂ系前駆体に切
れ込みを設けた。これらの前駆体は大気中において１１
６０℃まで８時間で昇温、４０分保持された後、１０４
０℃まで１時間で降温し１時間保持した。その間予め作
製しておいたＮｄ系の種結晶（ＱＭＧ結晶）を用いてＳ
ｅｅｄｉｎｇを行った。種結晶の方位はｃ軸が円盤状の
前駆体の法線になるように、劈開面を前駆体の上にのせ
た。その後１０１５〜９７５℃まで１５０時間かけて冷
却しＹ系コイル状ＱＭＧ結晶の成長を行った。さらに室
温まで約１５時間かけて冷却した。As shown in FIG. 7, these precursors are Al 2
Sm, Yb, Y, and Dy systems were arranged in this order from the bottom on the O 3 support material 20 in the stacking furnace. At this time, notches were provided in the Yb-based precursor so that the atmosphere was spread throughout the inside of the coil. These precursors are 11
After heating up to 60 ° C. in 8 hours and holding for 40 minutes, 104
The temperature was lowered to 0 ° C. in 1 hour and kept for 1 hour. In the meantime, Sd was produced by using an Nd-based seed crystal (QMG crystal) that had been prepared in advance.
eding. As for the orientation of the seed crystal, the cleavage plane was placed on the precursor so that the c-axis was the normal to the disk-shaped precursor. Then, it was cooled to 1015 to 975 ° C. over 150 hours to grow a Y-based coiled QMG crystal. Furthermore, it cooled to room temperature over about 15 hours.
【００４６】この結晶をダイヤモンドブレードを用い切
断（スライス）することによって厚さ約４ｍｍの渦巻コ
イル状のＱＭＧ材を得た。さらにコイルの両端に図１０
のようにＡｇペースト１８を塗布し８８０℃に加熱し
た。８８０℃で１０分保持した後、続いて酸素を炉内に
流し６５０℃から３５０℃まで５０時間かけて冷却し酸
素富化処理を行った。室温に冷却した後、エポキシ樹脂
１７を用いて図１０のように補強した。This crystal was cut (sliced) with a diamond blade to obtain a spiral coil QMG material having a thickness of about 4 mm. Furthermore, as shown in FIG.
Then, the Ag paste 18 was applied and heated to 880 ° C. After holding at 880 ° C. for 10 minutes, oxygen was then flown into the furnace and cooled from 650 ° C. to 350 ° C. over 50 hours to perform oxygen enrichment treatment. After cooling to room temperature, it was reinforced with epoxy resin 17 as shown in FIG.
【００４７】このようにして、線の断面積が約３．５ｍ
ｍ（幅）×４．０ｍｍ（厚さ）の８回巻きのコイルを作
製した。そして、このコイルのＡｇ電極に超音波半田を
用い銅製の電流端子を接続した。これを液体窒素温度
（約７７Ｋ）に冷却し５００Ａの電流を流したところ、
中心部で約０．９０ｋガウスの磁場を発生することに成
功した。In this way, the cross-sectional area of the wire is about 3.5 m.
An eight-turn coil measuring m (width) × 4.0 mm (thickness) was produced. Then, a current terminal made of copper was connected to the Ag electrode of this coil using ultrasonic solder. When this was cooled to liquid nitrogen temperature (about 77K) and a current of 500A was applied,
We succeeded in generating a magnetic field of about 0.90k Gauss at the center.
【００４８】実施例３ 実施例１のＹ系前駆体のＲＥ組成、添加条件、徐冷条件
およびコイルの厚さを表１のように変えて同様に実験を
行った。この表に示したように各ＲＥ組成の超伝導マグ
ネットはクエンチすることなくＹ系とほぼ同等の磁場を
発生した。Example 3 The same experiment was conducted by changing the RE composition, addition conditions, slow cooling conditions and coil thickness of the Y-based precursor of Example 1 as shown in Table 1. As shown in this table, the superconducting magnet of each RE composition generated a magnetic field almost equal to that of the Y system without quenching.
【００４９】[0049]
【表１】 [Table 1]
【００５０】実施例４ 実施例２のＹ系前駆体のＲＥ組成、前駆体９（図７参
照）のＲＥ組成、添加条件、徐冷条件およびコイルの厚
さを表２のように変えて同様に実験を行った。この表に
示したように各ＲＥ組成の超伝導マグネットはクエンチ
することなくＹ系とほぼ同等の磁場を発生した。Example 4 Same as Example 2 except that the RE composition of the Y-based precursor, the RE composition of the precursor 9 (see FIG. 7), the addition conditions, the slow cooling conditions and the coil thickness are changed as shown in Table 2. The experiment was conducted. As shown in this table, the superconducting magnet of each RE composition generated a magnetic field almost equal to that of the Y system without quenching.
【００５１】[0051]
【表２】 [Table 2]
【００５２】実施例５ 実施例２で作製したＹ系渦巻状コイルを図１１の（ａ）
積層前、（ｂ）積層後の斜視図に示すように４枚積層し
た。この時１層目と３層目のコイル１Ａ，１Ｃは上から
見て時計回りに電流が流れたときに中心から外へ流れる
向きになっており、また２層目と４層目のコイル１Ｂ，
１Ｄは外から中心に向かうように積層した。そして１層
目のコイル１Ａ中心部の電極と２層目のコイル１Ｂの中
心部の電極２１Ａとを低融点の半田（商品名：セラソル
ザー）を用い超音波半田ごてにより接続した。また同様
に２層目のコイル１Ｃの外側の電極と３層目のコイル１
Ｄの外側の電極２１Ｂとを、３層目の内側の電極と４層
目の内側の電極とをそれぞれ接続した。そして１層目と
４層目の外側の電極を直流電源の電流リードに接続し
た。さらに層間をエポキシ樹脂により固定した。Example 5 The Y-based spiral coil produced in Example 2 is shown in FIG.
Four sheets were laminated before lamination and as shown in the perspective view after (b) lamination. At this time, the coils 1A and 1C of the first and third layers are oriented so as to flow outward from the center when a current flows clockwise when viewed from above, and the coils 1B and 2B of the second and fourth layers. ，
1D was laminated from the outside toward the center. Then, the electrode in the central portion of the coil 1A of the first layer and the electrode 21A in the central portion of the coil 1B of the second layer were connected with an ultrasonic soldering iron using a low melting point solder (product name: Cerasolzer). Similarly, the outer electrode of the coil 1C of the second layer and the coil 1 of the third layer
The outer electrode 21B of D was connected to the inner electrode of the third layer and the inner electrode of the fourth layer. The outer electrodes of the first and fourth layers were connected to the current leads of the DC power supply. Further, the layers were fixed with an epoxy resin.
【００５３】この４層マグネットを液体窒素中に浸し、
マグネットが７７Ｋまで十分冷却された後、５００Ａ通
電した。層間の電極部で幾分窒素の沸騰が大きくなった
ものの、マグネットは軸上で図１２のグラフのような磁
界分布を発生した。Immerse this four-layer magnet in liquid nitrogen,
After the magnet was sufficiently cooled to 77K, 500A was energized. Although the boiling of nitrogen increased to some extent in the electrode portion between the layers, the magnet generated a magnetic field distribution on the shaft as shown in the graph of FIG.
【００５４】実施例６ 実施例５で作製した４層マグネットを１０ｋガウスの外
部磁場中に配置し、液体窒素を投入し７７Ｋに冷却し
た。そして外部磁場と同じ方向に磁場が発生するように
通電した。このとき２４５Ａ通電した時に超伝導体の一
部が焼損した。焼損した部分は第２層目の中間から２巻
目であり、超伝導相（１２３相）は熱により完全に分解
していた。Example 6 The four-layer magnet produced in Example 5 was placed in an external magnetic field of 10 k Gauss, liquid nitrogen was charged, and it was cooled to 77K. Then, electricity was applied so that a magnetic field was generated in the same direction as the external magnetic field. At this time, a part of the superconductor was burnt out when a current of 245 A was applied. The burned-out portion was from the middle to the second roll of the second layer, and the superconducting phase (123 phase) was completely decomposed by heat.
【００５５】そこで渦巻の形状を図１３のように線の幅
を中心部５ｍｍ、中間部４．５ｍｍ、外周部４ｍｍと
し、他の条件を実施例２と同様にして渦巻状コイルを作
製した。このときコイルの厚さを４ｍｍと３．５ｍｍの
２種類にした。そして１層目と４層目を厚さ３．５ｍｍ
にし、２層目と３層目を厚さ４ｍｍのものを用いた。実
施例５と同様に４つの層を接続し、補強した。Then, as shown in FIG. 13, a spiral coil was produced under the same conditions as in Example 2 except that the width of the spiral was 5 mm in the center, 4.5 mm in the middle, and 4 mm in the outer circumference. At this time, there were two types of coil thickness, 4 mm and 3.5 mm. The thickness of the first and fourth layers is 3.5 mm
The second and third layers were 4 mm thick. Four layers were connected and reinforced as in Example 5.
【００５６】この４層マグネットを１０ｋガウスの外部
磁場中に配置し、液体窒素を投入し７７Ｋに冷却した。
そして外部磁場と同じ方向に磁場が発生するように通電
した。このとき４００Ａ通電することができ中心部にお
いて外部磁場と合わせて１３．８ｋガウスを記録した。
このことから、中心部でより大きい断面積を有するマグ
ネットが断面積がすべて同じものに比べ優れていること
がわかった。This four-layer magnet was placed in an external magnetic field of 10 kGauss, liquid nitrogen was charged, and the temperature was cooled to 77K.
Then, electricity was applied so that a magnetic field was generated in the same direction as the external magnetic field. At this time, a current of 400 A could be applied, and 13.8 kGauss was recorded in the central part together with the external magnetic field.
From this, it was found that a magnet having a larger cross-sectional area in the central portion was superior to those having the same cross-sectional area.
【００５７】実施例７ Ａｇペーストによる電極作製工程およびエポキシ樹脂に
よる補強工程を省いた他は実施例２と同じ方法で作製し
たＹ系渦巻状コイルを厚さ０．２ｍｍのＰｔ製のスペー
サーを配し先の図１１（ｂ）に示したものと同様に４枚
積層した。この時１層目と３層目のコイル１Ａ，１Ｃは
上から見て時計回りに電流２が流れたときに中心から外
へ流れる向きになっており、また２層目と４層目のコイ
ル１Ｂ，１Ｄから外から中心に向かうように積層した。
そして１層目の中心部の端と２層目の中心部の端とを図
１４のように加工し、Ｙｂ系前駆体１３を配置した。ま
た同様に２層目の外側の端と３層目の外側の端の間、３
層目の内側の端と４層目の内側の端の間においても同様
の加工およびＹｂ系前駆体の配置を行った。またＡｇペ
ーストを１および４層目の外側の端に塗布した。Example 7 A Y-based spiral coil manufactured by the same method as in Example 2 except that the electrode manufacturing process using Ag paste and the reinforcing process using epoxy resin were omitted was provided with a Pt spacer having a thickness of 0.2 mm. Then, four sheets were laminated in the same manner as that shown in FIG. 11 (b). At this time, the coils 1A and 1C of the first and third layers are oriented so that the current 2 flows clockwise from the center when viewed from above, and the coils of the second and fourth layers are also oriented. The layers 1B and 1D were laminated from the outside toward the center.
Then, the end of the central portion of the first layer and the end of the central portion of the second layer were processed as shown in FIG. 14 to dispose the Yb-based precursor 13. Similarly, between the outer edge of the second layer and the outer edge of the third layer, 3
Similar processing and placement of the Yb-based precursor were performed between the inner edge of the fourth layer and the inner edge of the fourth layer. Also, Ag paste was applied to the outer edges of the first and fourth layers.
【００５８】このように積層されたコイルおよび前駆体
は炉内に配置され、大気中で９６０℃まで８時間で昇温
された。この温度で５分保持された後、９３０℃まで２
時間で冷却、さらに８７０℃まで１２０時間かけて冷却
した。さらに酸素気流中で７００℃から３５０℃まで６
０時間かけて冷却した後、室温まで冷却した。炉内から
慎重に取り出した後、補強のためにエポキシ樹脂を導体
間および層間の一部に充填し硬化させた。十分硬化させ
た後、スペーサーのＰｔ板を抜き取った。また１層目と
４層目の外側のＡｇ電極に直流電源の電流リードを低融
点半田を用いて接続した。The coil and the precursor thus laminated were placed in a furnace and heated to 960 ° C. in the atmosphere for 8 hours. After being held at this temperature for 5 minutes, 2 up to 930 ° C
It was cooled in time, and further cooled to 870 ° C. in 120 hours. Furthermore, in an oxygen stream from 700 to 350 ° C 6
After cooling for 0 hours, it was cooled to room temperature. After careful removal from the furnace, epoxy resin was filled and cured between the conductors and a part of the layers for reinforcement. After curing sufficiently, the Pt plate of the spacer was taken out. Further, the current leads of the DC power supply were connected to the Ag electrodes on the outer sides of the first and fourth layers using low melting point solder.
【００５９】この４層マグネットを液体窒素中に浸し、
マグネットが７７Ｋまで十分冷却された後、５００Ａ通
電した。層間の接続部で窒素の沸騰にはほとんど変化が
なかった。マグネットは、軸上で図１５のような磁界分
布を発生した。Immerse this four-layer magnet in liquid nitrogen,
After the magnet was sufficiently cooled to 77K, 500A was energized. There was almost no change in the boiling of nitrogen at the connection between the layers. The magnet generated a magnetic field distribution on the shaft as shown in FIG.
【００６０】実施例８ Ａｇペーストによる電極作製工程およびエポキシ樹脂に
よる補強工程を省いた他は実施例２と同じ方法で作製し
たＹ系渦巻状コイルおよび板状のＹ系ＱＭＧ材料を図１
６のように厚さ０．２ｍｍのＰｔ製のスペーサーを層間
に配し４枚積層した。この時１層目と３層目のコイル１
Ａ，１Ｂは上から見て時計回りに電流が流れたとき中心
から外へ流れる向きになっており、また２層目と４層目
のコイル１Ｂ，１Ｄは外から中心に向かうように積層し
た。そして１層目の中心部の端と２層目の中心部の端と
を先の図１４と同様に加工し、Ｙｂ系前駆体を配置し
た。また同様に２層目の外側の端と３層目の外側の端の
間、３層目の内側の端と４層目の内側の端の間において
も同様の加工およびＹｂ系前駆体の配置を行った。Example 8 A Y-based spiral coil and a plate-shaped Y-based QMG material produced in the same manner as in Example 2 except that the step of forming an electrode with Ag paste and the step of reinforcing with an epoxy resin were omitted are shown in FIG.
As in No. 6, a Pt spacer having a thickness of 0.2 mm was arranged between the layers and four sheets were laminated. At this time, the coil 1 of the first layer and the third layer
A and 1B are oriented so that the current flows from the center to the outside when the current flows clockwise when viewed from above, and the coils 1B and 1D of the second and fourth layers are laminated from the outside to the center. . Then, the end of the central portion of the first layer and the end of the central portion of the second layer were processed in the same manner as in FIG. 14 above, and the Yb-based precursor was placed. Similarly, between the outer edge of the second layer and the outer edge of the third layer, similar processing and placement of the Yb-based precursor are also performed between the inner edge of the third layer and the inner edge of the fourth layer. I went.
【００６１】また図１６および図１７に示したように１
および４層目の外側の端部と板状ＱＭＧ材料の両端部に
おいても同様のくぼみ加工１４およびＹｂ系の前駆体１
３を配置した。このとき、板状ＱＭＧ材料１９は１およ
び４層目のＱＭＧコイル材１Ａ，１Ｄと結晶方位がほぼ
一致するように配置した。またＡｇペースト１８を１お
よび４層目の外側の端に塗布した。As shown in FIGS. 16 and 17, 1
Also at the outer end of the fourth layer and at both ends of the plate-shaped QMG material, similar indentation processing 14 and Yb-based precursor 1
3 was placed. At this time, the plate-shaped QMG material 19 was arranged so that the crystal orientations of the QMG coil materials 1A and 1D of the first and fourth layers were substantially the same. Also, Ag paste 18 was applied to the outer edges of the first and fourth layers.
【００６２】このように積層されたコイルおよび前駆体
は炉内に配置され、大気中で９６０℃まで８時間で昇温
された。この温度で５分保持された後、９３０℃まで２
時間で冷却さらに８７０℃まで１２０時間かけて冷却し
た。さらに酸素気流中で７００から３５０℃まで６０時
間かけて冷却した後、室温まで冷却した。炉内から慎重
に取り出した後、補強のためにエポキシ樹脂を導体間お
よび層間の一部に充填し硬化させた。十分硬化させた
後、スペーサーのＰｔ板を抜き取った。接続された板状
ＱＭＧ材料に発熱体としてマンガニン線を５０回巻き付
け、エポキシ樹脂により固定し、超伝導スイッチを作製
した。また１層目と４層目の外側のＡｇ電極に直流電源
の電流リードを低温半田を用いて接続した。The coil and the precursor thus laminated were placed in a furnace and heated to 960 ° C. in the atmosphere for 8 hours. After being held at this temperature for 5 minutes, 2 up to 930 ° C
Cooling in hours Further cooling to 870 ° C. over 120 hours. After further cooling in an oxygen stream from 700 to 350 ° C. for 60 hours, it was cooled to room temperature. After careful removal from the furnace, epoxy resin was filled and cured between the conductors and a part of the layers for reinforcement. After curing sufficiently, the Pt plate of the spacer was taken out. A manganin wire as a heating element was wound around the connected plate-shaped QMG material 50 times and fixed with an epoxy resin to manufacture a superconducting switch. Further, the current leads of the DC power supply were connected to the Ag electrodes on the outer sides of the first layer and the fourth layer using low temperature solder.
【００６３】この４層マグネットを液体窒素中に浸し、
マグネットが７７Ｋまで十分冷却し、マンガニン線に８
Ａ通電し一部常伝導状態にした後、マグネットに５００
Ａ通電した。その後マンガニン線への通電をやめ、マグ
ネットへの通電を１００Ａ／ｍｉｎで減らしゼロにし
た。マグネットは、通電電流をゼロにしてから約３０秒
後、軸上で図１８のような磁界分布を発生した。これに
より永久電流モードでの動作が確認された。Immerse this four-layer magnet in liquid nitrogen,
The magnet cools well to 77K, and the manganin wire is 8
After energizing A and making it partly normal conduction, 500 on the magnet
A was energized. After that, the power supply to the manganin wire was stopped and the power supply to the magnet was reduced to 100 A / min to zero. The magnet generated a magnetic field distribution as shown in FIG. 18 on the axis about 30 seconds after the applied current was zero. This confirmed the operation in the persistent current mode.
【００６４】[0064]
【発明の効果】以上詳述したごとく本発明は、高品位の
酸化物超伝導マグネットを可能にするもので各種分野で
の応用が可能であり、極めて工業的効果が大きい。具体
例としては、実験用各種マグネット、モーター内の励磁
用マグネット、加速器用マグネット、核磁気共鳴用マグ
ネット等があげられる。As described above in detail, the present invention enables a high-quality oxide superconducting magnet, can be applied in various fields, and has a great industrial effect. Specific examples thereof include various experimental magnets, excitation magnets in motors, accelerator magnets, nuclear magnetic resonance magnets, and the like.
【図１】渦巻状コイルの外観を示す（ａ）平面図および
（ｂ）側面図FIG. 1A is a plan view and FIG. 1B is a side view showing the appearance of a spiral coil.
【図２】渦巻状コイルの形状と結晶方位との関係を示す
図FIG. 2 is a diagram showing the relationship between the shape of a spiral coil and the crystal orientation.
【図３】渦巻状コイルの積層方法の例を示す図FIG. 3 is a diagram showing an example of a method of stacking spiral coils.
【図４】渦巻状コイルの積層方法の例を示す図で、
（ａ）積層前、（ｂ）積層後を示すFIG. 4 is a diagram showing an example of a method of stacking spiral coils,
(A) Before lamination, (b) After lamination
【図５】前駆体の加工方法の例を示す図FIG. 5 is a diagram showing an example of a precursor processing method.
【図６】前駆体の加工方法の例を示す図で、（ａ）全体
図、（ｂ）一部を拡大した平面図FIG. 6 is a diagram showing an example of a precursor processing method, in which (a) an overall view and (b) a partially enlarged plan view.
【図７】炉内に配置された前駆体を示す図FIG. 7 is a diagram showing a precursor placed in a furnace.
【図８】超伝導接合の方法の例を示す図で、（ａ）コイ
ルの接合部における加工、（ｂ）熱処理後の接合部分、
（ｃ）図（ｂ）の一部拡大を示すFIG. 8 is a diagram showing an example of a superconducting joining method, in which (a) processing at the joining portion of the coil, (b) joining portion after heat treatment,
(C) shows a partial enlargement of FIG.
【図９】渦巻コイルのＡｇペーストおよび補強用樹脂の
一例を示す図FIG. 9 is a view showing an example of a Ag paste of a spiral coil and a reinforcing resin.
【図１０】熱硬化性樹脂で補強された渦巻コイルの例を
示す図FIG. 10 is a view showing an example of a spiral coil reinforced with a thermosetting resin.
【図１１】渦巻状コイルの積層方法の例を示す図で、
（ａ）積層前、（ｂ）積層後を示すFIG. 11 is a diagram showing an example of a method of stacking spiral coils,
(A) Before lamination, (b) After lamination
【図１２】本発明の超伝導マグネットの軸上の磁場分布
の例を示すグラフFIG. 12 is a graph showing an example of the magnetic field distribution on the axis of the superconducting magnet of the present invention.
【図１３】外側の導体の断面積が内側の導体の断面積に
比べ小さくなっている渦巻コイルの例を示す図FIG. 13 is a diagram showing an example of a spiral coil in which the cross-sectional area of the outer conductor is smaller than the cross-sectional area of the inner conductor.
【図１４】超伝導接合方法の例を示す図FIG. 14 is a diagram showing an example of a superconducting joining method.
【図１５】本発明の超伝導マグネットの軸上の磁場分布
の例を示すグラフFIG. 15 is a graph showing an example of the magnetic field distribution on the axis of the superconducting magnet of the present invention.
【図１６】超伝導接続された積層コイルを示す図FIG. 16 is a diagram showing a laminated coil connected in a superconducting manner.
【図１７】図１６の積層コイルの一部分の超伝導接合方
法を示す図FIG. 17 is a diagram showing a superconducting joining method for a portion of the laminated coil shown in FIG. 16;
【図１８】本発明の超伝導マグネットの軸上の磁場分布
の例を示すグラフFIG. 18 is a graph showing an example of the magnetic field distribution on the axis of the superconducting magnet of the present invention.
【符号の説明】 １，１Ａ，１Ｂ，１Ｃ，１Ｄ コイル ２ 電流 ３ ｃ軸の方位 ４ 導体 ５ 接続部分 ６，９，１０，１１，１３ 前駆体 ７ 切れ込み ８ 切り残した部分 １２ 接続部分 １４ くぼみ １５ 超伝導体 １６ １２３相の結晶 １７ エポキシ樹脂 １８ Ａｇペースト １９ ＱＭＧ材料 ２０ 支持材 ２１Ａ，２１Ｂ 電極 Ｎ コイルを形成する面の法線[Explanation of symbols] 1,1A, 1B, 1C, 1D Coil 2 Current 3 c-axis direction 4 Conductor 5 Connection part 6,9,10,11,13 Precursor 7 Notch 8 Uncut part 12 Connection part 14 Recess 15 Superconductor 16 12 3 Phase Crystal 17 Epoxy Resin 18 Ag Paste 19 QMG Material 20 Supporting Material 21A, 21B Electrode N Normal of Surface Forming Coil
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｈ０１Ｂ 13/00 ５６５ Ｄ Ｈ０１Ｆ 6/00 ＺＡＡ 41/04 Ｚ ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification number Internal reference number FI Technical indication H01B 13/00 565 D H01F 6/00 ZAA 41/04 Z
Claims (19)
（ＲＥはＹを含む希土類元素およびそれらの組み合わ
せ）中にＲＥ2 ＢａＣｕＯ5 が微細分散した組織を有
し、渦巻状のコイル形状を有することを特徴とする超伝
導マグネット。1. A spiral coil having a structure in which RE 2 BaCuO 5 is finely dispersed in a single crystalline REBa 2 Cu 3 O 7-X phase (RE is a rare earth element containing Y and a combination thereof). A superconducting magnet having a shape.
ｃ軸の方向が４０度以内に揃っており、かつ微量のＰｔ
またはＲｈの少なくとも一方を含有することを特徴とす
る請求項１に記載の超伝導マグネット。2. The REBa 2 Cu 3 O 7-X phase has a crystallographic orientation in which the c-axis direction is aligned within 40 degrees and a small amount of Pt.
Alternatively, the superconducting magnet according to claim 1, containing at least one of Rh.
ｃ軸が渦巻を構成する平面の法線に対して２０度以内に
揃っていることを特徴とする請求項１または２に記載の
超伝導マグネット。 3. The crystallographic c-axis of the REBa 2 Cu 3 O 7-X phase is aligned within 20 degrees with respect to the normal to the plane forming the spiral, according to claim 1 or 2. The superconducting magnet described.
面積に比べて大きくなっていることを特徴とする請求項
１ないし３のいずれかに記載の超伝導マグネット。4. The superconducting magnet according to claim 1, wherein the cross-sectional area of the inner line of the spiral is larger than that of the outer line.
とも一部に樹脂が存在することによって補強されている
ことを特徴とする請求項１ないし４のいずれかに記載の
超伝導マグネット。5. The superconducting magnet according to claim 1, wherein the superconducting magnet is reinforced by the presence of resin in at least a part of the gap of the superconductor forming the spiral.
巻状のコイルが複数積層されていることを特徴とする超
伝導マグネット。6. A superconducting magnet, wherein a plurality of spiral coils according to claim 1 are stacked.
左巻き）が交互になっていることを特徴とする請求項６
に記載の超伝導マグネット。7. The spiral direction (right-handed or left-handed) of adjacent layers is alternated.
Superconducting magnet described in.
端部間が高電気伝導率を有する金属により接続されてい
ることを特徴とする請求項６または７に記載の超伝導マ
グネット。8. The superconducting magnet according to claim 6, wherein the ends of each of the laminated spiral coils are connected by a metal having a high electric conductivity.
端部間がコイル導体のＴｆ（ＲＥＢａ2 Ｃｕ3 Ｏ7-X 相
の生成温度）より低いＴｆを有する超伝導体であるＲＥ
Ｂａ2 Ｃｕ3 Ｏ7-X 相により接続されていることを特徴
とする請求項６または７に記載の超伝導マグネット。9. A RE, which is a superconductor having a Tf between the ends of each of the laminated spiral coils that is lower than the Tf (REBa 2 Cu 3 O 7 -X phase formation temperature) of the coil conductor.
The superconducting magnet according to claim 6 or 7, wherein the superconducting magnets are connected by a Ba 2 Cu 3 O 7-X phase.
が端部の渦巻状のコイルの層の厚さより厚くなっている
ことを特徴とする請求項６ないし９のいずれかに記載の
超伝導マグネット。10. The spiral coil layer at the central portion is thicker than the spiral coil layer at the end portion, according to any one of claims 6 to 9. Superconducting magnet.
一部に樹脂が存在することによって補強されていること
を特徴とする請求項６ないし１０のいずれかに記載の超
伝導マグネット。11. The superconducting magnet according to claim 6, wherein the spiral coil is reinforced by the presence of resin in at least a part of the layers between the spiral coils.
の１または複数の渦巻状コイルによって形成されたコイ
ルの始端と終端とを単結晶状のＲＥＢａ2 Ｃｕ3 Ｏ7-X
相中にＲＥ2 ＢａＣｕＯ5 が微細分散した組織を有する
酸化物超伝導材料を用いて接続することによって超伝導
体からなる閉回路を構成し、かつ電流導入端子および超
伝導スイッチからなることを特徴とする超伝導マグネッ
ト。12. A single crystal REBa 2 Cu 3 O 7-X having a starting end and an ending end of a coil formed by one or a plurality of spiral coils according to any one of claims 1 to 11.
A closed circuit composed of a superconductor is formed by connecting an oxide superconducting material having a structure in which RE 2 BaCuO 5 is finely dispersed in the phase, and is composed of a current introducing terminal and a superconducting switch. And a superconducting magnet.
中にＲＥ2 ＢａＣｕＯ5 が微細分散した組織を有する酸
化物超伝導材料から板状に切り出した後に切れ目を入れ
ることにより渦巻状のコイル形状に加工することを特徴
とする超伝導マグネットの製造方法。13. A spiral shape is obtained by cutting a plate-shaped oxide superconducting material having a structure in which RE 2 BaCuO 5 is finely dispersed in a single-crystal REBa 2 Cu 3 O 7-X phase and then making a cut. A method for manufacturing a superconducting magnet, which is characterized in that it is processed into a coil shape.
固定した後、ウォータージェットカッティングにより渦
巻加工することを特徴とする請求項１３に記載の超伝導
マグネットの製造方法。14. The method for manufacturing a superconducting magnet according to claim 13, wherein the plate-shaped superconductor is fixed to the support base with an adhesive and then spirally processed by water jet cutting.
体から成形体を作製し、成形体を渦巻状のコイル形状に
加工した後、これを２１１相と液相からなる半溶融状態
に加熱し、その後酸化性雰囲気中で徐冷することで単結
晶状のＲＥＢａ2 Ｃｕ3 Ｏ7-X 相中にＲＥ2 ＢａＣｕＯ
5 が微細分散した組織を有する超伝導材料を形成せしめ
ることを特徴とする超伝導マグネットの製造方法。15. A molded body is produced from a precursor containing oxides of RE, Ba, and Cu, and the molded body is processed into a spiral coil shape, which is then made into a semi-molten state consisting of a 211 phase and a liquid phase. By heating and then slowly cooling in an oxidizing atmosphere, RE 2 BaCuO is formed in the single crystal REBa 2 Cu 3 O 7-X phase.
5. A method for manufacturing a superconducting magnet, wherein 5 forms a superconducting material having a finely dispersed structure.
覆うように前駆体を配置し、これらを２１１相と液相か
らなる半溶融状態に加熱し、次に種結晶により結晶方位
を制御し、酸化性雰囲気中で徐冷することを特徴とする
請求項１５に記載の超伝導マグネットの製造方法。16. A precursor is disposed on a spirally formed body so as to cover the spirally formed body, these are heated to a semi-molten state composed of a 211 phase and a liquid phase, and then a crystal orientation is obtained by a seed crystal. 16. The method for producing a superconducting magnet according to claim 15, wherein the temperature is controlled and gradually cooled in an oxidizing atmosphere.
載の方法により作製された渦巻状のコイルを渦巻の方向
（右巻きまたは左巻き）が交互になるように積層し、各
コイルを電気的に接続することを特徴とする超伝導マグ
ネットの製造方法。17. A spiral coil produced by the method according to claim 13 is laminated so that the spiral directions (right-handed or left-handed) alternate, and each coil is electrically connected. A method for manufacturing a superconducting magnet, characterized by connecting.
るように、コイル導体のＴｆより低いＴｆを有する超伝
導相であるＲＥＢａ2 Ｃｕ3 Ｏ7-X 相によりそれぞれの
渦巻状のコイルの端部間を接続することを特徴とする請
求項１７に記載の超伝導マグネットの製造方法。18. The spiral coil of each REBA 2 Cu 3 O 7-X phase, which is a superconducting phase having a Tf lower than the Tf of the coil conductor, so that the entire laminated coil becomes a superconductor. The method for manufacturing a superconducting magnet according to claim 17, wherein the ends are connected to each other.
載の方法によって形成されたコイルの始端と終端とを単
結晶状のＲＥＢａ2 Ｃｕ3 Ｏ7-X 相中にＲＥ2 ＢａＣｕ
Ｏ5 が微細分散した組織を有する超伝導材料により接続
することを特徴とする超伝導マグネットの製造方法。19. The method of claim 13 to 18 RE 2 BaCu the beginning and end of the coil formed by the method described in the single crystalline REBa 2 Cu 3 O 7-X phase either
A method for manufacturing a superconducting magnet, which comprises connecting with a superconducting material having a structure in which O 5 is finely dispersed.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5828394A JP3794591B2 (en) | 1994-03-04 | 1994-03-04 | Manufacturing method of superconducting magnet |
| CNB951903039A CN1152396C (en) | 1994-03-04 | 1995-03-03 | Superconducting magnet and production method thereof |
| PCT/JP1995/000351 WO1995024047A1 (en) | 1994-03-04 | 1995-03-03 | Superconducting magnet and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5828394A JP3794591B2 (en) | 1994-03-04 | 1994-03-04 | Manufacturing method of superconducting magnet |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2006044723A Division JP2006222435A (en) | 2006-02-22 | 2006-02-22 | Superconducting magnet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07245211A true JPH07245211A (en) | 1995-09-19 |
| JP3794591B2 JP3794591B2 (en) | 2006-07-05 |
Family
ID=13079870
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5828394A Expired - Lifetime JP3794591B2 (en) | 1994-03-04 | 1994-03-04 | Manufacturing method of superconducting magnet |
Country Status (3)
| Country | Link |
|---|---|
| JP (1) | JP3794591B2 (en) |
| CN (1) | CN1152396C (en) |
| WO (1) | WO1995024047A1 (en) |
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| JP2005191538A (en) * | 2003-12-02 | 2005-07-14 | Nippon Steel Corp | Working method of oxide superconductor, oxide superconductive element and superconducting magnet |
| JP2006332577A (en) * | 2005-04-28 | 2006-12-07 | Nippon Steel Corp | Oxide superconductor coil, its manufacturing method, its exciting method, its cooling method and magnet system |
| JP2009170550A (en) * | 2008-01-11 | 2009-07-30 | Nippon Steel Corp | Oxide superconducting magnet, its manufacturing method, and cooling method |
| WO2011071071A1 (en) * | 2009-12-08 | 2011-06-16 | 新日本製鐵株式会社 | Oxide superconducting bulk magnet member |
| JP2011142303A (en) * | 2009-12-08 | 2011-07-21 | Nippon Steel Corp | Oxide superconducting bulk magnet member |
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| JPH05315127A (en) * | 1992-05-06 | 1993-11-26 | Sumitomo Heavy Ind Ltd | Manufacture of superconducting coil |
-
1994
- 1994-03-04 JP JP5828394A patent/JP3794591B2/en not_active Expired - Lifetime
-
1995
- 1995-03-03 WO PCT/JP1995/000351 patent/WO1995024047A1/en active Application Filing
- 1995-03-03 CN CNB951903039A patent/CN1152396C/en not_active Expired - Lifetime
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Also Published As
| Publication number | Publication date |
|---|---|
| CN1152396C (en) | 2004-06-02 |
| WO1995024047A1 (en) | 1995-09-08 |
| CN1127050A (en) | 1996-07-17 |
| JP3794591B2 (en) | 2006-07-05 |
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