JPH02296778A - Production of ceramic superconductor - Google Patents
Production of ceramic superconductorInfo
- Publication number
- JPH02296778A JPH02296778A JP1119553A JP11955389A JPH02296778A JP H02296778 A JPH02296778 A JP H02296778A JP 1119553 A JP1119553 A JP 1119553A JP 11955389 A JP11955389 A JP 11955389A JP H02296778 A JPH02296778 A JP H02296778A
- Authority
- JP
- Japan
- Prior art keywords
- ceramic
- fired
- superconductor
- superconducting
- ceramic superconductor
- 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.)
- Pending
Links
- 239000000919 ceramic Substances 0.000 title claims abstract description 49
- 239000002887 superconductor Substances 0.000 title claims abstract description 37
- 238000004519 manufacturing process Methods 0.000 title claims description 17
- 238000000034 method Methods 0.000 claims abstract description 9
- 239000000758 substrate Substances 0.000 claims description 15
- 238000010304 firing Methods 0.000 claims description 10
- 238000000465 moulding Methods 0.000 claims 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 abstract description 13
- 239000001301 oxygen Substances 0.000 abstract description 13
- 229910052760 oxygen Inorganic materials 0.000 abstract description 13
- 239000000463 material Substances 0.000 abstract description 9
- 239000000843 powder Substances 0.000 abstract description 9
- 239000011230 binding agent Substances 0.000 abstract description 5
- 238000001354 calcination Methods 0.000 abstract description 5
- 238000005304 joining Methods 0.000 abstract description 4
- 238000005245 sintering Methods 0.000 abstract description 4
- 239000002904 solvent Substances 0.000 abstract description 4
- 229920002037 poly(vinyl butyral) polymer Polymers 0.000 abstract description 3
- 229910021521 yttrium barium copper oxide Inorganic materials 0.000 abstract description 3
- WUOACPNHFRMFPN-UHFFFAOYSA-N alpha-terpineol Chemical compound CC1=CCC(C(C)(C)O)CC1 WUOACPNHFRMFPN-UHFFFAOYSA-N 0.000 abstract description 2
- SQIFACVGCPWBQZ-UHFFFAOYSA-N delta-terpineol Natural products CC(C)(O)C1CCC(=C)CC1 SQIFACVGCPWBQZ-UHFFFAOYSA-N 0.000 abstract description 2
- 239000008188 pellet Substances 0.000 abstract description 2
- 229940116411 terpineol Drugs 0.000 abstract description 2
- 238000007723 die pressing method Methods 0.000 abstract 1
- 235000011837 pasties Nutrition 0.000 abstract 1
- 239000007858 starting material Substances 0.000 abstract 1
- 239000002131 composite material Substances 0.000 description 10
- 150000001875 compounds Chemical class 0.000 description 5
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 239000002002 slurry Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 3
- 229910052747 lanthanoid Inorganic materials 0.000 description 3
- 150000002602 lanthanoids Chemical class 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- -1 J+0+o Chemical class 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910014454 Ca-Cu Inorganic materials 0.000 description 1
- 229910052691 Erbium Inorganic materials 0.000 description 1
- 229910052688 Gadolinium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 238000005481 NMR spectroscopy Methods 0.000 description 1
- 229910052769 Ytterbium Inorganic materials 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000002270 dispersing agent Substances 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000010030 laminating Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000000149 penetrating effect Effects 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Landscapes
- Ceramic Products (AREA)
- Compositions Of Oxide Ceramics (AREA)
- Inorganic Compounds Of Heavy Metals (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は複数のセラミック超電導基材を接合して一体で
一様な特性のセラミック超電導体を製造する方法に関す
る。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a method for manufacturing an integral ceramic superconductor having uniform characteristics by bonding a plurality of ceramic superconducting substrates.
［従来の技術］
近年、セラミック超電導体は高い臨界温度を示すことで
注目を集め、電力分野、核磁気共鳴装置、磁気シールド
等の各分野ての用途か期待されている。[Prior Art] In recent years, ceramic superconductors have attracted attention due to their high critical temperature, and are expected to be used in various fields such as electric power, nuclear magnetic resonance devices, and magnetic shielding.
これらセラミック超電導体で各種機能部品を構成する場
合、特に磁気シールド用に使用する大型部品を構成する
場合、セラミック超電導体は一体で−様な特性を保有す
ることが好ましい。しかしながら、これら大型部品ある
いは異形部品を一体的に製造することは実際には困難で
あり、通常各パーツを作製し、次いでこれら各パーツを
接合し一体物を得ることにより、大型部品あるいは異形
部品を製造することか考えられる。When constructing various functional parts using these ceramic superconductors, especially when constructing large components used for magnetic shielding, it is preferable that the ceramic superconductor be integrated and have similar characteristics. However, it is actually difficult to manufacture these large parts or irregularly shaped parts in an integrated manner.Usually, large parts or irregularly shaped parts are manufactured by manufacturing each part and then joining these parts to obtain an integrated product. I can think of manufacturing it.
現在、セラミック超電導基材（部材）の接合においては
、被接合セラミック超電導基材と同一組成のセラミック
超電導体を接合層とすることが知られている。Currently, in bonding ceramic superconducting substrates (members), it is known to use a ceramic superconductor having the same composition as the ceramic superconducting substrates to be bonded as a bonding layer.
さらに、被接合セラミック超電導基材とその接合層との
密着性改善のために非超電導体を一部添加することか知
られている。Furthermore, it is known to add a portion of a non-superconductor to improve the adhesion between the ceramic superconducting substrate to be bonded and its bonding layer.
［発明か解決しようとする課題］
しかしなから、前者の場合、被接合セラミック超電導基
材として超電導特性を有する焼成体を用い、これを同一
・組成の接合形成層て仮接合し、超電導特性を出現させ
る焼成条件て本焼成しているため、得られた焼成体（超
電導体）に於いては接合か良好でなく、しかも機械的強
度および臨界電流密度（Ｊｃ）か低いという問題があっ
た。[Problem to be solved by the invention] However, in the former case, a fired body having superconducting properties is used as the ceramic superconducting base material to be joined, and this is temporarily joined with a bond forming layer of the same composition to improve the superconducting properties. Since the main firing was performed under the firing conditions to produce the superconductor, the resulting fired body (superconductor) had problems in that the bonding was not good and the mechanical strength and critical current density (Jc) were low.
又、後者においては接合層に非超電導体を含ませるため
、超電導特性か著しく劣化し実用的ではない。In addition, in the latter case, since the bonding layer contains a non-superconductor, the superconducting properties are significantly deteriorated, making it impractical.
従って、本発明は前記従来の製造法の問題を解決した、
超電導特性が−様で、一体的に構成された接合セラミッ
ク超電導体を製造する方法を提供することを目的とする
。Therefore, the present invention solves the problems of the conventional manufacturing method.
It is an object of the present invention to provide a method for manufacturing an integrally constructed bonded ceramic superconductor with -like superconducting properties.
［課題を解決するための手段］
そしてその目的は、本発明によれば、複数のセラミック
超電導基材を接合して一体で−様な特性のセラミック超
電導体を製造する方法てあって、被接合セラミック超電
導基材を仮焼成し、次いてこれらの仮焼成成形体を該成
形体と同一の成分を含む接合成形層で仮接合して一体の
成形体を得た後、該成形体を焼成することにより、超電
導特性を有するセラミック超電導体を得ることを特徴と
するセラミック超電導体の製法、により達成される。[Means for Solving the Problems] According to the present invention, there is provided a method for manufacturing a ceramic superconductor having similar characteristics by joining a plurality of ceramic superconducting substrates together. The ceramic superconducting base material is pre-fired, and then these pre-fired molded bodies are temporarily joined with a bonding layer containing the same components as the molded body to obtain an integral molded body, and then the molded body is fired. This is achieved by a method for producing a ceramic superconductor characterized by obtaining a ceramic superconductor having superconducting properties.
以下、本発明について詳細に説明する。The present invention will be explained in detail below.
本発明のセラミック超電導体は、例えばＭ−ＲａＣｕ−
０県北合物（但し、ＭはＳｃ、 Ｔｌ、Ｙ及びｈａ、Ｅ
ｕ、 Ｇｄ、Ｅｒ、 Ｙｂ、Ｌｕ等のランタニドから選
ばれる一種以上を表わす。）及びＢ１−３ｒ−Ｃａ−Ｃ
ｕ系化合物等の多層ベロフスカイト構造を有するもので
ある。The ceramic superconductor of the present invention is, for example, M-RaCu-
0 Prefecture Kitaai Mono (However, M is Sc, Tl, Y, ha, E
Represents one or more lanthanides selected from lanthanides such as u, Gd, Er, Yb, and Lu. ) and B1-3r-Ca-C
It has a multilayer belovskite structure such as a U-based compound.
例えば、ＹＢａ２Ｃｕ３Ｏ７、ＬａＢａ２Ｃｕ：＋０７
等Ｍ−ＢａＪ：ｕ−０県北合物のＭかランタニド金属で
ある場合には、超電導特性を示す最適焼成温度は９２０
〜９６０°Ｃてあり、接合されるセラミック超電導基材
の仮焼成温度はこの温度よりも低いことが必要である。For example, YBa2Cu3O7, LaBa2Cu: +07
Etc. M-BaJ: u-0 When M from Kenhokugoi is a lanthanide metal, the optimum firing temperature that exhibits superconducting properties is 920
~960°C, and the temporary firing temperature of the ceramic superconducting substrates to be joined must be lower than this temperature.
具体的な仮焼成温度としては、好ましくは７５０〜９０
０℃か良い。また、この材料の場合、焼成中の酸素分圧
により臨界電流密度Ｊｃが影響を受ける。酸素分圧か１
〜１０ａｔｍのときに臨界電流密度Ｊｃが良好となるの
で、仮焼成条件としては酸素分圧を例えばｌａｔｍに下
げて焼成することにより仮焼体を得ることもてきる。The specific calcining temperature is preferably 750 to 90
0℃ is good. Furthermore, in the case of this material, the critical current density Jc is affected by the oxygen partial pressure during firing. Oxygen partial pressure 1
Since the critical current density Jc becomes good when the temperature is 10 atm to 10 atm, a calcined body can be obtained by lowering the oxygen partial pressure to, for example, latm as the calcining conditions.
又Ｂｉ２５ｒ２ＣａＣｕＯ，、Ｂｉ２５ｒ２Ｃａ２ＣＩ
Ｊ＋０＋ｏ等Ｂ１−３ｒ−Ｃａ−Ｃｕ系化合物、及びこ
の化合物に更にｐｂあるいは／及びｓｂを添加した化合
物の場合には、構成成分を含んで半融状態あるいは溶融
状態とする工程を経た後、溶融温度以下、酸素存在下で
熱処理すると良好なセラミック超電導体を得ることが知
られている。従って、この材料の場合の仮焼成体は半融
あるいは溶融状態になる温度以下で仮焼成することによ
り得られる。これらは融点か９２０°Ｃ近傍にあるため
、仮焼成温度は７５０°Ｃ〜９００°Ｃか好ましい。又
、熱処理時に、上記化合物からなる超電導体か超電導特
性を生じる条件よりも酸素分圧を下げた状態で焼成する
ことによっても仮焼結体か得られる。Also Bi25r2CaCuO, Bi25r2Ca2CI
In the case of B1-3r-Ca-Cu-based compounds such as J+0+o, and compounds in which pb or/and sb is further added to this compound, after a step of containing the constituent components and making it into a semi-molten state or a molten state, it is melted. It is known that a good ceramic superconductor can be obtained by heat treatment in the presence of oxygen at a temperature below this temperature. Therefore, a calcined body of this material can be obtained by calcining it at a temperature below which the material becomes half-molten or molten. Since these have melting points near 920°C, the pre-calcination temperature is preferably 750°C to 900°C. Further, a pre-sintered body can also be obtained by firing the superconductor made of the above compound at a lower oxygen partial pressure than the conditions under which superconducting properties are produced during heat treatment.
本発明により得られるセラミック超電導体は、全体が同
一組成から成る焼結体であっても良いし、基体の表面に
セラミック超電導体か形成された複合体でも良い。特に
Ｂ１−３ｒ−Ｃａ−Ｃｕ−０系材料の場合には、溶融過
程を経て焼成されるために保持基体か必要となる。この
場合には主に金属基体を使うため、接合に当っては金属
同士の接合を行なった後セラミック接合層を形成するこ
とになる。The ceramic superconductor obtained by the present invention may be a sintered body having the same composition as a whole, or may be a composite body in which the ceramic superconductor is formed on the surface of a base. In particular, in the case of B1-3r-Ca-Cu-0 based materials, a holding base is required because they are fired through a melting process. In this case, since metal substrates are mainly used, a ceramic bonding layer is formed after the metals are bonded together.
本発明の接合は、例えばセラミック超電導体粉末を適当
な溶媒を用いてスラリー状にして、接合すべき仮焼成成
形体の各接合部に塗布し、該各接合部を合せた後最適な
焼成条件で接合部を加熱することにより、セラミック超
電導体を接合、製造することかできる。In the joining of the present invention, for example, ceramic superconductor powder is made into a slurry using an appropriate solvent, and the slurry is applied to each joining part of the pre-fired compacts to be joined, and after the joining parts are combined, the optimal firing conditions are set. Ceramic superconductors can be bonded and manufactured by heating the bonded portion.
また、セラミック超電導体からなる成形体を挟んて被接
合板焼成成形体を配置して、加熱処理して同時に接合し
てもよい。Alternatively, the fired molded bodies of the plates to be joined may be arranged with a molded body made of a ceramic superconductor sandwiched therebetween, and the molded bodies may be heat-treated and joined at the same time.
本発明における接合層の厚さは、接合物の使用目的に応
じ適宜選択すればよい。The thickness of the bonding layer in the present invention may be appropriately selected depending on the intended use of the bonded product.
なお、本発明て得られるセラミック超電導体の接合構造
か強度的に強く、しかも超電導特性か良好であるのは、
被接合体が仮焼成成形体であるため本焼成時に接合界面
てのセラミック粒子同士の焼結か進み、一体位成体と同
様の焼結状態になるためと思われる。Furthermore, the reason why the bonding structure of the ceramic superconductor obtained by the present invention is strong in strength and has good superconducting properties is as follows.
This seems to be because, since the objects to be joined are pre-fired compacts, sintering of the ceramic particles at the bonding interface progresses during the final firing, resulting in a sintered state similar to that of an integral body.
本発明に係るセラミック超電導体を磁気シールド材に適
用する場合であって、空洞を有し、その内部で磁気シー
ルドするような筒状構造物においては、両端からの磁束
侵入を防止するため接合層を軸に直角な方向に設けるよ
うに配置するのか好ましい。この場合、接合層の酸化物
超電導体の超電導特性が被接合体より低くても、シール
ドの効果か損われることがない。When the ceramic superconductor according to the present invention is applied to a magnetic shielding material, in a cylindrical structure that has a cavity and is magnetically shielded inside, a bonding layer is used to prevent magnetic flux from penetrating from both ends. It is preferable to arrange it so that it is provided in a direction perpendicular to the axis. In this case, even if the superconducting properties of the oxide superconductor in the bonding layer are lower than those of the objects to be bonded, the shielding effect is not impaired.
［実施例］
以下、本発明を実施例により更に詳しく説明する。但し
本発明は本実施例に限定されるものてはない。[Examples] Hereinafter, the present invention will be explained in more detail with reference to Examples. However, the present invention is not limited to this example.
（実施例１）
ＹＢａ２Ｃｕ：＋Ｏｙ原料粉末を金型ブレス法により、
φ３０ｍａ＋Ｘ ｌ Ｏｍｍ（厚さ）のベレット状に成
形した。この成形体２枚を酸素中８８０°Ｃて３時間焼
成し、仮焼体を得た。第１図に示すように、この２枚の
仮焼体２，３をＹＢａ２Ｃｕ３０．粉末ペースト４を介
して積層して積層成形体１を得た。ペーストは、原料粉
末にバインダーとしてポリビニルブチラール（ＰＶＢ）
を加え、溶媒としてテルピネオールを加え混練したもの
を用いた。(Example 1) YBa2Cu:+Oy raw material powder was molded using a mold press method.
It was molded into a pellet shape with a diameter of 30 ma+X l Omm (thickness). Two of these molded bodies were fired in oxygen at 880°C for 3 hours to obtain a calcined body. As shown in FIG. 1, these two calcined bodies 2 and 3 are made of YBa2Cu30. The laminated molded body 1 was obtained by laminating the powder paste 4 therebetween. The paste uses polyvinyl butyral (PVB) as a binder in raw material powder.
was added and kneaded with terpineol added as a solvent.
この積層体を酸素中９５０’Ｃで５ｈｒ焼成した。This laminate was fired in oxygen at 950'C for 5 hours.
焼結体の両端に金属治具を接着剤で取り付け、弓張り強
度試験機を用いて接合強度を測定した。接合強度は７０
ＭＰａてあり、Ｙ系焼結体単体ての引張り強度ＭＰａの
８割程度てあり、非常に高い接合強度を示した。Metal jigs were attached to both ends of the sintered body with adhesive, and the joint strength was measured using a bow tension tester. Joint strength is 70
MPa, which was approximately 80% of the tensile strength MPa of the Y-based sintered body alone, demonstrating extremely high bonding strength.
この焼結体を接合層か中心となるように２×２×２０■
に切断加工し、液体窒素温度７７にでの臨界電流密度（
Ｊｃ）を四端子法て測定した。接合体のＪｃは２６０
Ａ／ｃｍ”てＹ系焼結体単体てのＪｃ値とほぼ同じであ
った。Place this sintered body in a 2x2x20
The critical current density at liquid nitrogen temperature of 77
Jc) was measured using the four-terminal method. Jc of zygote is 260
A/cm'' was almost the same as the Jc value of the Y-based sintered body alone.
（実施例２）
厚さ１．５ｍｍて５０ｍｍＸ２０ｎ＋ａの５ＵＳ３０４
の板上に厚さ０．２ｍｍの２ｒＯ２溶射を施した基板と
、 Ｂｉ２５ｒ２（：ａｃｕ２０８粉末のスラリーを用
意した。なおスラリーはセラミック（Ｂｉ２５ｒｚＣａ
Ｃｕ２０８）粉末１００重量部に対して１重量部のＰＶ
Ｂと０．２重量部の分散剤を加え、エタノールを溶媒に
して調製した。スラリーの粘度は約２０００ＣＰＳてあ
った。(Example 2) 5US304 with thickness 1.5mm and 50mm x 20n+a
A substrate with 2rO2 thermal sprayed to a thickness of 0.2 mm and a slurry of Bi25r2(:acu208 powder) were prepared.
Cu208) 1 part by weight of PV per 100 parts by weight of powder
B and 0.2 parts by weight of a dispersant were added, and ethanol was used as a solvent. The viscosity of the slurry was about 2000 CPS.
基板を８０°Ｃに加熱し、この上にスラリーをスプレー
で塗布し乾燥しなからセラミック粉末を埋設させた。セ
ラミック層の厚さは約Ｉｎｎである。The substrate was heated to 80° C., a slurry was sprayed onto the substrate, and after drying, ceramic powder was embedded. The thickness of the ceramic layer is approximately Inn.
この基板を酸素雰囲気中８３０°Ｃで５ｈｒ焼成し、小
型の仮焼成複合体を得た。次に、第２図に示すように上
記小型板焼成複合体２０．３０を２枚結合させた。また
結合部４１は５ｔＪＳ：１０４基体の端部を数個所煮付
て溶接した。この仮焼成複合体１０の接合部４０に、上
記と同様にスプレーにより接合形成層５０を形成させた
。接合形成層５０は小型板焼成複合体２０及び３０の上
に形成されている仮焼成セラミック超電導体層２１．３
１とオーバーラツプするように形成させた。尚、接合形
成層５０の厚さは約１＋＋＋ｍである。This substrate was fired at 830°C for 5 hours in an oxygen atmosphere to obtain a small pre-fired composite. Next, as shown in FIG. 2, two of the above-mentioned small-sized fired composite plates 20 and 30 were joined together. The joint portion 41 was made by boiling and welding the ends of a 5tJS:104 substrate at several locations. A bond forming layer 50 was formed on the bonding portion 40 of this pre-fired composite 10 by spraying in the same manner as described above. The bond forming layer 50 is a pre-fired ceramic superconductor layer 21.3 formed on the small plate fired composites 20 and 30.
It was formed so as to overlap with 1. Note that the thickness of the bonding layer 50 is approximately 1+++ m.
次いて、この仮焼成複合体１０を、酸素雰囲気中９２０
℃で１０分保持した後８９０°Ｃて５ｈｒ焼成した。Next, this pre-fired composite 10 is heated in an oxygen atmosphere for 920 minutes.
After being held at 890°C for 10 minutes, it was fired for 5 hours.
得られた焼成体について、その接合層を中心にして端部
の臨界電流密度Ｊｃを液体窒素温度７７Ｋ（但し、磁場
強度Ｂ＝Ｏガウス）て測定したところ８５５ Ａ／ｃｍ
２であり、焼結体単体てのＪｃとほぼ同しであった。Regarding the obtained fired body, the critical current density Jc at the end around the bonding layer was measured at a liquid nitrogen temperature of 77 K (however, magnetic field strength B = O Gauss) and found to be 855 A/cm.
2, which was almost the same as the Jc of the sintered body alone.
（比較例）
実施例２と同し形状、同し工程で得た小型成形体２枚を
、酸素雰囲気中９２０°Ｃて１０分保持した後８９０°
Ｃて５ｈｒ焼成し、焼成体を得た。得られた焼成体のＪ
ｃは、実施例２と同条件で測定したところ、それぞれ８
２０．８７０Ａ／Ｃ［Ｉ＋２であった。(Comparative example) Two small molded bodies obtained in the same shape and in the same process as in Example 2 were held at 920°C for 10 minutes in an oxygen atmosphere and then heated to 890°C.
The product was fired for 5 hours at C to obtain a fired product. J of the obtained fired body
When measured under the same conditions as Example 2, c was 8.
20.870A/C [I+2.
この本焼成複合体を、実施例２と同様に金属同士を溶接
により接合し、接合層を形成して上記と回し条件で焼成
した。In this fired composite, the metals were joined together by welding in the same manner as in Example 2, a joining layer was formed, and the composite was fired under the same conditions as described above.
この焼成体のＪｃを接合層を中心に含む経路て測定した
結果、２５Ａ／ｃｌＩ＋２てあった。この原因は接金層
と本焼成セラミックスの界面で両者の良好な結合か生じ
ていないためと思われる。The Jc of this fired body was measured along a path including the bonding layer in the center, and was found to be 25 A/clI+2. The reason for this is thought to be that a good bond between the weld layer and the fired ceramic was not formed at the interface between the two.
（実施例３）
金型ブレスを用いてＹＢａ２Ｃｕ３０．原料粉末より円
筒及び円板を成形した。円筒の形状は、長さか５００ｍ
ｍで内径２００ｍｍ、外径２２０［１１１である。(Example 3) Using a mold press, YBa2Cu30. A cylinder and a disk were molded from the raw material powder. The shape of the cylinder is about 500m long.
m, the inner diameter is 200 mm, and the outer diameter is 220 [111 mm].
又、円板の形状は径が２２０ｍｍで厚さがＩＣ１＋ｍで
ある。Further, the shape of the disc has a diameter of 220 mm and a thickness of IC1+m.
この成形体を空気中９２０°Ｃて５ｈｒ焼成した。This molded body was fired in air at 920°C for 5 hours.
このとき、同時にＪＣＩＭ定用の５ｍｍＸ ５ｍｍＸ
３０ｍｍの成形棒も焼成した。この棒のＪｃを測定した
結果〜ＯＡ／ｃｍ２であった。従って同時に焼成した円
筒および円板も同程度のＪｃであると推定される。At this time, at the same time, 5mmX 5mmX for JCIM
A 30 mm shaped bar was also fired. The Jc of this rod was measured and found to be ~OA/cm2. Therefore, it is estimated that the cylinder and disk fired at the same time have the same Jc.
この円筒と円板を用いて、第３図に示すような有底円筒
成形体１００を作製した。なお、円筒１０１と円板１０
２の間には実施例１と同じペースト１０３か積層しであ
る。この成形体を酸素雰囲気中９５０°Ｃて５ｈｒ焼成
し、有底円筒を得た。Using this cylinder and disc, a bottomed cylindrical molded body 100 as shown in FIG. 3 was produced. In addition, the cylinder 101 and the disk 10
2, the same paste 103 as in Example 1 is laminated. This molded body was fired for 5 hours at 950°C in an oxygen atmosphere to obtain a cylinder with a bottom.
このとき同時に焼成したＪｃ測定サンプルのＪｃは２３
０ Ａ／ｃｍ２であった。従りて同時に焼成した有底円
筒も同等のＪｃを示すものと推定てきる。At this time, the Jc of the Jc measurement sample fired at the same time was 23
It was 0 A/cm2. Therefore, it can be assumed that the bottomed cylinders fired at the same time also exhibit the same Jc.
［発明の効果］
以上説明したように、本発明のセラミック超電導体の製
法によれば、仮焼成して得た仮焼成成形体を、これと同
一の成分を含む接合成形層て仮接合して一体の成形体を
得た後焼成しているので、接合部においてセラミック同
士が焼結し、一体焼成物と同等の強度や超電導特性を得
ることかできる。[Effects of the Invention] As explained above, according to the method for producing a ceramic superconductor of the present invention, a pre-fired compact obtained by pre-sintering is temporarily bonded with a bonding layer containing the same components. Since the integral molded body is fired after being obtained, the ceramics are sintered together at the joints, making it possible to obtain the same strength and superconducting properties as an integrally fired body.
また、本発明のセラミック超電導体の製法は。Furthermore, the method for manufacturing the ceramic superconductor of the present invention is as follows.
各種大型製品及び異形製品に適用でき、均一性能を有す
る大型セラミックの超電導体を容易且つ経済的に製造す
ることかできる。The present invention can be applied to various large products and irregularly shaped products, and large ceramic superconductors with uniform performance can be manufactured easily and economically.
第１図は本発明の製法に用いる複数の仮焼成体の接合状
態の一例を概略的に示す斜視図、第２図は本発明の製法
に用いる複数の仮焼成体の接合状態の他の例を示す断面
図、第３図は本発明の製法に用いて作製する有底円筒の
例を示す概略断面図である。
■・・・積層成形体、２，３・・・仮焼成体、４・・・
ペースト、１０・・・仮焼成複合体、２０．３０・・・
仮焼成複合体、２１．３１・・・仮焼成セラミック超電
導体層、４０・・・接合部、４１・・・結合部、５０・
・・接合形成層、１００・・・有底円筒成形体、１０１
・・・円筒、１０２・・・円板、１０３・・・ペースト
。
第２図FIG. 1 is a perspective view schematically showing an example of a joined state of a plurality of pre-fired bodies used in the manufacturing method of the present invention, and FIG. 2 is another example of a joined state of a plurality of pre-fired bodies used in the manufacturing method of the present invention. FIG. 3 is a schematic cross-sectional view showing an example of a bottomed cylinder manufactured using the manufacturing method of the present invention. ■...Laminated molded body, 2, 3... Temporarily fired body, 4...
Paste, 10... Temporarily fired composite, 20.30...
Calcined composite, 21.31 Calcined ceramic superconductor layer, 40 Joint part, 41 Joint part, 50.
... Bonding forming layer, 100 ... Bottomed cylindrical molded body, 101
...Cylinder, 102...Disc, 103...Paste. Figure 2
Claims (2)
様な特性のセラミック超電導体を製造する方法であって
、被接合セラミック超電導基材を仮焼成し、次いでこれ
らの仮焼成成形体を該成形体と同一の成分を含む接合成
形層で仮接合して一体の成形体を得た後、該成形体を焼
成することにより、超電導特性を有するセラミック超電
導体を得ることを特徴とするセラミック超電導体の製法
。(1) A method for manufacturing an integrated ceramic superconductor with uniform characteristics by bonding a plurality of ceramic superconducting substrates, in which the ceramic superconducting substrates to be bonded are pre-sintered, and then these pre-sintered molded bodies are A ceramic characterized in that a ceramic superconductor having superconducting properties is obtained by temporarily bonding with a bonding molding layer containing the same components as the molded body to obtain an integral molded body, and then firing the molded body. Superconductor manufacturing method.
電導特性を生じる条件から外れたものである請求項１記
載のセラミック超電導体の製法。(2) The method for producing a ceramic superconductor according to claim 1, wherein the pre-firing conditions deviate from conditions that produce superconducting properties of the ceramic superconducting substrate to be joined.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1119553A JPH02296778A (en) | 1989-05-12 | 1989-05-12 | Production of ceramic superconductor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1119553A JPH02296778A (en) | 1989-05-12 | 1989-05-12 | Production of ceramic superconductor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02296778A true JPH02296778A (en) | 1990-12-07 |
Family
ID=14764164
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1119553A Pending JPH02296778A (en) | 1989-05-12 | 1989-05-12 | Production of ceramic superconductor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02296778A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02302380A (en) * | 1989-05-17 | 1990-12-14 | Dowa Mining Co Ltd | Joining of superconductor |
| JPH035381A (en) * | 1989-05-31 | 1991-01-11 | Ibiden Co Ltd | Adhesive for ceramic blank |
| WO2017135387A1 (en) * | 2016-02-05 | 2017-08-10 | 一般財団法人ファインセラミックスセンター | Method for producing ceramic sintered body, and method and device for producing ceramic molded body |
| JP2017141152A (en) * | 2016-02-05 | 2017-08-17 | 一般財団法人ファインセラミックスセンター | Method for producing ceramic molded body and apparatus for producing the same used therefor |
| JP2018108666A (en) * | 2016-12-28 | 2018-07-12 | 一般財団法人ファインセラミックスセンター | Method of manufacturing ceramic molded body and manufacturing apparatus used therefor |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5918176A (en) * | 1982-07-23 | 1984-01-30 | 株式会社東芝 | Manufacture of ceramic structure |
| JPS60171274A (en) * | 1984-02-16 | 1985-09-04 | 黒崎窯業株式会社 | Ceramic bonding method |
| JPS63256574A (en) * | 1987-04-10 | 1988-10-24 | Sumitomo Electric Ind Ltd | Process for bonding ceramic superconductive material |
| JPH01160877A (en) * | 1987-12-17 | 1989-06-23 | Toshiba Corp | Method for bonding oxide superconductor material |
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1989
- 1989-05-12 JP JP1119553A patent/JPH02296778A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5918176A (en) * | 1982-07-23 | 1984-01-30 | 株式会社東芝 | Manufacture of ceramic structure |
| JPS60171274A (en) * | 1984-02-16 | 1985-09-04 | 黒崎窯業株式会社 | Ceramic bonding method |
| JPS63256574A (en) * | 1987-04-10 | 1988-10-24 | Sumitomo Electric Ind Ltd | Process for bonding ceramic superconductive material |
| JPH01160877A (en) * | 1987-12-17 | 1989-06-23 | Toshiba Corp | Method for bonding oxide superconductor material |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02302380A (en) * | 1989-05-17 | 1990-12-14 | Dowa Mining Co Ltd | Joining of superconductor |
| JPH035381A (en) * | 1989-05-31 | 1991-01-11 | Ibiden Co Ltd | Adhesive for ceramic blank |
| WO2017135387A1 (en) * | 2016-02-05 | 2017-08-10 | 一般財団法人ファインセラミックスセンター | Method for producing ceramic sintered body, and method and device for producing ceramic molded body |
| JP2017141152A (en) * | 2016-02-05 | 2017-08-17 | 一般財団法人ファインセラミックスセンター | Method for producing ceramic molded body and apparatus for producing the same used therefor |
| EP3412642A4 (en) * | 2016-02-05 | 2019-12-11 | Japan Fine Ceramics Center | Method for producing ceramic sintered body, and method and device for producing ceramic molded body |
| US11027454B2 (en) | 2016-02-05 | 2021-06-08 | Japan Fine Ceramics Center | Method for producing ceramic sintered body, and method and device for producing ceramic molded body |
| US11724415B2 (en) | 2016-02-05 | 2023-08-15 | Japan Fine Ceramics Center | Method for producing ceramic sintered body, and method and device for producing ceramic molded body |
| JP2018108666A (en) * | 2016-12-28 | 2018-07-12 | 一般財団法人ファインセラミックスセンター | Method of manufacturing ceramic molded body and manufacturing apparatus used therefor |
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