JPH01220307A - High strength superconductive wire having high critical current density and its manufacture - Google Patents
High strength superconductive wire having high critical current density and its manufactureInfo
- Publication number
- JPH01220307A JPH01220307A JP63043530A JP4353088A JPH01220307A JP H01220307 A JPH01220307 A JP H01220307A JP 63043530 A JP63043530 A JP 63043530A JP 4353088 A JP4353088 A JP 4353088A JP H01220307 A JPH01220307 A JP H01220307A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- superconducting
- filled
- ceramic powder
- silver
- 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
- 238000004519 manufacturing process Methods 0.000 title claims description 3
- 239000000843 powder Substances 0.000 claims abstract description 58
- 239000000919 ceramic Substances 0.000 claims abstract description 55
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 14
- 239000001301 oxygen Substances 0.000 claims abstract description 14
- 150000001875 compounds Chemical class 0.000 claims abstract description 4
- 239000010949 copper Substances 0.000 claims abstract description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052784 alkaline earth metal Inorganic materials 0.000 claims abstract description 3
- 150000001342 alkaline earth metals Chemical class 0.000 claims abstract description 3
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 3
- 239000002131 composite material Substances 0.000 claims description 18
- 238000005096 rolling process Methods 0.000 claims description 16
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 claims description 11
- 229910052751 metal Inorganic materials 0.000 claims description 11
- 239000002184 metal Substances 0.000 claims description 11
- 229910052709 silver Inorganic materials 0.000 claims description 9
- 239000004332 silver Substances 0.000 claims description 9
- 238000000034 method Methods 0.000 claims description 8
- 238000010438 heat treatment Methods 0.000 abstract description 8
- 239000000203 mixture Substances 0.000 abstract description 6
- 239000002245 particle Substances 0.000 abstract description 6
- 239000011812 mixed powder Substances 0.000 abstract description 2
- AYJRCSIUFZENHW-UHFFFAOYSA-L barium carbonate Chemical compound [Ba+2].[O-]C([O-])=O AYJRCSIUFZENHW-UHFFFAOYSA-L 0.000 abstract 2
- 229910000589 SAE 304 stainless steel Inorganic materials 0.000 abstract 1
- 238000010586 diagram Methods 0.000 description 8
- 239000013078 crystal Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 150000002739 metals Chemical class 0.000 description 4
- 239000000956 alloy Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910000856 hastalloy Inorganic materials 0.000 description 1
- 229910001026 inconel Inorganic materials 0.000 description 1
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000002887 superconductor Substances 0.000 description 1
- 230000002087 whitening effect Effects 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E40/00—Technologies for an efficient electrical power generation, transmission or distribution
- Y02E40/60—Superconducting electric elements or equipment; Power systems integrating superconducting elements or equipment
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、Ｙを含む希土類元素（以下、これらの元素
をＲで示す）、アルカリ土類金属（以下Ａで示す）、鋼
（Ｃｕ ）および酸素（０）からなるイロブスカイト構
造を有する化合物（以下、この化合物なＭｉ電導セラミ
ックスという）を、複合管に充填してなる高強度と高臨
界電流密度を有する超電導ワイヤおよびその製造法に関
するものである。[Detailed Description of the Invention] [Industrial Application Field] This invention is applicable to rare earth elements including Y (hereinafter these elements will be referred to as R), alkaline earth metals (hereinafter referred to as A), and steel (Cu). and a superconducting wire having high strength and high critical current density obtained by filling a composite tube with a compound having an ilovskite structure consisting of oxygen (0) (hereinafter referred to as the compound Mi conductive ceramic), and a method for manufacturing the same. It is.
一般に、超電導セラミックスを用いたワイヤの加工方法
としては。Generally, as a method for processing wire using superconducting ceramics.
（ａ） 原料粉末として、いずれも平均粒径：ｌＯμ
寓以下のＲ２Ｏ３粉末、Ａの炭酸塩粉末、ＣｕＯ粉末を
用意し、これら原料粉末を所定の配合組成に配合し、混
合して大気中または酸素雰囲気中で温度＝８５０〜９５
０℃にて焼成し、イロブスカイト構造を有する超電導セ
ラミックスを作製し、これを平均粒径：ｌＯμ冨以下に
粉砕する。(a) As raw material powder, average particle size: lOμ
Prepare the following R2O3 powder, A carbonate powder, and CuO powder, blend these raw material powders to a predetermined composition, mix and heat in air or oxygen atmosphere at a temperature of 850 to 95.
A superconducting ceramic having an ilovskite structure is produced by firing at 0° C., and this is pulverized to an average particle size of 10 μm or less.
（ｂ） 上記粉砕した粉末を銀（Ａｇ）Ｗ管内に充填
し１両端を真空密封し、この充填Ａｇ管材にスェージラ
ダ加工や溝ロール加工まなはダイス加工等の伸線加工を
施し、直径２５Ｍ以下の充填ワイヤとし。(b) The above-mentioned pulverized powder is filled into a silver (Ag) W tube, both ends are vacuum-sealed, and this filled Ag tube material is subjected to wire drawing processing such as swage ladder processing, groove roll processing, or die processing, and has a diameter of 25M or less. Filled with wire.
（Ｃ） 最終的に、充填線材に充填されている超電導
セラミックスを焼結し、その後、酸素吸収のために、上
記伸線加工された充填Ａｇワイヤを、大気中または酸素
雰囲気中で、温度＝９００〜９５０℃にて熱処理し、製
品としている。(C) Finally, the superconducting ceramics filled in the filled wire is sintered, and then, in order to absorb oxygen, the drawn filled Ag wire is placed in the air or in an oxygen atmosphere at a temperature of The product is heat-treated at 900-950°C.
上記従来の技術１ｃ）の工程において、超電導セラミッ
クスワイヤを熱処理することＫよシ超［４セラミツクス
粉末の焼結とその後の酸素吸収を行なうのであるが、上
記伸線加工した直径：５鵡以下の充填Ａｇワイヤの熱処
理温度は９００〜９５０℃であり、この熱処理温度はＡ
ｇの融点（９６０，８℃）ｋ近いために、超電導セラミ
ックスを被覆しているＡｇワイヤは軟化し１曲が）やす
くなシ、不注意な白けは、充填されている超電導セラミ
ックスに不連続または切断を生じせしめ、＾温熱処理の
ためＫＡｇワイヤ自身の強度も極めて低下しているので
断線することもあつな。In the process of conventional technology 1c), the superconducting ceramic wire is heat-treated to sinter the superconducting ceramic powder and then absorb oxygen. The heat treatment temperature of the filled Ag wire is 900-950℃, and this heat treatment temperature is A
Since the melting point of g (960.8°C) is close to k, the Ag wire covering the superconducting ceramics is easily softened (1 bend), and inadvertent whitening may cause discontinuities or Since the strength of the KAg wire itself is extremely reduced due to the high temperature treatment, it is likely that the wire will break.
上記超電導セラミックスを被覆する材料としてＡｇ以外
の金属５例えばＮ１合金、ステンレス鍋などの高温強度
がすぐれた材料が考えられるが、上記Ａｇ以外の金属は
、酸素の拡散浸透および排出を行うことができないため
、上記Ａｇ以外の金属によシ超電導ワイヤを作製すると
、加工中または加工後に超電導セラミックスより放出さ
れた酸素によりワイヤに膨らみが生じ、また上記大気中
または酸素雰囲気中にて行なわれる最終熱処理により、
充填されている超電導セラミックスに酸素を吸収させる
仁とができない。As a material for coating the above-mentioned superconducting ceramics, metals other than Ag5 such as materials with excellent high-temperature strength such as N1 alloy and stainless steel pots can be considered, but metals other than the above-mentioned Ag are incapable of diffusing and permeating oxygen and discharging it. Therefore, if a superconducting wire is made from a metal other than the above-mentioned Ag, the wire will bulge due to oxygen released from the superconducting ceramic during or after processing, and the final heat treatment performed in the air or oxygen atmosphere will cause bulges in the wire. ,
The superconducting ceramics filled with oxygen cannot be absorbed.
したがって、現在のところ、超電導セラミックス粉末の
被覆材としてＡｇ以外の金属は考えられない。ところが
、上記Ａｇは高価であるとともに、高温熱処理中での扱
いが難しく、高温および常温における強度も弱いために
上述の如きトラブルを生じることが毎々あった。Therefore, at present, metals other than Ag cannot be considered as coating materials for superconducting ceramic powder. However, the above-mentioned Ag is expensive, difficult to handle during high-temperature heat treatment, and has low strength at both high and normal temperatures, which often causes the above-mentioned troubles.
さらに、上記従来の技術で述べた方法によｔ）Ｈ造した
超電導ワイヤの臨界電流密度Ｊｃは、１０ｓＡ／ｃＩＩ
Ｌ２のオーダーであシ、実用に供する超電導ワイヤの臨
界電流密度は、少くともｌＯＡ／ｃＩＬ２を必要として
いる。上記４ｏプスカイト構造を有する超電導セラミッ
クスの結晶は、結晶異方性が大きく、結晶のＣ軸方向に
は電流が流れにくく、Ｃ軸方向に垂直な方向には電流が
流れやすいため、上記超電導ワイヤに充填されている超
電導セラミックス粉末の結晶のＣ軸方向がワイヤの長手
方向に対して垂直に配向するように充填し、その配向層
が十分な厚さを有すると、 １０ Ａ／ｃａ２以上
の高臨界電流密度を有する超電導ワイヤが得られるはず
であるけれども、上記超電導ワイヤ中の超電導セラミッ
クス粉末のＣ軸方向がワイヤの長手方向に対して垂直に
配向している十分な厚さの配向層を得るための手段につ
いても知られてはいなかった。Furthermore, the critical current density Jc of the superconducting wire produced by the method described in the prior art section is 10 sA/cII.
On the order of L2, the critical current density of a superconducting wire for practical use requires at least lOA/cIL2. The superconducting ceramic crystal having the above-mentioned 4o-skite structure has a large crystal anisotropy, and it is difficult for current to flow in the direction of the C-axis of the crystal, but it is easy to flow in the direction perpendicular to the C-axis direction. If the packed superconducting ceramic powder is filled so that the C-axis direction of the crystals is oriented perpendicular to the longitudinal direction of the wire, and the oriented layer has a sufficient thickness, a high criticality of 10 A/ca2 or more can be achieved. Although a superconducting wire with a current density should be obtained, in order to obtain a sufficiently thick oriented layer in which the C-axis direction of the superconducting ceramic powder in the superconducting wire is oriented perpendicular to the longitudinal direction of the wire. The means of doing so were not known.
そこで１本発明者等は、高価なＡｇの使用を減らし、さ
らに高温および室温強直がすぐれるとともに少なくとも
１０ Ａ／Ｃｌ１２のオーダーの鍋臨界−流密度の電流
を流すことのできる超電導ワイヤを開発すべく研究を行
なったところ。Therefore, the present inventors have developed a superconducting wire that reduces the use of expensive Ag, has excellent high-temperature and room-temperature stiffness, and is capable of passing a current with a pot critical current density of the order of at least 10 A/Cl12. I did a lot of research.
超′Ｒｔ導セラミックス粉末を、内層がＡｇで外層がＡ
ｇ部分とＡｇ以外の金属部分からなり、上記外層のＡｇ
部分は上記内層のＡｇと一体であり、外面に露出してい
る複合管に充填し。The ultra'Rt conductive ceramic powder has an inner layer of Ag and an outer layer of A.
It consists of a g part and a metal part other than Ag, and the Ag of the above outer layer
The part is integral with the inner layer of Ag and is filled into the composite tube exposed to the outside.
上記超電導セラミックス粉末を充填した複合管を伸線加
工して超１４を導セラミックス粉末充填ワイヤとし。The composite tube filled with the above-mentioned superconducting ceramic powder was wire-drawn to make Super 14 a conductive ceramic powder-filled wire.
上記伸線加工した超電導セラミックス粉末充填ワイヤを
、１パスの圧下率が５０％以上の平ロール圧延を行ない
。The drawn superconducting ceramic powder-filled wire is subjected to flat roll rolling with a rolling reduction of 50% or more in one pass.
ついで、上記平ロール圧延した超を専セラミックス粉末
充填ワイヤを、温度：９００〜９５０℃にて熱処理する
と。Then, the flat-rolled ultrasonic ceramic powder-filled wire is heat-treated at a temperature of 900 to 950°C.
上記高温および常温強度にすぐれるとともに高臨界電流
密度を有する超電導ワイヤが得られるという知見を得た
のである。It was discovered that a superconducting wire having excellent high-temperature and room-temperature strength as well as a high critical current density can be obtained.
この発明は、かかる知見にもとづいてなされたものであ
って１次のような作用がある。This invention was made based on this knowledge and has the following effects.
（１）上記複合管の外層のｒＡｇ以外の金属部分」Ｋ高
温および常温強度のすぐれた金属１例えばインコネル、
ハステロイ等のＮｉ基合金、８ＵＳ３０４等のオーステ
ナイトステンレス鋼などを用いると。(1) Metal parts other than rAg in the outer layer of the composite pipe 1 Metals with excellent high-temperature and room-temperature strength 1 For example, Inconel,
When using Ni-based alloys such as Hastelloy, austenitic stainless steels such as 8US304, etc.
熱処理中の強度不足によるトラブルは解消され。Problems caused by insufficient strength during heat treatment have been resolved.
高温および常温強度のすぐれた超電導ワイヤを得ること
ができ、上記複合管の外層にｒＡｇ部分」を設けること
Ｋより、加工中または加工後に超電導セラミックス粉末
から放出された酸素によるワイヤの膨らみの発生が防止
され、大気または酸素雰囲気熱処理中の酸素の吸収も行
なわれる。A superconducting wire with excellent high-temperature and room-temperature strength can be obtained, and by providing the "rAg part" on the outer layer of the composite tube, bulging of the wire due to oxygen released from the superconducting ceramic powder during or after processing can be prevented. Oxygen absorption during air or oxygen atmosphere heat treatment is also prevented.
（２） 上記伸線加工した超電導セラミックス粉末充
填ワイヤを１パスの圧下率が５０チ以上の平ロール圧延
を行なうと、ワイヤに充填されている超電導セラミック
ス粉末の結晶のＣ軸方向がワイヤの長手方向に対して垂
直に揃った配向層（以下。(2) When the drawn wire filled with superconducting ceramic powder is flat-rolled with a rolling reduction of 50 inches or more in one pass, the C-axis direction of the crystals of the superconducting ceramic powder filled in the wire is aligned with the longitudinal direction of the wire. Orientation layer aligned perpendicular to the direction (hereinafter referred to as
圧縮配向ｌ−という）が形成され、しかも上記圧縮配向
層の厚さは５μ冨以上となシ、臨界電流密反を１０
Ａ／ｃＸ２以上にすることができる。A compression-oriented layer (referred to as 1-) is formed, and the thickness of the compression-oriented layer is 5 μm or more, and the critical current density is 10
A/cX2 or more can be achieved.
ここで圧下率とは、伸線加工した平ロール圧延前の超を
導セラミックス粉末充填ワイヤの外径なｈｏ、平ロール
圧延後の断面偏平な超電導セラミックス粉末充填ワイヤ
の厚さをｈとすると。Here, the rolling reduction is defined as ho, the outer diameter of the superconducting ceramic powder-filled wire before flat roll rolling, and h the thickness of the superconducting ceramic powder-filled wire with a flat cross section after flat roll rolling.
ｈｏ−ｈ 圧下率−−Ｘ Ｉ ＯＯ（＠ Ｏ で表わすことができる。ho-h Rolling reduction rate--X I OO (@ O It can be expressed as
この圧下率：５０−以上の平ロールによる圧延はｌバス
で行ない、しかも縁材の塑性加工工程の最終段階で行な
う必要がある。かかるｌ／々ス圧延は可及的に急激に行
なうことが望ましい。This rolling with flat rolls having a rolling reduction ratio of 50 or more is carried out in an 1-bath and must be carried out at the final stage of the plastic working process of the edge material. It is desirable that such l/mth rolling be performed as rapidly as possible.
上記圧縮配向層の層厚を５〜１５０μ諷に定めた理由＃
ｉ、５μｍ未満では、従来の超電導ワイヤのように臨界
ｔａ密＆ＪＣは１０Ａ／ｃＷＬ２のオーダーにしかなら
ないために実用にならず、上記圧縮配向層の層厚は大き
いほど＾臨界寛流密反が得られるが、普通の圧延または
プレスによシ得られる圧動配向層の層厚は１５０μ票が
限界でるる。したがって、上記圧縮配向層の層厚は５〜
１５０μ風に定めた。Reason for setting the layer thickness of the compression alignment layer to 5 to 150 μm #
i, less than 5 μm, the critical ta density & JC is only on the order of 10 A/cWL2 like in conventional superconducting wires, so it is not practical, and the larger the layer thickness of the compressive alignment layer, the more the critical relaxation density becomes. However, the thickness of the pressure-aligned layer obtained by ordinary rolling or pressing is limited to 150 μm. Therefore, the layer thickness of the compressed alignment layer is 5~
The wind was set at 150μ.
（３）上記方法によシ形成された圧縮配向層を有する超
電導セラミックス粉末充填ワイヤを、最後に大気中また
は酸素雰囲気中で熱処理しても圧縮配向層のＣ軸方向お
よび厚さに何ら変化は認められない。(3) Even when the superconducting ceramic powder-filled wire having the compressed oriented layer formed by the above method is finally heat-treated in air or oxygen atmosphere, there is no change in the C-axis direction and thickness of the compressed oriented layer. unacceptable.
（４） 複合管の内層をＡｇ層とした理由はｓ Ａｇ
以外の例えばＮ１基合金ま九はオーステナイト系ステン
レス鋼と超電導セラきツクス粉末が接触した状態で処理
されると、化学反応を起し、 ＮｉＯ、ＦｅＯ。(4) The reason why the inner layer of the composite pipe is made of Ag is sAg
For example, when other N1-based alloys are treated with austenitic stainless steel and superconducting ceramic powder in contact with each other, a chemical reaction occurs, forming NiO and FeO.
Ｆｅ２Ｏ３、Ｃｒ２Ｏ５等の酸化物が生成し、超電導特
性が大幅に劣化することによるものである。This is due to the formation of oxides such as Fe2O3 and Cr2O5, which significantly deteriorates superconducting properties.
つぎに、この発明を実施例にもとづいて具体的に説明す
る。Next, the present invention will be specifically explained based on examples.
原料粉末として、いずれも平均粒径：６μ重のＹ２Ｏ３
粉末、 ！３ａｃＯ３粉末、およびＣｕＯ粉末を用意し
。As raw material powder, average particle size: 6 μ weight Y2O3
Powder,! Prepare 3acO3 powder and CuO powder.
これら粉末をＹ２Ｏ３： ｌ ５． ｌ ３ 転ＢａＣ
０，： ５２．８９％ 、 ＣｕＯ： ３１．９８
’ｌｋ （以上重量ｓ）の割合で配合し、混合し、この
混合粉末を、大気中、温度＝９１０℃、ｌＯ時間保持の
条件で焼成し、平均粒径：２，５／ＪＩＩＫ粉砕して５
ＹＢａ２Ｃｕ３０７の組成を有しはロブスカイト構造を
有する超電廊セラミツクス粉末を作製した。
′
第１図は、この実施例で用いる複合管の概略図である。These powders are Y2O3: l5. l 3 BaC
0,: 52.89%, CuO: 31.98
'lk (or more weight s) and mix, and this mixed powder is fired in the air at a temperature of 910°C and held for 10 hours, and the average particle size is 2,5/JIIK pulverized. 5
A superconductor ceramic powder having a composition of YBa2Cu307 and a lobskite structure was prepared.
' Figure 1 is a schematic diagram of the composite tube used in this example.
上記複合管は、内層４がＡｇからなり、外層はＡｇ部分
２とＳＵＳ ３０４のオーステナイトステンレス銅から
なるＡｇ以外の金属部分ｌから構成されており、上記内
層４は肉厚：０．５ｍＸ内径：５、 ’Ｏｔｘを有し、
上記外層は肉厚＝０．５朋×外径ニア、０躊を有し、上
記外層のＡｇ部分２は直径：１．８騙の円形で構成され
ている。The above composite tube has an inner layer 4 made of Ag, an outer layer made of an Ag part 2 and a non-Ag metal part 1 made of SUS 304 austenitic stainless copper, and the inner layer 4 has a wall thickness of 0.5 m and an inner diameter: 5, has 'Otx;
The outer layer has a wall thickness of 0.5 mm×outer diameter near and 0 hardness, and the Ag portion 2 of the outer layer has a circular shape with a diameter of 1.8 mm.
かかる複合管に上記超１！感セラミックス粉末３を充填
し１両端部を真空密封した後、ロータリースェージング
加工にて直径：３．Ｏｍとし、引き続いて溝ロール加工
により直径：２．０驕超電尋セラミツクス粉末充填ワイ
ヤとした。The above-mentioned super 1 for such a composite pipe! After filling with sensitive ceramic powder 3 and vacuum-sealing both ends of 1, a rotary swaging process was performed to reduce the diameter to 3. 0m, and then grooved roll processing was performed to obtain a 2.0 diameter superelectroceramic powder-filled wire.
第２図は、上記超電導セラミックス粉末充填ワイヤの概
略図である。上記超電導セラミックス充填ワイヤの外層
５のＡｇ部分２は長円形になっていた。FIG. 2 is a schematic diagram of the superconducting ceramic powder-filled wire. The Ag portion 2 of the outer layer 5 of the superconducting ceramic filled wire had an oval shape.
上記第２図に示される超１！導セラミックス粉末充填ワ
イヤを２個の平ロールにより圧下率＝８０％ ０） ｌ
パス圧延し、厚さ：０．４１ｃｍの断面偏平な帯状超電
導セラミックス粉末充填ワイヤを作製した。Super 1 shown in Figure 2 above! Rolling down of conductive ceramic powder-filled wire with two flat rolls = 80% 0) l
Pass rolling was performed to produce a strip-shaped superconducting ceramic powder-filled wire with a flat cross section and a thickness of 0.41 cm.
第３図には、上記帯状超電導セラミックス粉末充填ワイ
ヤの概略図を示し、第４図（ａ）および（１））には、
上記帯状超電導セラミックス粉末充填ワイヤの断面拡大
概略図を示す。FIG. 3 shows a schematic diagram of the band-shaped superconducting ceramic powder-filled wire, and FIG. 4 (a) and (1)) show the following:
An enlarged cross-sectional schematic diagram of the above-mentioned strip-shaped superconducting ceramic powder-filled wire is shown.
上記乎ロール圧延後の帯状超電導セラミックス粉末充填
ワイヤの充填粉末３には第４図（ａ）およびｌｂ）に示
されるように圧縮配向層５が形成されており、第４図（
ａ）に示されるように、Ａｇ内層番に沿って厚さ：５μ
寓以上の圧扁配向層５が形成されていることもあり、第
４図（ｂ） Ｋ示されるように、コア全体が厚さ：５μ
観以上の圧動配向層５となっている場ｐもある。As shown in FIGS. 4(a) and lb), a compressed orientation layer 5 is formed on the filling powder 3 of the strip-shaped superconducting ceramic powder-filled wire after rolling.
Thickness: 5μ along the Ag inner layer number as shown in a)
Because the compressed orientation layer 5 is formed in a thickness larger than 100 mm, the entire core has a thickness of 5 μm, as shown in FIG. 4(b).
There is also a case where the pressure-dynamic alignment layer 5 is larger than that of the image.
上記帯状超電導セラミックス粉末充填ワイヤを。Above is the strip-shaped superconducting ceramic powder-filled wire.
大気中、温度＝９２０℃、１５時間保持の条件にて熱処
理を行ない、帯状超電導ワイヤを作製し。Heat treatment was performed in the atmosphere at a temperature of 920° C. for 15 hours to produce a strip-shaped superconducting wire.
この帯状超電導ワイヤの臨界電流密度を測定したところ
、 Ｊｃ ： １．６Ｘｌｏ Ａ／ｃ！Ｉｔ２であった
。When the critical current density of this strip-shaped superconducting wire was measured, it was found that Jc: 1.6Xlo A/c! It was It2.
上記帯状超電導ワイヤを切断し、超電導セラミックス粉
末充填層をＸ＠回折により配向テストを行なったところ
、超電導セラミックス粉末の結晶のＣ軸方向が帯状超電
導ワイヤの長手方向に対して垂直に配向している圧縮配
向層が存在しておシ上記圧縮配向層の層厚は８０μ諺で
あった。When the above band-shaped superconducting wire was cut and the superconducting ceramic powder filled layer was subjected to an orientation test using X@ diffraction, it was found that the C-axis direction of the crystals of the superconducting ceramic powder was oriented perpendicular to the longitudinal direction of the band-shaped superconducting wire. A compressed orientation layer was present, and the layer thickness of the compressed orientation layer was approximately 80 μm.
なお、この実施例では、複合管として断面円形の複合円
筒管を用いたが、断面形状は円形に限定されることなく
長円またはその他の多角形であってもよく、さらに、伸
線力り工された超電導セラミックス粉末充填ワイヤの断
面は円形に限定されるものではない。In this example, a composite cylindrical pipe with a circular cross section was used as the composite pipe, but the cross-sectional shape is not limited to a circular shape, but may be an ellipse or other polygon. The cross section of the fabricated superconducting ceramic powder-filled wire is not limited to a circular shape.
この発明によると、従来のＡｇ被覆超ｍｓワイヤよ）も
Ａｇの使用量が少なく、Ａ温および常温における強度が
優れるとともに高臨界電流密度を有する超ｖＬ導ワイヤ
を簡単に製造することができるというすぐれた効果があ
る。According to this invention, it is possible to easily produce an ultra-vL conductive wire that uses less Ag than the conventional Ag-coated ultra-ms wire, has excellent strength at A temperature and room temperature, and has a high critical current density. It has excellent effects.
第１図は、超を導セラミックス粉末を充填するための複
合管の概略図。
第２図は、超電導セラミックス粉末を充填した複合管を
伸縮加工した超電導セラミックス粉末充填複合ワイヤの
概略図。
第３図は、平ロール圧延後の断面偏平な帯状超電導セラ
ミックス粉末充填ワイヤの概略図。
第４図（ａ）および（ｂ）は、？！Ｆ状超電導セラミッ
クス粉末充填ワイヤの断面拡大概略図を示す。
１・・・外層のＡｇ以外の金属部分。
２・・・外層のＡｇ部分。
３・・・超電導セラミックス粉末。
４・・・内層。
５・・・圧縮配向Ｊ餉。FIG. 1 is a schematic diagram of a composite tube for filling superconducting ceramic powder. FIG. 2 is a schematic diagram of a superconducting ceramic powder-filled composite wire obtained by expanding and contracting a composite tube filled with superconducting ceramic powder. FIG. 3 is a schematic diagram of a strip-shaped superconducting ceramic powder-filled wire with a flat cross section after flat roll rolling. FIGS. 4(a) and (b) are? ! An enlarged cross-sectional schematic diagram of an F-shaped superconducting ceramic powder-filled wire is shown. 1...Metal part other than Ag in the outer layer. 2...Ag part of the outer layer. 3...Superconducting ceramic powder. 4...Inner layer. 5... Compression orientation J-kei.
Claims (2)
らなり、上記外層の銀部分は、上記内層の銀と一体であ
りかつ外面に露出している断面偏平な複合管と、 上記断面偏平な複合管に充填されているＹを含む希土類
元素、アルカリ土類金属、銅および酸素からなるペロブ
スカイト構造を有する化合物（以下、超電導セラミック
スという）粉末とからなる超電導ワイヤであつて、 上記超電導セラミックス粉末は、上記ペロブスカイト構
造のＣ軸方向が上記超電導ワイヤの長手方向に対して垂
直に配向している配向層を有するように充填されており
、上記配向層の厚さは、５〜１５０μｍであることを特
徴とする高臨界電流密度を有する高強度超電導ワイヤ。(1) A composite tube with a flat cross-section, the inner layer of which is silver, the outer layer of which is composed of a silver portion and a metal portion other than silver, the silver portion of the outer layer being integral with the silver of the inner layer and exposed to the outside; A superconducting wire made of powder of a compound having a perovskite structure (hereinafter referred to as superconducting ceramics) made of rare earth elements including Y, alkaline earth metals, copper and oxygen (hereinafter referred to as superconducting ceramics), which is filled in the composite tube with a flat cross section, The superconducting ceramic powder is filled so as to have an orientation layer in which the C-axis direction of the perovskite structure is oriented perpendicularly to the longitudinal direction of the superconducting wire, and the thickness of the orientation layer is 5 to 150 μm. A high-strength superconducting wire having a high critical current density.
が銀部分と銀以外の金属部分からなり上記外層の銀部分
は上記内層の銀と一体でありかつ外面に露出している複
合管に充填し、 上記超電導セラミックス粉末を充填した複合管を伸線加
工して超電導セラミックス粉末充填ワイヤとし、 上記伸線加工した超電導セラミックス粉末充填ワイヤを
、１パスの圧下率が５０％以上の平ロール圧延を行なつ
て、断面偏平な超電導セラミックス粉末充填ワイヤとし
、 ついで、上記断面偏平な超電導セラミックス粉末充填ワ
イヤを、温度：９００〜９５０℃にて熱処理することを
特徴とする高臨界電流密度を有する高強度超電導ワイヤ
の製造方法。(2) The above superconducting ceramic powder is packed into a composite tube in which the inner layer is silver, the outer layer is composed of a silver part and a metal part other than silver, and the silver part of the outer layer is integrated with the silver of the inner layer and is exposed on the outside. The composite tube filled with the superconducting ceramic powder is wire-drawn to obtain a superconducting ceramic powder-filled wire, and the wire-drawn superconducting ceramic powder-filled wire is flat-rolled with a rolling reduction of 50% or more in one pass. to obtain a wire filled with superconducting ceramic powder having a flat cross section, and then heat-treating the wire filled with superconducting ceramic powder having a flat cross section at a temperature of 900 to 950°C. Method for manufacturing superconducting wire.
Priority Applications (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63043530A JPH01220307A (en) | 1988-02-26 | 1988-02-26 | High strength superconductive wire having high critical current density and its manufacture |
| EP89902962A EP0358779B1 (en) | 1988-02-26 | 1989-02-27 | High-strength superconductive wire and cable having high current density, and method of producing them |
| DE89902962T DE68905980T2 (en) | 1988-02-26 | 1989-02-27 | HIGH-STRENGTH SUPER-CONDUCTIVE WIRES AND CABLES WITH HIGH CURRENT DENSITY AND METHOD FOR THE PRODUCTION THEREOF. |
| US07/445,639 US5068219A (en) | 1988-02-26 | 1989-02-27 | High strength superconducting wires and cables each having high current density, and a process for fabricating them |
| KR1019890701967A KR900701019A (en) | 1988-02-26 | 1989-02-27 | High strength superconducting wires and cables with high current density and manufacturing method |
| PCT/JP1989/000198 WO1989008317A1 (en) | 1988-02-26 | 1989-02-27 | High-strength superconductive wire and cable having high current density, and method of producing them |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63043530A JPH01220307A (en) | 1988-02-26 | 1988-02-26 | High strength superconductive wire having high critical current density and its manufacture |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01220307A true JPH01220307A (en) | 1989-09-04 |
Family
ID=12666300
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63043530A Pending JPH01220307A (en) | 1988-02-26 | 1988-02-26 | High strength superconductive wire having high critical current density and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01220307A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009539208A (en) * | 2006-06-02 | 2009-11-12 | デンマークス テクニスケ ウニヴェルシテト | High critical temperature superconducting article with improved mechanical strength |
| US10844479B2 (en) | 2014-02-21 | 2020-11-24 | Ut-Battelle, Llc | Transparent omniphobic thin film articles |
-
1988
- 1988-02-26 JP JP63043530A patent/JPH01220307A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009539208A (en) * | 2006-06-02 | 2009-11-12 | デンマークス テクニスケ ウニヴェルシテト | High critical temperature superconducting article with improved mechanical strength |
| US10844479B2 (en) | 2014-02-21 | 2020-11-24 | Ut-Battelle, Llc | Transparent omniphobic thin film articles |
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