JPH05185251A - Joint part of ni-ti alloy and joining method therefor - Google Patents
Joint part of ni-ti alloy and joining method thereforInfo
- Publication number
- JPH05185251A JPH05185251A JP4110833A JP11083392A JPH05185251A JP H05185251 A JPH05185251 A JP H05185251A JP 4110833 A JP4110833 A JP 4110833A JP 11083392 A JP11083392 A JP 11083392A JP H05185251 A JPH05185251 A JP H05185251A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- joining
- dissimilar metal
- members
- joint
- 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
- 238000005304 joining Methods 0.000 title claims abstract description 59
- 238000000034 method Methods 0.000 title claims abstract description 42
- 229910001069 Ti alloy Inorganic materials 0.000 title claims description 17
- 229910052751 metal Inorganic materials 0.000 claims abstract description 100
- 239000002184 metal Substances 0.000 claims abstract description 100
- 239000000956 alloy Substances 0.000 claims abstract description 92
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 90
- 229910001000 nickel titanium Inorganic materials 0.000 claims abstract description 64
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical compound [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 claims abstract description 60
- 238000002844 melting Methods 0.000 claims abstract description 22
- 230000008018 melting Effects 0.000 claims abstract description 21
- 238000005242 forging Methods 0.000 claims description 23
- 238000003825 pressing Methods 0.000 claims description 10
- 229910052759 nickel Inorganic materials 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 230000017525 heat dissipation Effects 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 239000004020 conductor Substances 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 229910001285 shape-memory alloy Inorganic materials 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims 1
- 229910052763 palladium Inorganic materials 0.000 claims 1
- 150000002739 metals Chemical class 0.000 abstract description 10
- 239000000155 melt Substances 0.000 abstract description 5
- 230000002542 deteriorative effect Effects 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 20
- 238000003466 welding Methods 0.000 description 19
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 9
- 239000010936 titanium Substances 0.000 description 9
- 230000000694 effects Effects 0.000 description 8
- 238000005219 brazing Methods 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 239000010949 copper Substances 0.000 description 6
- 239000011651 chromium Substances 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 238000007747 plating Methods 0.000 description 4
- 238000005452 bending Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 230000003446 memory effect Effects 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910000599 Cr alloy Inorganic materials 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000002093 peripheral effect Effects 0.000 description 2
- 230000005855 radiation Effects 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910000792 Monel Inorganic materials 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- GXDVEXJTVGRLNW-UHFFFAOYSA-N [Cr].[Cu] Chemical compound [Cr].[Cu] GXDVEXJTVGRLNW-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
- 239000000788 chromium alloy Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、Ｎｉ−Ｔｉ系合金、特
に形状記憶特性や超弾性特性を有するＮｉ−Ｔｉ系合金
部材と異種金属もしくは異種合金との高強度な接合部及
び、その接合方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength joint between a Ni--Ti alloy, particularly a Ni--Ti alloy member having shape memory characteristics and superelasticity, and a dissimilar metal or a dissimilar alloy, and the joint thereof. It is about the method.
【０００２】[0002]
【従来の技術】上記の形状記憶効果及び超弾性効果は、
共に変態ヒステリシスの小さい、いわゆる熱弾性形マル
テンサイト変態に起因するもので、形状記憶効果とは、
マルテンサイト温度領域で変形されたものがマルテンサ
イト逆変態（オーステナイト変態）温度以上に加熱する
と元の形に戻る現象である。一方、超弾性効果とは、オ
ーステナイト温度領域で変形した材料が、変形に伴う応
力誘起マルテンサイト変態によって、上記のような加熱
無しでも８％もの変形歪がゴムのように弾性的に元に戻
る現象である。2. Description of the Related Art The above-mentioned shape memory effect and superelastic effect are
Both are caused by so-called thermoelastic martensitic transformation, which has a small transformation hysteresis, and the shape memory effect is
This is a phenomenon in which the material deformed in the martensite temperature region returns to its original shape when heated above the martensite reverse transformation (austenite transformation) temperature. On the other hand, the superelastic effect means that a material deformed in the austenite temperature region elastically recovers 8% of the deformation strain like rubber without the above-mentioned heating due to the stress-induced martensitic transformation accompanying the deformation. It is a phenomenon.
【０００３】このような形状記憶および超弾性効果を示
す材料の中で最も実用化が進んでいるものにＮｉ−Ｔｉ
系合金がある。実際にこのＮｉ−Ｔｉ系合金で形状記憶
効果を応用実用化したものとしてはエアコンの吹き出し
口，炊飯ジャーの調圧弁，医療用ボーンプレイト等があ
る。また、超弾性効果を応用実用化したものとしては歯
列矯正ワイヤー，ブラジャーのカップワイヤー，眼鏡フ
レーム，医療用ガイドワイヤー等がある。さらに現在
は、このような実用化に伴い周辺技術の開発も進められ
ている。その中の一つに、Ｎｉ−Ｔｉ系合金と異種金属
との接合技術がある。Among the materials exhibiting such a shape memory and superelasticity effect, Ni-Ti is most practically used.
There are system alloys. Practical applications of the shape memory effect with this Ni-Ti alloy include air conditioner outlets, rice cooker pressure regulating valves, and medical bone plates. In addition, there are orthodontic wires, brassiere cup wires, spectacle frames, medical guide wires, and the like as applied and practical applications of the superelastic effect. Furthermore, at present, peripheral technologies are being developed along with such practical use. One of them is a joining technique of a Ni—Ti alloy and a dissimilar metal.
【０００４】[0004]
【発明が解決しようとする課題】Ｎｉ−Ｔｉ系合金は、
金属間化合物でありながら延性をもつ特異な合金である
が、その組成範囲はＮｉとＴｉが原子比で１：１近傍も
しくは、これに特定な元素を微量添加した極狭い範囲で
あり、この比が僅かにずれると急激に脆化する。また本
合金は高活性であるためＦｅ，Ｃｕ，Ｎｉなどの多くの
金属と容易に反応し脆弱な反応相を生成する。この反応
相の生成がＮｉ−Ｔｉ系合金と異種金属材料との溶接及
び、ろう接を困難なものとしている。The Ni--Ti alloy is
Although it is a unique alloy that is an intermetallic compound with ductility, its composition range is about 1: 1 in atomic ratio of Ni and Ti, or an extremely narrow range in which a specific element is added in a trace amount. If it deviates slightly, it becomes brittle. Further, since the present alloy is highly active, it easily reacts with many metals such as Fe, Cu and Ni to form a brittle reaction phase. The formation of this reaction phase makes welding and brazing of the Ni—Ti alloy and the dissimilar metal material difficult.
【０００５】従来Ｎｉ−Ｔｉ系合金の接合に関しては、
Ｎｉ−Ｔｉ系合金同士は、レーザー溶接，ＴＩＧ溶接，
電子ビーム溶接等の融接法もしくは、アップセットバッ
ト溶接，フラッシュバット溶接，摩擦圧接等の圧接法に
よって容易に接合でき、中でもアップセットバット溶接
が強度の点で優れていることが知られている。Regarding the conventional joining of Ni--Ti alloys,
Ni-Ti alloys are laser welded, TIG welded,
It can be easily joined by fusion welding such as electron beam welding or pressure welding such as upset butt welding, flash butt welding, friction welding, etc. Among them, it is known that upset butt welding is superior in strength. ..
【０００６】しかしながらＮｉ−Ｔｉ系合金と該合金以
外の異種金属とを直接高強度に溶接する技術は知られて
いなかった。これはＮｉ−Ｔｉ系合金が高活性であるた
め溶接加熱時に相手金属であるＦｅ，Ｃｕ，Ｎｉ等と容
易に反応して脆弱な反応相を生成してしまうことに起因
している。従って上記したどの溶接法を用いても、接合
部に脆弱な反応相を形成し実用に耐えうる強度を得るこ
とができなかった。このことから、Ｎｉ−Ｔｉ系合金を
異種金属と直接溶接することは不可能とされてきた。そ
こで、従来の接合技術では次の二つの方法がとられてき
た。However, a technique for directly welding a Ni--Ti alloy and a dissimilar metal other than the alloy with high strength has not been known. This is because the Ni-Ti alloy is highly active and easily reacts with the counterpart metals Fe, Cu, Ni, etc. during welding heating to generate a brittle reaction phase. Therefore, even if any of the above-mentioned welding methods is used, a brittle reaction phase is formed in the joint portion, and it is not possible to obtain the strength that can be practically used. From this, it has been impossible to directly weld the Ni-Ti alloy to the dissimilar metal. Therefore, the following two methods have been adopted in the conventional joining technique.
【０００７】その一つに、機械的接合法がある。これ
は、リベットなどでかしめたり、ビスで止める等の手段
によって接合する方法であるが、接合部が大きくなりま
た、繰り返し動作において緩みが生ずるなどの欠点があ
った。One of them is a mechanical joining method. This is a method of joining by means such as caulking with a rivet or stopping with a screw, but there are drawbacks that the joining portion becomes large and loosening occurs during repeated operation.
【０００８】また、他の一つの方法にメッキろう接法が
ある。これは、Ｎｉ−Ｔｉ系合金部材の接合面に予め、
ろう接性の良い金属たとえばニッケルや銅合金等をメッ
キし、その上から相手部材とろう接することによりＮｉ
−Ｔｉ系合金とろう材である溶融金属との反応を阻止
し、安定した接合強度を得る方法である。しかしなが
ら、接合強度がメッキの密着強度に依存するために高い
応力がかかる部位の接合は不可能であった。Another method is plating brazing. This is because the joint surface of the Ni-Ti alloy member is previously
By plating a metal having a good brazing property, such as nickel or a copper alloy, and brazing it with the mating member from above, Ni is formed.
This is a method of preventing a reaction between a Ti-based alloy and a molten metal which is a brazing material to obtain stable bonding strength. However, since the bonding strength depends on the adhesion strength of the plating, it is impossible to bond the parts to which high stress is applied.
【０００９】[0009]
【課題を解決するための手段】本発明は、上記の問題点
に鑑みなされたもので、Ｎｉ−Ｔｉ系合金から成る部材
と異種金属もしくは異種合金から成る部材とを直接溶接
接合する際に、溶融時に生成される脆弱な反応相を合理
的に処理することにより、Ｎｉ−Ｔｉ系合金の上記特性
を損なわないで両部材を強固に接合する接合方法と、そ
のような方法により得られた接合部を開示するものであ
る。SUMMARY OF THE INVENTION The present invention has been made in view of the above problems, and when a member made of a Ni--Ti alloy and a member made of a different metal or a different alloy are directly welded to each other, A bonding method in which both members are strongly bonded without deteriorating the above-mentioned properties of the Ni-Ti alloy by reasonably treating the brittle reaction phase generated during melting, and the bonding obtained by such a method. This section discloses the section.
【００１０】即ち本発明のＮｉ−Ｔｉ系合金と異種金属
との接合部は、Ｎｉ−Ｔｉ系合金と該合金以外の異種金
属との接合界面部が、該接合界面に接する少なくとも一
方の金属の溶融による両金属の反応溶融・加圧により得
られた溶湯鍛造組織と、これを挟んだＮｉ−Ｔｉ系合金
側に該合金を高温軟化させて加圧することにより得られ
たＮｉ−Ｔｉ系合金の熱間鍛造組織及び異種金属側に該
金属を高温軟化させて加圧することにより得られた上記
異種金属の熱間鍛造組織とからなることを特徴とするも
のである。That is, in the joint portion of the Ni—Ti alloy and the dissimilar metal of the present invention, the joint interface portion of the Ni—Ti alloy and the dissimilar metal other than the alloy is made of at least one metal in contact with the joint interface. Of the molten metal forging structure obtained by reaction melting and pressurization of both metals by melting, and the Ni-Ti alloy obtained by softening and pressing the Ni-Ti alloy at the Ni-Ti alloy alloy side The present invention is characterized by comprising a hot forged structure and a hot forged structure of the above-mentioned dissimilar metal obtained by softening the metal at a high temperature to the side of the dissimilar metal and pressurizing the metal.
【００１１】そしてこの場合、Ｎｉ−Ｔｉ系合金として
40〜60at％Ｎｉ−Ｔｉ合金、またはこのＮｉＴｉ合金の
ＮｉもしくはＴｉの一部をＦｅ，Ｃｒ，Ａｌ，Ｖ，Ｐ
ｄ，Ａｇ，Ｍｎ，Ｍｇ，Ｃｏ，Ｎｂ，Ｍｏ，Ｃｕの内の
一種もしくは二種以上を総量で20at％を越えない範囲で
置換したＮｉＴｉ合金からなる形状記憶合金または超弾
性合金を用いるのは有効であり、また異種金属としては
Ｎｉ，Ｔｉ，Ｃｕ，Ｆｅの単体金属、Ｎｉ基合金，Ｔｉ
基合金，Ｆｅ基合金，Ｃｕ基合金の何れかを用いるのが
効果が大きい。In this case, as a Ni--Ti alloy,
40-60 at% Ni-Ti alloy, or Ni or part of Ni of this NiTi alloy is Fe, Cr, Al, V, P
A shape memory alloy or a superelastic alloy made of a NiTi alloy in which one or more of d, Ag, Mn, Mg, Co, Nb, Mo, and Cu are substituted in a total amount not exceeding 20 at% is used. Effective and as dissimilar metals, simple metals of Ni, Ti, Cu and Fe, Ni-based alloys, Ti
It is highly effective to use any one of the base alloy, the Fe base alloy and the Cu base alloy.
【００１２】また本発明の接合方法は、Ｎｉ−Ｔｉ系合
金部材と異種金属部材とを接合するにあたり、両部材の
被接合面を互いに接触させ、その接合部を短時間に、ど
ちらか一方の部材の溶融温度まで加熱してこれを局部的
に反応溶融し、その溶融部に接する部分の両部材を高温
軟化せしめ、同時に両部材を介して接合部を高圧力で圧
縮加工することにより、接合界面に、上記両部材の反応
溶融・加圧により得られる溶湯鍛造組織を形成し、さら
にこの溶湯鍛造組織を挟んでＮｉ−Ｔｉ系合金部材側に
該部材を高温軟化させて加圧することにより得られるＮ
ｉ−Ｔｉ系合金の熱間鍛造組織と、異種金属部材側に該
部材を高温軟化させて加圧することにより得られる異種
金属の熱間鍛造組織を形成することを特徴とするもので
ある。Further, according to the joining method of the present invention, when joining a Ni--Ti alloy member and a dissimilar metal member, the surfaces to be joined of both members are brought into contact with each other, and the joining portion is made in a short period of time. By heating up to the melting temperature of the member and locally reacting and melting it, both parts of the part in contact with the melting part are softened at high temperature, and at the same time, the joint part is compressed by high pressure through both parts to join Obtained by forming a molten metal forging structure obtained by reaction melting and pressurization of both members on the interface, and further nipping the molten metal forging structure to the Ni-Ti alloy member side at high temperature to soften and pressurize the member. N to be
The present invention is characterized by forming a hot forged structure of an i-Ti alloy and a hot forged structure of a dissimilar metal obtained by softening the member at a different temperature at a high temperature and pressurizing the member.
【００１３】また本発明の他の接合方法としては、上記
接合方法において接合部を両部材を介して２kg／mm2 以
上の圧力で圧縮することにより、上記反応溶融部を接合
界面から外部へ押出して鋳造組織を有する押出部を接合
界面の外周に形成してなるものであり、この際上記押出
部を切除して研摩仕上げを施すのは有効である。As another joining method of the present invention, the reaction-melting portion is extruded from the joining interface to the outside by compressing the joining portion through both members at a pressure of 2 kg / mm 2 or more in the above joining method. In this case, an extruded portion having a cast structure is formed on the outer periphery of the joining interface. At this time, it is effective to cut off the extruded portion and perform a polishing finish.
【００１４】さらに本発明の他の接合方法としては、被
接合面近傍のＮｉ−Ｔｉ系合金部材側及び異種金属部材
側に高熱伝導材からなる放熱部を取付け、上記の外部へ
押出された反応溶融物を該放熱部に接触させて急冷凝固
せしめる接合方法を実施することを特徴とするものであ
る。Further, as another joining method of the present invention, a heat radiating portion made of a high thermal conductive material is attached to the Ni-Ti alloy member side and the dissimilar metal member side in the vicinity of the surfaces to be joined, and the reaction extruded to the outside is carried out. The present invention is characterized in that a joining method is carried out in which a melt is brought into contact with the heat radiating portion and rapidly solidified.
【００１５】[0015]
【作用】このように本発明では、Ｎｉ−Ｔｉ系合金と異
種金属との接合部の構成として、接合界面に両金属の溶
湯鍛造組織からなる層を形成し、これを挟んでそれぞれ
の金属の熱間鍛造組織の層を形成したものである。この
場合溶湯鍛造組織とは、上記のいずれかの金属材料が接
合界面で溶融した時に、同時にまたは溶融前から連続し
てこの接合界面を加圧することにより溶湯に対して加圧
力が伝達された状態で凝固した金属組織をいうものであ
る。そしてこの溶湯鍛造組織は接合界面全面にわたって
約20μｍ以下の厚さで形成するのが良い。従って接合界
面での局部的な加熱により生成される溶湯は短時間かつ
微小量で十分であり、本発明ではそのわずかに生成した
溶湯に加圧力を加えて凝固させることにより薄く層状の
溶湯鍛造組織を得るものである。As described above, according to the present invention, as the structure of the joint between the Ni--Ti alloy and the dissimilar metal, a layer made of the molten metal forging structure of both metals is formed at the joint interface, and the layers are sandwiched to form the layers of the respective metals. A layer of a hot forged structure is formed. In this case, the molten metal forging structure is a state in which a pressing force is transmitted to the molten metal when any of the above metal materials is melted at the bonding interface, by simultaneously or continuously pressurizing the bonding interface. It refers to the metallographic structure solidified in. The molten metal forging structure is preferably formed with a thickness of about 20 μm or less over the entire bonding interface. Therefore, a short time and a minute amount of the molten metal generated by local heating at the bonding interface are sufficient, and in the present invention, a slightly layered molten metal forging structure is obtained by applying a pressure to the slightly generated molten metal to solidify the molten metal. Is what you get.
【００１６】しかし接合界面部の加熱条件等により溶融
相が多量に生じたり、Ｎｉ−Ｔｉ系合金と異種金属との
脆弱な反応溶融相が生成した場合には、その接合部の強
度は低下してしまう。例えば51.0at％Ｎｉ−Ｔｉ合金線
材と80wt％Ｎｉ−20wt％Ｃｒ合金線材の端面同士を互い
に突合わせて、従来のアップセットバット溶接を行なっ
たところ、図９に示すように接合界面及びその外周部に
残留した溶融反応相から成る鋳造組織(9) と、さらに接
合部の外部にはみ出した溶融物がＮｉ−Ｔｉ系合金部材
表面と反応してできた液相−固相間の拡散層(10)という
二種類の脆弱相が生成しており、この二層を起点とする
破断こそが接合強度を低下させる主原因であることを突
き止めた。However, when a large amount of a molten phase is generated due to the heating condition of the joint interface or a brittle reaction melt phase of the Ni--Ti alloy and the dissimilar metal is generated, the strength of the joint decreases. Will end up. For example, when the end faces of a 51.0 at% Ni-Ti alloy wire rod and an 80 wt% Ni-20 wt% Cr alloy wire rod are butted against each other and conventional upset butt welding is performed, as shown in FIG. Cast structure (9) consisting of the molten reaction phase remaining in the joint, and a diffusion layer between the liquid phase and the solid phase formed by the reaction of the melt protruding outside the joint with the surface of the Ni-Ti alloy member ( Two types of fragile phases called 10) have been generated, and it was found that the fractures originating from these two layers are the main cause of the decrease in the bonding strength.
【００１７】そこで本発明は、そのような溶融反応相に
対しては、これを挟む異種金属側及びＮｉ−Ｔｉ系合金
側をともに高温軟化させて圧力媒体として利用すること
により、接合界面へ圧縮加工を施して上記脆弱な反応溶
融相や余分な溶融相を部材外部に押出すと共に、残留し
た最小量の溶融相に鍛造加工を施してこれを凝固せしめ
溶湯鍛造組織を形成して接合部を高強化せしめている。
さらに溶湯鍛造組織の両側の上記高温軟化した部分にも
加圧力が加わっているので熱間鍛造組織が形成され、接
合界面での応力集中を阻止するのに役立っている。Therefore, according to the present invention, with respect to such a molten reaction phase, both the dissimilar metal side and the Ni--Ti system alloy side sandwiching the molten reaction phase are softened at a high temperature and used as a pressure medium, thereby compressing to the bonding interface. While processing and extruding the fragile reaction melt phase and excess melt phase to the outside of the member, forge processing is performed on the minimum amount of remaining melt phase to solidify it and form a molten metal forging structure to form a joint part. Highly strengthened.
Further, since a pressing force is applied to the above-mentioned high temperature softened portions on both sides of the molten metal forging structure, a hot forging structure is formed, which serves to prevent stress concentration at the joint interface.
【００１８】ここで最低加圧力としては異種金属の物性
により変化するものであるが、一般に２kg／mm2 以上必
要である。加圧力が２kg／mm2 未満では接合界面から反
応溶融相等を外部へ押出す力が不足し、かつ得られる鍛
造組織も不十分である。Here, the minimum pressing force varies depending on the physical properties of the dissimilar metals, but it is generally required to be 2 kg / mm 2 or more. When the applied pressure is less than 2 kg / mm 2 , the force for extruding the reactive melt phase and the like from the joint interface to the outside is insufficient, and the obtained forged structure is also insufficient.
【００１９】また上記脆弱な拡散層に対しては、この生
成を阻むためには接合界面で生成される溶湯を最小量に
抑えて接合界面への加圧により押出される溶湯を最小限
にすることが肝要であるため、接合部の加熱は短時間及
び局部的と限定した。しかしながら溶湯生成量が多過ぎ
た場合であっても、本発明ではあらかじめ接合部近傍の
Ｎｉ−Ｔｉ系合金側及び異種金属側の両部材に高熱伝導
材からなる放熱部を取付けてあるので、接合界面の外部
へ押出された多量の溶湯は急速に凝固してＮｉ−Ｔｉ系
合金と溶湯との拡散反応相の生成を妨げることができ
る。特に押出された溶湯が直ちに放熱部（放熱治具）に
接触するように、両放熱治具を互いに接合界面に接近さ
せておけば溶湯は両放熱治具の間に延ばされるので急冷
にはより効果的である。For the fragile diffusion layer, in order to prevent this formation, the amount of molten metal generated at the joint interface should be minimized and the amount of molten metal extruded by the pressure applied to the joint interface should be minimized. However, the heating of the joint was limited to short time and local. However, even if the amount of molten metal produced is too large, in the present invention, the heat dissipating portion made of a high thermal conductive material is attached to both the Ni-Ti alloy side and the dissimilar metal side in the vicinity of the joint in advance. A large amount of the molten metal extruded to the outside of the interface can solidify rapidly and prevent the formation of a diffusion reaction phase between the Ni—Ti alloy and the molten metal. In particular, if both extruded melts are brought close to the joint interface so that the extruded melt immediately contacts the dissipative part (dissipation jig), the melt will be extended between the dissipative jigs, so it is better for rapid cooling. It is effective.
【００２０】ここで放熱部（放熱治具）とは上記のよう
に溶湯を接触せしめてこれを急冷凝固するものである
が、さらに接合界面を加圧する際に該接合部の位置がず
れないように固定せしめる作用も有する。なお、この放
熱治具は空冷による自然冷却でもよいが、比較的熱伝導
率の劣る素材からなる放熱治具を使用するときは、水も
しくは液体ガス等で該放熱治具を強制冷却すると効果は
大である。Here, the heat radiating portion (heat radiating jig) refers to the molten metal which is brought into contact with the molten metal as described above and rapidly solidified, but the position of the bonded portion is not displaced when the bonding interface is further pressurized. It also has the effect of fixing to. This heat radiating jig may be naturally cooled by air cooling, but when using a heat radiating jig made of a material having a relatively low thermal conductivity, forcibly cooling the heat radiating jig with water or liquid gas is not effective. Is large.
【００２１】なお上記部材外部に押出された溶湯は、接
合界面の外周部で凝固して通常の鋳造組織を有する押出
部を形成するので、該押出部は切除した後その表面は研
摩仕上げすることにより接合部は高い強度を保つことが
できる。Since the molten metal extruded to the outside of the member solidifies at the outer peripheral portion of the joint interface to form an extruded portion having a normal cast structure, the extruded portion is cut off and then its surface is polished to finish. This makes it possible to maintain high strength at the joint.
【００２２】また本発明では、両部材の接合部は局部的
に短時間で加熱されるので、接合部以外の特性劣化、特
に熱影響による形状記憶特性および超弾性特性の劣化は
阻止されるものであるが、さらに上記放熱治具を設けた
ので一層効果的である。Further, in the present invention, since the joint portion of both members is locally heated in a short time, deterioration of characteristics other than the joint portion, particularly deterioration of shape memory characteristics and superelasticity characteristics due to heat influence is prevented. However, since the heat dissipation jig is further provided, it is more effective.
【００２３】そしてこの放熱治具は、このような冷却効
果の他に接合部以外の変形を防止する効果があり、異形
材から成る精密部品の接合も可能である。In addition to such a cooling effect, this heat dissipation jig has the effect of preventing the deformation of the parts other than the joint, and it is also possible to join precision parts made of profiled materials.
【００２４】なお接合界面の加熱方法は通常の抵抗溶接
機を利用できる。A normal resistance welding machine can be used for heating the bonding interface.
【００２５】[0025]
【実施例】次に本発明を実施例により説明する。 （実施例１）圧縮装置(1) と溶接電源(2) とを備えた図
１に示す溶接機により、以下の実験を行なった。Ｎｉ−
Ｔｉ系合金として（51.0at％Ｎｉ−残Ｔｉ）から成る線
径 2.6mmで長さ20mmの超弾性線材(3) 及び表１に示す組
成の同じく線径 2.6mm×長さ20mmの異種金属線材(4) を
用い、両者を図１に示すように放熱治具として銅クロム
合金からなる空冷電極(5) でクランプし、先ず本発明接
合法として上記超弾性線材と異種金属線材の端面同士を
圧力装置(6) で20kg／mm2 、10kg／mm2 及び３kg／mm2
に加圧した状態で電流値を各金属の物性差により1500〜
3000Ａの間で最適値を選び、１／20秒間通電して接合し
た。次に比較接合法として加圧力を 1.5kg／mm2 に下
げ、その他は上記と同じ条件で両線材を接合した。EXAMPLES Next, the present invention will be described with reference to examples. (Example 1) The following experiment was conducted using the welding machine shown in Fig. 1 equipped with a compression device (1) and a welding power source (2). Ni-
Super-elastic wire (3) with a wire diameter of 2.6 mm and a length of 20 mm composed of (51.0 at% Ni-remaining Ti) as a Ti-based alloy, and a dissimilar metal wire rod of the same composition shown in Table 1 with a wire diameter of 2.6 mm and a length of 20 mm. Using (4), both are clamped by an air-cooled electrode (5) made of a copper chromium alloy as a heat radiating jig as shown in FIG. 1, and the end faces of the superelastic wire and the dissimilar metal wire are first joined by the joining method of the present invention. 20 kg / mm 2 at a pressure device (6), 10kg / mm 2 and 3 kg / mm 2
The current value is 1500-
The optimum value was selected in the range of 3000 A, and the current was applied for 1/20 seconds for joining. Next, as a comparative joining method, the pressure was reduced to 1.5 kg / mm 2 , and the other wires were joined under the same conditions as above.
【００２６】このときの本発明接合法による接合部の状
態を図２に、比較接合法による接合部の状態を図３に示
す。図２によれば押出された溶湯（Ｍ）が空冷電極(5)
(5)間に挟まれた状態でこれら電極(5)(5)に面接触して
強制冷却されて凝固しているのに対して、図３の加圧力
を下げた比較接合法では押出された溶湯（Ｍ）はその量
も少なく、且つ自然冷却されて凝固していた。また上記
超弾性線材の端面にＮｉメッキを施して、これに表１に
示す組成の異種金属線材をろう接した従来の接合法によ
り、両線材を接合した。FIG. 2 shows the state of the joint portion according to the joining method of the present invention at this time, and FIG. 3 shows the state of the joint portion according to the comparative joining method. According to FIG. 2, the extruded molten metal (M) is the air-cooled electrode (5).
In the state of being sandwiched between (5), these electrodes (5) and (5) are in surface contact with each other and are forcibly cooled and solidified, whereas in the comparative joining method in which the pressing force is lowered in FIG. The amount of molten metal (M) was small, and it was naturally cooled and solidified. Both ends of the superelastic wire were plated with Ni by a conventional bonding method in which a dissimilar metal wire having a composition shown in Table 1 was brazed to the end.
【００２７】これらの接合線材に対して、両端部を把持
して引張る引張り強度試験を施し、その結果接合部の引
張り強さが50kg／mm2 以上のものを◎、30kg／mm2 以上
50kg／mm2 未満のものを○、20kg／mm2 以上30kg／mm2
未満のものを△、20kg／mm2 未満のものを×として第１
表に示た。なお実用上必要な強度は20kg／mm2 以上であ
る。A tensile strength test of gripping both ends and pulling was performed on these joint wires, and as a result, those having a joint strength of 50 kg / mm 2 or more were marked with ◎, 30 kg / mm 2 or more.
Less than 50kg / mm 2 ○, 20kg / mm 2 or more 30kg / mm 2
Less than 1 is △, less than 20kg / mm 2 is x
Shown in the table. The strength required for practical use is 20 kg / mm 2 or more.
【００２８】[0028]
【表１】 [Table 1]
【００２９】表１から明らかなように接合時の加圧力が
10kg／mm2 の本発明接合法による接合部はいずれも20kg
／mm2 以上の強度を有し、十分実用的といえる。これに
対して従来のろう接によるものの強度はいずれも20kg／
mm2 未満と小さく、また接合時の加圧力が 1.5kg／mm2
と小さい比較接合法でも十分な接合強度は得られなかっ
た。As is clear from Table 1, the applied pressure at the time of joining is
20 kg for all joints made by the joining method of the present invention of 10 kg / mm 2.
It has a strength of / mm 2 or more and can be said to be sufficiently practical. In contrast, the strength of conventional brazing is 20 kg /
It is as small as less than mm 2 and the welding pressure at the time of joining is 1.5 kg / mm 2
Even with a small comparative joining method, sufficient joining strength could not be obtained.
【００３０】また上記接合線材のうちＮｉ−Ｔｉ系合金
（51.0at％Ｎｉ−残Ｔｉ）線材の相手材とて87Ｎｉ−13
Ｃｒの線材を20kg／mm2 の加圧力で接合した際の本発明
接合部の溶接組織写真を図４及び図５に、そして 1.5kg
／mm2 の圧力で接合した際の比較接合部の溶接組織写真
を図８として示した。Among the above-mentioned joining wire rods, 87Ni-13 was used as the counterpart of the Ni--Ti alloy (51.0 at% Ni--remaining Ti) wire rod.
4 and 5 are photographs of the welded structure of the joint portion of the present invention when the Cr wire rod is joined under the pressure of 20 kg / mm 2 , and 1.5 kg.
FIG. 8 shows a photograph of the welded structure of the comparative joint when the joint was performed at a pressure of / mm 2 .
【００３１】図４によれば、両合金の反応相が接合部の
外部に押出されており、さらに接合界面を拡大した図５
によれば接合界面には約10μｍの溶湯鍛造組織(11)が形
成され、これを挟んで一方側には51.0at％Ｎｉ−Ｔｉ合
金の熱間鍛造組織(12)と他方側には87Ｎｉ−13Ｃｒの熱
間鍛造組織(13)が形成されているのがわかる。また上記
51Ｎｉ−Ｔｉ合金の熱間鍛造組織(12)及び熱間鍛造を受
けていない51Ｎｉ−Ｔｉ合金の母材組織(14)の顕微鏡組
織写真をそれぞれ図６及び図７に示した。As shown in FIG. 4, the reaction phases of both alloys are extruded to the outside of the joint, and the joint interface is enlarged.
According to the method, a molten metal forging structure (11) of about 10 μm is formed at the joint interface, and a hot forging structure of 51.0 at% Ni-Ti alloy (12) is formed on one side and 87Ni- It can be seen that a hot forged structure (13) of 13Cr is formed. Also above
Microstructure photographs of the hot forged structure (12) of the 51Ni-Ti alloy and the base metal structure (14) of the 51Ni-Ti alloy which has not been subjected to the hot forging are shown in FIGS. 6 and 7, respectively.
【００３２】これに対して図８の組織写真によれば接合
界面の内部に反応相が残留していることが明らかであ
る。即ち加圧力不足および／または十分な熱間鍛造組織
が形成されなかったため反応溶融相が残留したまま凝固
してしまったものといえる。On the other hand, according to the structure photograph of FIG. 8, it is clear that the reaction phase remains inside the bonded interface. In other words, it can be said that the reaction melt phase solidified while the reactive melt phase remained because the pressure was insufficient and / or a sufficient hot forged structure was not formed.
【００３３】（実施例２）次に表１に示すSUS 304 線材
と51.0at％Ｎｉ−Ｔｉ合金からなる超弾性線材とを20kg
／mm2 と 1.5kg／mm2 の加圧力下で接合した接合線材及
び従来のメッキろう接で接合した接合線材について、接
合界面の位置を中心にして前後に90°ずつの角度（計 1
80°）で曲げる屈曲試験を毎分30回の速さにて 240回繰
返す繰返し曲げ試験を実施した。(Example 2) Next, 20 kg of SUS 304 wire shown in Table 1 and a super elastic wire made of 51.0 at% Ni-Ti alloy were used.
90mm forward and backward with respect to the position of the bonding interface (total 1) for the bonding wire and the conventional bonding wire that are bonded under pressure of 1.5 kg / mm 2 and 1.5 kg / mm 2.
A repeated bending test in which the bending test of bending at 80 °) was repeated 240 times at a speed of 30 times per minute was performed.
【００３４】その結果加圧力20kg／mm2 の本発明接合法
による接合線材では、試験終了後原形状に完全に復元し
て何らの変形もなく、超弾性特性は全く劣化していなか
った。これに対して加圧力 1.5kg／mm2 の比較接合法及
び従来のメッキろう接法による接合線材は、試験途中で
接合部にて破断してしまった。As a result, with the joining wire rod according to the present invention having a pressing force of 20 kg / mm 2 , after the test was completed, the original shape was completely restored, no deformation was observed, and the superelastic characteristics were not deteriorated at all. On the other hand, the joining wire rods by the comparative joining method with the applied pressure of 1.5 kg / mm 2 and the conventional plating brazing method were fractured at the joining part during the test.
【００３５】（実施例３）図１に示す溶接機により、以
下の実験を行なった。Ｎｉ−Ｔｉ系合金としてＮｉ50.8
at％−残Ｔｉから成る、 500℃・30分で直線状に記憶処
理を施した線径 1.5mm長さ40mmの丸線（以下丸線）１本
と異種金属としてモネルから成る長さ20mmの眼鏡フレー
ムのリム用異型線（以下異型線）２本を用いた。Example 3 The following experiment was conducted with the welding machine shown in FIG. Ni50.8 as Ni-Ti alloy
At% -remaining Ti, one round wire with a diameter of 1.5 mm and a length of 40 mm (hereinafter referred to as a round wire) that has been linearly memorized at 500 ° C for 30 minutes, and Monel as a dissimilar metal with a length of 20 mm. Two atypical lines for the rim of the spectacle frame (hereinafter atypical lines) were used.
【００３６】丸線(7) の両端部にそれぞれ異型線(8) の
先端部を５mm重ねて側面同士を接合すべく、図１０に示
す銅クロムからなる空冷電極治具(5')(5')にクランプ
し、10kg／mm2 に加圧した状態で1200Ａの電流を１／30
秒間通電して接合を完了した。このときの接合状態は図
１１に示すように、接合界面から押出された溶湯（Ｍ）
は放熱治具としての空冷電極治具(5')(5')に接触して急
冷凝固していることがわかった。The air-cooled electrode jig (5 ') (5') (5 ') made of copper chrome shown in FIG. ') And clamped at 10 kg / mm 2 and 1200A current is 1/30
Power was applied for 2 seconds to complete the joining. The joining state at this time is, as shown in FIG. 11, the molten metal (M) extruded from the joining interface.
It was found that was rapidly solidified by contacting the air-cooled electrode jigs (5 ') (5') as a heat dissipation jig.
【００３７】次に、接合界面から外部へ押し出された押
出部を切除研磨した後、両端のそれぞれの異型線をチャ
ッキングし、軸方向に左右に 120°づつの角度（計 240
°）で捻るの捻り試験を毎分10回の速度にて 1,000回繰
り返す繰り返し捻り試験を実施した。その結果、接合部
が破断すること無くまた、超弾性特性もほとんど劣化し
ていなかった。Next, after extruding and extruding the extruded portion extruded from the bonding interface to the outside, the irregular lines at both ends are chucked, and 120 ° to the left and right in the axial direction (total 240 °).
The twisting test of twisting was carried out repeatedly at a rate of 10 times per minute for 1,000 times. As a result, the joints were not broken and the superelastic properties were hardly deteriorated.
【００３８】このように本発明接合法は、Ｎｉ−Ｔｉ系
合金の優れた特性に何ら悪影響を及ぼすことなく、高強
度に異種金属材料とＮｉ−Ｔｉ系合金材料とを接合でき
るものである。これに対して比較接合法や従来接合法に
よるものは、接合強度が小さいために繰返し捻試験が実
施できなかった。As described above, the joining method of the present invention can join the dissimilar metal material and the Ni-Ti alloy material with high strength without adversely affecting the excellent characteristics of the Ni-Ti alloy. On the other hand, in the comparative joining method and the conventional joining method, the joint strength was too small to carry out the repeated twist test.
【００３９】[0039]
【発明の効果】このように本発明によれば、形状記憶特
性や超弾性特性などの優れた特性を有するＮｉ−Ｔｉ系
合金が他の異種金属と高強度で、かつ上記特性の劣化も
なく容易に接合できるので、Ｎｉ−Ｔｉ系合金材料の用
途を大きく広げる等顕著な効果を奏するものである。As described above, according to the present invention, a Ni-Ti alloy having excellent characteristics such as shape memory characteristics and superelasticity has high strength with other dissimilar metals and does not deteriorate the above characteristics. Since they can be easily joined, they have remarkable effects such as widening the applications of Ni-Ti alloy materials.
【図１】本発明接合法に使用した装置を示す説明図であ
る。FIG. 1 is an explanatory view showing an apparatus used in the joining method of the present invention.
【図２】本発明接合法による接合部を示す断面図であ
る。FIG. 2 is a cross-sectional view showing a joint portion according to the joining method of the present invention.
【図３】比較接合法による接合部を示す断面図である。FIG. 3 is a cross-sectional view showing a joint portion by a comparative joining method.
【図４】本発明接合法にて接合した51.0at％Ｎｉ−Ｔｉ
と87wt％Ｎｉ−13wt％Ｃｒとの接合部を示す金属組織写
真である（倍率17倍）。FIG. 4 is 51.0 at% Ni-Ti joined by the joining method of the present invention.
3 is a photograph of the metallographic structure showing the joint between the alloy and 87 wt% Ni-13 wt% Cr (magnification 17 times).
【図５】図４の接合部を拡大して示す金属組織写真であ
る（倍率1500倍）。FIG. 5 is a photograph of a metallographic structure showing an enlarged view of the joint portion of FIG. 4 (magnification: 1500 times).
【図６】図４の接合部の51.0at％Ｎｉ−Ｔｉ合金の熱間
鍛造組織を示す拡大金属組織写真である（倍率 700
倍）。6 is an enlarged metallographic photograph showing the hot forged structure of the 51.0 at% Ni—Ti alloy in the joint portion of FIG. 4 (magnification 700
Times).
【図７】図４の接合部近傍の51.0at％Ｎｉ−Ｔｉ合金の
母材組織を示す拡大金属組織写真である（倍率 700
倍）。7 is an enlarged metallographic photograph showing a base metal structure of a 51.0 at% Ni—Ti alloy in the vicinity of the joint in FIG. 4 (magnification 700
Times).
【図８】比較接合法にて接合した51.0at％Ｎｉ−Ｔｉと
87wt％Ｎｉ−13wt％Ｃｒとの接合部を示す金属組織写真
である（倍率17倍）。FIG. 8: 51.0 at% Ni-Ti joined by the comparative joining method
It is a metallographic photograph showing a joint with 87 wt% Ni-13 wt% Cr (magnification 17 times).
【図９】従来のアップセットバット溶接により51.0at％
Ｎｉ−Ｔｉと80wt％Ｎｉ−20wt％Ｃｒを接合した際の接
合部を示す金属組織の説明図である。FIG. 9: 51.0 at% by conventional upset butt welding
It is explanatory drawing of the metal structure which shows the joint part when joining Ni-Ti and 80 wt% Ni-20 wt% Cr.
【図１０】実施例３で用いた接合試験を示す説明図であ
る。FIG. 10 is an explanatory diagram showing a bonding test used in Example 3;
【図１１】実施例３の接合試験での接合部を示す断面図
である。FIG. 11 is a cross-sectional view showing a joint portion in a joint test of Example 3.
１ 圧縮装置 ２ 溶接電源 ３ 超弾性線材 ４ 異種金属線材 ５，５′ 空冷電極治具（放熱部、放熱治具） ６ 圧力装置 ７ Ｎｉ−Ｔｉ系合金丸線 ８ 異型線 ９ 鋳造組織 10 拡散層 11 溶湯鍛造組織 12 51Ｎｉ−Ｔｉ合金の熱間鍛造組織 13 87Ｎｉ−13Ｃｒ合金の熱間鍛造組織 14 51Ｎｉ−Ｔｉ合金の母材組織 DESCRIPTION OF SYMBOLS 1 Compressor 2 Welding power source 3 Super elastic wire rod 4 Dissimilar metal wire rod 5,5 'Air-cooled electrode jig (heat radiation part, heat radiation jig) 6 Pressure device 7 Ni-Ti alloy round wire 8 Variant wire 9 Cast structure 10 Diffusion layer 11 Molten metal forging structure 12 51 Ni-Ti alloy hot forging structure 13 87 Ni-13Cr alloy hot forging structure 14 51 Ni-Ti alloy base material structure
───────────────────────────────────────────────────── フロントページの続き (72)発明者 増永 悟 福井県福井市今市町第４号17番地 マスナ ガメンローパーク株式会社内 (72)発明者 村田 和男 福井県福井市今市町第４号17番地 マスナ ガメンローパーク株式会社内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Satoru Masunaga No. 4, Imaichi-cho, Fukui-shi, Fukui Prefecture No. 17 in Masuna Gamenlo Park Co., Ltd. (72) Inventor Kazuo Murata No. 4, Imaichi-cho, Fukui-shi, Fukui Prefecture Masuna Gamenlo Park Co., Ltd.
Claims (7)
属との接合界面部が、該接合界面に接する少なくとも一
方の金属の溶融による両金属の反応溶融・加圧により得
られた溶湯鍛造組織と、これを挟んだＮｉ−Ｔｉ系合金
側に該合金を高温軟化させて加圧することにより得られ
たＮｉ−Ｔｉ系合金の熱間鍛造組織及び異種金属側に該
金属を高温軟化させて加圧することにより得られた上記
異種金属の熱間鍛造組織とからなることを特徴とするＮ
ｉ−Ｔｉ系合金と異種金属の接合部。1. A molten metal forging obtained by the reaction melting and pressurization of a Ni-Ti alloy and a dissimilar metal other than the alloy at the joint interface portion by melting of at least one metal in contact with the joint interface. The structure and the hot forging structure of the Ni-Ti alloy obtained by softening the alloy at a high temperature to the Ni-Ti alloy side sandwiching the structure and pressurizing the alloy and the high temperature softening of the metal to the dissimilar metal side N comprising a hot forged structure of the above-mentioned dissimilar metal obtained by pressing
A joint between an i-Ti alloy and a dissimilar metal.
Ｔｉ合金、またはこのＮｉＴｉ合金のＮｉもしくはＴｉ
の一部をＦｅ，Ｃｒ，Ａｌ，Ｖ，Ｐｄ，Ａｇ，Ｍｎ，Ｍ
ｇ，Ｃｏ，Ｎｂ，Ｍｏ，Ｃｕの内の一種もしくは二種以
上を総量で20at％を越えない範囲で置換したＮｉＴｉ合
金からなる形状記憶合金または超弾性合金である請求項
１記載のＮｉ−Ｔｉ系合金と異種金属の接合部。2. The Ni-Ti alloy is 40-60 at% Ni-
Ti alloy, or Ni or Ti of this NiTi alloy
Part of Fe, Cr, Al, V, Pd, Ag, Mn, M
The Ni-Ti alloy according to claim 1, which is a shape memory alloy or a superelastic alloy made of a NiTi alloy in which one or more of g, Co, Nb, Mo and Cu are substituted in a total amount not exceeding 20 at%. Joint of dissimilar metal with system alloy.
ｉ基合金，Ｔｉ基合金，Ｆｅ基合金，Ｃｕ基合金の何れ
かである請求項１記載のＮｉ−Ｔｉ系合金と異種金属の
接合部。3. The dissimilar metal is Ni, Ti, Cu, Fe, N.
The joint between the Ni-Ti alloy and the dissimilar metal according to claim 1, which is one of an i-based alloy, a Ti-based alloy, a Fe-based alloy, and a Cu-based alloy.
を接合するにあたり、両部材の被接合面を互いに接触さ
せ、その接合部を短時間に、どちらか一方の部材の溶融
温度まで加熱してこれを局部的に反応溶融し、その溶融
部に接する部分の両部材を高温軟化せしめ、同時に両部
材を介して接合部を高圧力で圧縮加工することにより、
接合界面に、上記両部材の反応溶融・加圧により得られ
る溶湯鍛造組織を形成し、さらにこの溶湯鍛造組織を挟
んでＮｉ−Ｔｉ系合金部材側に該部材を高温軟化させて
加圧することにより得られるＮｉ−Ｔｉ系合金の熱間鍛
造組織と、異種金属部材側に該部材を高温軟化させて加
圧することにより得られる異種金属の熱間鍛造組織を形
成することを特徴とするＮｉ−Ｔｉ系合金の接合方法。4. When joining a Ni—Ti alloy member and a dissimilar metal member, the surfaces to be joined of both members are brought into contact with each other, and the joining portion is heated to the melting temperature of one of the members in a short time. Then, this is locally melted by melting, and both members of the portion in contact with the melted portion are softened at high temperature, and at the same time, the joint portion is compressed by high pressure through both members,
By forming a molten metal forging structure obtained by reaction melting and pressurization of both members at the joint interface, and further nipping the molten metal forging structure to the Ni-Ti alloy member side to soften the member at high temperature and press it A hot forged structure of the obtained Ni-Ti alloy, and a hot forged structure of a dissimilar metal obtained by softening and pressing the member at the dissimilar metal member side at a high temperature. Method of joining base alloys.
を接合するにあたり、両部材の被接合面を互いに接触さ
せ、その接合部を短時間にどちらか一方の部材の溶融温
度まで加熱してこれを局部的に反応溶融し、この溶融部
に接する部分の両部材を高温軟化せしめ、同時に両部材
を介して接合部を２kg／mm2 以上の圧力で加圧圧縮する
ことにより、上記溶融部を上記接合界面から外部へ押出
して鋳造組織を有する押出部を接合界面の外周に形成
し、かつ接合界面に上記両部材の溶融・加圧により得ら
れる溶湯鍛造組織を形成し、さらにこの溶湯鍛造組織を
挟んでＮｉ−Ｔｉ系合金部材側に該部材を高温軟化させ
て加圧することにより得られるＮｉ−Ｔｉ系合金の熱間
鍛造組織と、異種金属部材側に該部材を高温軟化させて
加圧することにより得られる上記異種金属の熱間鍛造組
織を形成することを特徴とするＮｉ−Ｔｉ系合金と異種
金属の接合方法。5. When joining a Ni—Ti alloy member and a dissimilar metal member, the surfaces to be joined of both members are brought into contact with each other, and the joining portion is heated to the melting temperature of one of the members in a short time. By locally reacting and melting it, softening both members at the part in contact with this melting part at a high temperature, and simultaneously pressing and compressing the joint through both members at a pressure of 2 kg / mm 2 or more Part is extruded to the outside from the joining interface to form an extruded part having a cast structure on the outer periphery of the joining interface, and a molten metal forging structure obtained by melting and pressurizing the both members is formed at the joining interface, and further the molten metal is formed. A hot forged structure of Ni-Ti alloy obtained by softening the member at high temperature to the Ni-Ti alloy member side by sandwiching the forged structure and pressurizing the member, and softening the member at high temperature to the dissimilar metal member side. Obtained by pressurizing A method for joining a Ni-Ti alloy and a dissimilar metal, characterized in that a hot forged structure of the dissimilar metal is formed.
れた少なくとも上記一方の部材の鋳造組織を有する押出
部を切除して研摩仕上げを施した請求項５記載のＮｉ−
Ｔｉ系合金と異種金属の接合方法。6. The Ni- according to claim 5, wherein the extruded portion of at least one of the members formed by extruding from the bonding interface to the outside is cut off and polished.
A method for joining a Ti-based alloy and a dissimilar metal.
接合するにあたり、被接合面近傍のＮｉ−Ｔｉ系合金部
材及び異種金属部材に高熱伝導材からなる放熱部を取付
けて両部材の被接合面を互いに接触させ、その接合部を
短時間に、どちらか一方の部材の溶融温度まで加熱して
これを局部的に反応溶融し、その溶融部に接する部分の
両部材を高温軟化せしめ、同時に両部材を介して接合部
を高圧力で圧縮加工することにより、接合部外に押し出
した反応溶融物を上記放熱部に接触せしめて急速に凝固
させると共に、接合界面に、上記両部材の溶融・加圧に
より得られる溶湯鍛造組織を形成し、さらにこの溶湯鍛
造組織を挟んでＮｉ−Ｔｉ系合金部材側に該部材を高温
軟化させて加圧することにより得られるＮｉ−Ｔｉ系合
金の熱間鍛造組織と、異種金属部材側に該部材を高温軟
化させて加圧することにより得られる異種金属の熱間鍛
造組織を形成することを特徴とするＮｉ−Ｔｉ系合金と
異種金属の接合方法。7. When joining a Ni—Ti based alloy member to a dissimilar metal member, a radiating portion made of a high thermal conductive material is attached to the Ni—Ti based alloy member and the dissimilar metal member in the vicinity of the surfaces to be joined to attach the members. The joining surfaces are brought into contact with each other, and the joining portion is heated in a short time to the melting temperature of one of the members to locally react and melt it, and both members of the portion in contact with the melting portion are softened at high temperature, At the same time, by compressing the joint portion with high pressure through both members, the reaction melt extruded outside the joint portion is brought into contact with the heat dissipation portion to rapidly solidify, and at the joint interface, the melting of both members is performed. Hot forming of a Ni-Ti alloy obtained by forming a molten metal forging structure obtained by pressurization, further nipping the molten metal forging structure to the Ni-Ti alloy member side, and softening and pressing the member at high temperature. With forged tissue A method for joining a Ni-Ti alloy and a dissimilar metal, which comprises forming a hot forged structure of a dissimilar metal obtained by softening the member at a high temperature and pressurizing it on the dissimilar metal member side.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11083392A JP2737817B2 (en) | 1991-04-09 | 1992-04-03 | Joint between Ni-Ti alloy and dissimilar metal and joining method thereof |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10345291 | 1991-04-09 | ||
| JP3-103452 | 1991-04-09 | ||
| JP11083392A JP2737817B2 (en) | 1991-04-09 | 1992-04-03 | Joint between Ni-Ti alloy and dissimilar metal and joining method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05185251A true JPH05185251A (en) | 1993-07-27 |
| JP2737817B2 JP2737817B2 (en) | 1998-04-08 |
Family
ID=26444090
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11083392A Expired - Lifetime JP2737817B2 (en) | 1991-04-09 | 1992-04-03 | Joint between Ni-Ti alloy and dissimilar metal and joining method thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2737817B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012104539A (en) * | 2010-11-08 | 2012-05-31 | Showa Denko Kk | Cladding material for insulating substrate |
| JP2015507085A (en) * | 2011-12-16 | 2015-03-05 | レイセオン カンパニー | Superelastic wire and forming method |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4277117B2 (en) * | 2007-03-29 | 2009-06-10 | 福井県 | Dissimilar metal joined body of nickel / titanium alloy material and pure titanium material and joining method thereof |
-
1992
- 1992-04-03 JP JP11083392A patent/JP2737817B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012104539A (en) * | 2010-11-08 | 2012-05-31 | Showa Denko Kk | Cladding material for insulating substrate |
| JP2015507085A (en) * | 2011-12-16 | 2015-03-05 | レイセオン カンパニー | Superelastic wire and forming method |
| US10119176B2 (en) | 2011-12-16 | 2018-11-06 | Raytheon Company | Superelastic wire and method of formation |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2737817B2 (en) | 1998-04-08 |
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