JP3434126B2 - Liquid phase diffusion bonding alloy foil that can be bonded in oxidizing atmosphere - Google Patents
Liquid phase diffusion bonding alloy foil that can be bonded in oxidizing atmosphereInfo
- Publication number
- JP3434126B2 JP3434126B2 JP14203896A JP14203896A JP3434126B2 JP 3434126 B2 JP3434126 B2 JP 3434126B2 JP 14203896 A JP14203896 A JP 14203896A JP 14203896 A JP14203896 A JP 14203896A JP 3434126 B2 JP3434126 B2 JP 3434126B2
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- Japan
- Prior art keywords
- liquid phase
- phase diffusion
- diffusion bonding
- bonding
- joint
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- 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.)
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Description
【０００１】[0001]
【発明の属する技術分野】本発明は、厚鋼板、鋼管、棒
鋼（鋼線、鉄筋を含む）等のＦｅ基材料を接合対象とし
て、酸化雰囲気中での液相拡散接合を可能とし、接合強
度に優れた接合部を短時間で得ることができる液相拡散
接合用合金箔に関するものである。TECHNICAL FIELD The present invention enables Fe-based materials such as thick steel plates, steel pipes, steel bars (including steel wires and reinforcing bars) to be bonded, and enables liquid phase diffusion bonding in an oxidizing atmosphere to improve the bonding strength. The present invention relates to a liquid phase diffusion bonding alloy foil capable of obtaining a highly excellent bonded portion in a short time.
【０００２】[0002]
【従来の技術】液相拡散接合は、接合しようとする材料
の間に箔、粉末、あるいはメッキ等の形態で被接合材よ
りも融点の低い共晶組成を有する合金を介在させて加圧
し、挿入合金（以下「インサートメタル」と称する）の
液相線直上の温度に接合部を加熱することによって溶
融、等温凝固させる接合法であり、固相接合法の１種と
考えられている。この液相拡散接合は、比較的低い加圧
力で接合できることから、従来、接合による残留応力
や、変形を極力避ける必要のある接合に用いられ、主と
して同時に溶接の困難な高合金鋼、耐熱鋼あるいはこれ
らと炭素鋼との接合に適用されている。一方、炭素鋼か
らなる一般鋼材どうしの接合手段としては、従来から各
種の溶接が主流であり、液相拡散接合が適用された例は
少ない。2. Description of the Related Art In liquid phase diffusion bonding, a material to be bonded is pressed with an alloy having a eutectic composition having a melting point lower than that of a material to be bonded in the form of foil, powder, or plating. This is a joining method of melting and isothermally solidifying an insertion alloy (hereinafter referred to as “insert metal”) by heating the joining portion to a temperature just above the liquidus line, and is considered to be one of solid-phase joining methods. Since this liquid phase diffusion bonding can be bonded with a relatively low pressure, it has been conventionally used for bonding where it is necessary to avoid residual stress and deformation due to bonding as much as possible, and at the same time, high alloy steel, heat resistant steel or It is applied to the joining of these with carbon steel. On the other hand, as a means for joining general steel materials made of carbon steel, various kinds of welding have been mainly used conventionally, and there are few cases where liquid phase diffusion joining is applied.
【０００３】液相拡散接合は、合金組成として０．５０
％以上のＣｒを含有する被接合材料の接合に適用されて
いる場合が多い。このＣｒ含有材料は緻密な酸化Ｃｒ
（多くの場合Ｃｒ2 Ｏ3 ）皮膜を表面に形成するため
に、耐酸化性、耐食性が優れているのが特徴である。し
たがって、接合時の加熱によっても当然ながら接合面に
酸化皮膜が形成されることとなり、溶融したインサート
メタルの濡れが阻害され、接合に必要な原子の拡散が著
しく妨げられ、良好な接合部を得ることは困難であっ
た。Liquid phase diffusion bonding has an alloy composition of 0.50.
In many cases, it is applied to the joining of materials to be joined containing Cr of more than 50%. This Cr-containing material is a dense Cr oxide
Since a (often Cr 2 O 3 ) film is formed on the surface, it is characterized by excellent oxidation resistance and corrosion resistance. Therefore, even when heating at the time of bonding, an oxide film is naturally formed on the bonding surface, the wetting of the molten insert metal is hindered, the diffusion of atoms necessary for bonding is significantly hindered, and a good bonding portion is obtained. It was difficult.
【０００４】そのため、従来、特開昭５３−８１４５８
号公報、特開昭６２−３４６８５号公報、更に特開昭６
２−２２７５９５号公報に見られるように、何れも液相
拡散接合の際、雰囲気を真空、不活性、もしくは還元性
に保たねばならず、接合コストの著しい上昇を招いてい
た。Therefore, in the past, Japanese Patent Laid-Open No. 53-81458 has been used.
JP, JP-A-62-34685, and JP-A-6-
As can be seen from JP-A-2-227595, in any of the liquid phase diffusion bonding, the atmosphere had to be kept in vacuum, inactive, or reducible, resulting in a significant increase in bonding cost.
【０００５】本発明者らは、ステンレス鋼、高ニッケル
基合金、耐熱合金鋼あるいはこれらの合金鋼を接合対象
として液相拡散接合を適用する場合において、大気中で
酸化被膜が被接合材表面に生成していても液相拡散接合
が可能で、接合コストを低減しながら良好な接合部を短
時間に得られる液相拡散接合を提供するために種々研究
を重ねた結果、Ｖを０．１〜２０．０原子％含有し、Ｓ
ｉを増量したインサートメタルを用いれば、大気中など
酸化雰囲気中でも液相拡散接合が可能であることを見い
出した。The present inventors have found that when liquid phase diffusion bonding is applied to stainless steel, high nickel base alloy, heat resistant alloy steel or these alloy steels, an oxide film is formed on the surface of the material to be bonded in the atmosphere. Liquid phase diffusion bonding is possible even if it is generated, and as a result of various studies to provide liquid phase diffusion bonding that can obtain a good joint in a short time while reducing the bonding cost, V was 0.1 ~ 20.0 atomic%, S
It was found that liquid phase diffusion bonding can be performed even in an oxidizing atmosphere such as the air by using an insert metal with an increased i.
【０００６】すなわち、Ｖはインサートメタルの融点を
上昇させる元素ではあるが、他の元素（本発明において
は専らＳｉ）を適当に調整することで接合性の極めて優
れたインサートメタルを得ることができることを見い出
し、先に特開平２−１５１３７７号公報、特開平２−１
５１３７８号公報、特開平２−１８５９４０号公報、特
開平７−２６８５２１号公報、特開平７−２７６０６６
号公報等に開示されるような、主としてステンレス鋼、
高ニッケル基合金、耐熱合金鋼あるいはこれらの合金鋼
と炭素鋼の液相拡散接合に用いられるＮｉベースのＶ、
Ｓｉを含有する酸化雰囲気中で接合可能な液相拡散接合
用合金箔を提案した。しかし、これらのＮｉベースの液
相拡散接合用合金箔は、上記したように主としてステン
レス鋼、高ニッケル基合金、耐熱合金鋼を接合対象とし
て、用いられるものでありＮｉをベースとするものであ
る。That is, V is an element that raises the melting point of the insert metal, but by appropriately adjusting other elements (in the present invention, exclusively Si), an insert metal having excellent bondability can be obtained. First, the inventors found out Japanese Patent Laid-Open Nos. 2-151377 and 2-1.
No. 51378, No. 2-185940, No. 7-268521, No. 7-276066.
Mainly stainless steel, as disclosed in Japanese Patent Publication No.
Ni-based V used for liquid phase diffusion bonding of high nickel base alloys, heat resistant alloy steels or these alloy steels and carbon steels,
We proposed an alloy foil for liquid phase diffusion bonding that can be bonded in an oxidizing atmosphere containing Si. However, as described above, these Ni-based alloy foils for liquid phase diffusion bonding are mainly used for bonding stainless steel, high nickel-based alloys, and heat-resistant alloy steels, and are Ni-based. .
【０００７】本発明者らは、最近、狭隘な場所で例えば
炭素鋼による鋼管、鉄筋、厚板などの鋼材で代表される
Ｆｅ基材料を、より短時間でかつ十分な接合強度を確保
しつつ低コストで接合することの要請が高まってきてお
り、従来の各種の溶接による接合によってはこの要請に
十分に応えられないとの認識に基づいて、Ｆｅ基材料を
接合対象として大気中での液相拡散接合の適用について
検討した。その結果、これらのＦｅ基材料を液相拡散接
合する場合に、上記Ｎｉベースの液相拡散接合用合金箔
をインサートメタルとして用いた場合には、被接合材間
にＮｉ相が介在して拡散組織が不均質になり、接合時間
が長くなるとともに、接合強度、靭性にも影響すること
から、上記の要請に十分に応えることは困難であること
を確認するに至った。Recently, the present inventors have been able to secure a sufficient bonding strength in a short time by using an Fe-based material typified by a steel material such as a steel pipe made of carbon steel, a reinforcing bar and a thick plate in a narrow space in a shorter time. There is an increasing demand for low-cost joining, and based on the recognition that conventional joining by various types of welding cannot sufficiently meet this requirement, the Fe-based material is used as a joining target for liquid bonding in the atmosphere. The application of phase diffusion bonding was examined. As a result, in the case of liquid phase diffusion bonding of these Fe-based materials, when the above Ni-based liquid phase diffusion bonding alloy foil is used as an insert metal, the Ni phase intervenes between the materials to be bonded and diffuses. It has been confirmed that it is difficult to sufficiently meet the above requirements, because the structure becomes heterogeneous, the bonding time becomes long, and the bonding strength and toughness are affected.
【０００８】[0008]
【発明が解決しようとする課題】本発明は、例えば炭素
鋼による厚鋼板、鋼管、棒鋼（鋼線、鉄筋を含む）等の
鋼材で代表されるＦｅ基材料を接合対象として、酸化雰
囲気で短時間に、均質な組織を有し十分な接合強度を有
する接合部を確保できる、酸化雰囲気中で接合可能なＦ
ｅ基材料の液相拡散接合用合金箔を提供するものであ
る。The present invention is intended for joining Fe-based materials represented by steel materials such as thick steel plates made of carbon steel, steel pipes, and steel bars (including steel wires and reinforcing bars) in an oxidizing atmosphere. F that can be bonded in an oxidizing atmosphere and can secure a bonded part having a uniform structure and sufficient bonding strength in time
An alloy foil for liquid phase diffusion bonding of an e-based material is provided.
【０００９】[0009]
【課題を解決するための手段】本発明は、Ｆｅをベース
とし、Ｓｉ、Ｖを必須成分として含有する、Ｆｅ基材料
同士を接合対象として、酸化雰囲気中で接合可能な液相
拡散接合用合金箔であり、（１）
第一の発明は、原子％で、
Ｂ ：１．０〜２０．０％、 Ｓｉ：１．０〜１４．６９％、
Ｖ ：０．１〜２０．０％
を含有し、残部は実質的にＦｅおよび不可避の不純物か
らなる組成を有し、厚さが３．０〜１００μｍであるこ
とを特徴とする。The present invention SUMMARY OF] is a Fe-based, containing Si, and V as essential components, Fe-based materials
To each other as bonding target is bondable liquid phase diffusion bonding alloy foil in an oxidizing atmosphere, (1) the first invention, in atomic%, B: 1.0~20.0%, Si : 1 0.0 to 14.69 %, V: 0.1 to 20.0%, the balance substantially consisting of Fe and inevitable impurities, and the thickness is 3.0 to 100 μm. Is characterized by.
【００１０】（２）第二の発明は、前記（１）記載の成
分に、原子％でさらに、
Ｃｒ：０．１〜２０．０％、 Ｎｉ：０．１〜１５．０％、
Ｃｏ：０．１〜１５．０％
の一種または二種以上を含有することを特徴とする。 (2) A second aspect of the present invention is the result of the above (1).
Min, further atomic%, Cr: 0.1~20.0%, Ni : 0.1~15.0%, Co: 0.1~15.0% of one or to contain two or more Is characterized by.
【００１１】（３）第三の発明は、前記（１）又は
（２）記載の成分に、原子％でさらに、
Ｗ ：０．１〜１０．０％、 Ｎｂ：０．１〜１０．０％、
Ｔｉ：０．１〜１０．０％
の一種または二種以上を含有することを特徴とする。 (3) The third aspect of the present invention is the above (1) or
(2) In addition to the component, in atomic%, W: 0.1 to 10.0%, Nb: 0.1 to 10.0%, Ti: 0.1 to 10.0%, or two or more. It is characterized by containing the above.
【００１２】（４）第四の発明は、組織の結晶構造が実
質的に非晶質であることを特徴とする第一〜第三の発明
のいずれか１項に記載の酸化雰囲気中で接合可能な液相
拡散接合用合金箔である。[0012] (4) The fourth aspect of the invention, bonding the crystal structure of the organization in an oxidizing atmosphere according to any one of substantially the first to third invention, wherein the amorphous possible liquid phase diffusion is bonding alloy foil.
【００１３】なお、本発明において、「Ｆｅ基材料」と
は、Ｆｅを原子％で５０％以上含有している各種の炭素
鋼による鋼材を意味している。「実質的に非晶質」と
は、組織の結晶構造の５０％以上が非晶質になっている
ものを意味している。「液相拡散接合」とは、拡散ろう
付けを含むものであり、接合しようとする材料の間に
箔、粉末、あるいはメッキ等の形態で被接合材よりも融
点の低い共晶組成を有する合金を介在させて加圧し、挿
入合金（以下インサートメタルと称する）の液相線直上
の温度に接合部を加熱することによって溶融、等温凝固
させる接合法であるが、溶融とは完全溶融の場合のみで
はなく、５０％以上の溶融を含んでいる。In the present invention, the "Fe-based material" means steel materials made of various carbon steels containing 50% or more of Fe in atomic%. “Substantially amorphous” means that 50% or more of the crystal structure of the structure is amorphous. "Liquid phase diffusion bonding" includes diffusion brazing, and an alloy having a eutectic composition having a melting point lower than that of the material to be bonded in the form of foil, powder, or plating between the materials to be bonded. It is a joining method of melting and isothermally solidifying by pressurizing through interposing and heating the joint to a temperature just above the liquidus of the insertion alloy (hereinafter referred to as insert metal), but melting is only in the case of complete melting Rather, it contains more than 50% melting.
【００１４】「酸化雰囲気」とは、接合雰囲気中に体積
％で０．１％以上の酸素ガスを含有し、酸素分圧が１０
-3atm 以上、すなわち還元性のガス、例えばＨ2 ，Ｈ2
Ｓ，水蒸気その他を含有している場合でも酸化力が酸素
濃度相当で０．１％以上である雰囲気を意味している。
また「融点」とは、２元以上の合金においては、その状
態図上での固相線を、特に断わらない限りにおいて意味
するものとする。The "oxidizing atmosphere" means that the bonding atmosphere contains 0.1% or more by volume of oxygen gas and the oxygen partial pressure is 10%.
-3 atm or more, that is, reducing gas such as H 2 and H 2
Even if it contains S, water vapor, etc., it means an atmosphere having an oxidizing power of 0.1% or more corresponding to the oxygen concentration.
In addition, "melting point" means a solidus line on a phase diagram of a binary or more alloy, unless otherwise specified.
【００１５】[0015]
【発明の実施の形態】本発明は、上記の特開平２−１５
１３７７号公報、特開平２−１５１３７８号公報、特開
平２−１８５９４０号公報、特開平７−２６８５２１号
公報、特開平７−２７６０６６号公報等に開示されるよ
うな、ＮｉベースのＶ、Ｓｉを含有する液相拡散接合用
合金箔で得られる効果に着目し、Ｆｅ基材料を接合対象
として、Ｎｉ相による組織不均一などの問題を生じな
い、液相拡散接合用合金箔について種々検討を重ね本発
明に到達した。BEST MODE FOR CARRYING OUT THE INVENTION The present invention is described in the above-mentioned JP-A-2-15.
Ni-based V and Si as disclosed in JP 1377, JP 2-151378 A, JP 2-185940 A, JP 7-268521 A, JP 7-276066 A, etc. Focusing on the effect obtained with the contained alloy foil for liquid phase diffusion bonding, various studies have been repeated on the alloy foil for liquid phase diffusion bonding that uses Fe-based materials as a bonding target and does not cause problems such as nonuniformity of the structure due to the Ni phase. The present invention has been reached.
【００１６】本発明では、被接合材のＦｅ基の組織に対
して組織不均一の問題を生じるＮｉを含有させる場合は
原子％で０．１〜１５％の範囲に抑え、接合対象である
Ｆｅ基材料と同様、Ｆｅベースとし、これに拡散元素で
低融点化に寄与するＢ、低融点化に寄与するＳｉ、酸化
被膜の影響を軽微にするＶを必須成分として含有する、
Ｆｅベースの酸化雰囲気中で接合可能なＦｅ基材料の液
相拡散接合用合金箔であり、これらの成分に主として接
合部の耐食性を高めるＣｒ、Ｎｉ、Ｃｏの一種または二
種以上を、あるいは主として接合部強度を高めるＷ、Ｎ
ｂ、Ｔｉの一種または二種以上を選択的に含有させ、さ
らに接合部の耐食性を高めるＣｒ、Ｎｉ、Ｃｏの一種ま
たは二種以上と、主として接合部強度を高めるＷ、Ｎ
ｂ、Ｔｉの一種または二種以上を同時に含有させるもの
である。In the present invention, in the case of containing Ni which causes the problem of non-uniformity of the Fe-based structure of the material to be joined, the content of Ni is controlled to be in the range of 0.1 to 15% by atomic% and the Fe to be joined Like the base material, it is Fe-based and contains B as a diffusion element that contributes to lowering the melting point, Si that contributes to lowering the melting point, and V that minimizes the effect of the oxide film as essential components.
An alloy foil for liquid phase diffusion bonding of an Fe-based material capable of bonding in an Fe-based oxidizing atmosphere, and these components mainly include one or more of Cr, Ni, and Co that enhance the corrosion resistance of the bonding portion, or mainly. W, N to increase the strength of the joint
One or more of b, Ti are selectively contained, and one or more of Cr, Ni, Co, which further enhances the corrosion resistance of the joint, and W, N, which mainly enhances the strength of the joint.
One or more of b and Ti are contained at the same time.
【００１７】これらの選択成分は、接合対象の成分組
成、接合部に求められる特性等に応じて組み合わせ、適
量含有させる。拡散原子としては、Ｂ、Ｐが知られてい
るが、本発明では、接合温度が１０５０〜１３００℃で
Ｐの場合より２００℃以上高くなるが、Ｐの場合より拡
散係数が大きく接合時間を大幅に短縮して接合強度を大
幅に高められるＢを拡散原子として選択する。These selected components are combined in appropriate amounts according to the composition of the components to be joined, the characteristics required for the joint, and the like. Although B and P are known as diffusing atoms, in the present invention, the bonding temperature is 1050 to 1300 ° C., which is higher by 200 ° C. or more than in the case of P, but the diffusion coefficient is large and the bonding time is significantly longer than in the case of P. B is selected as a diffusion atom, which can be shortened to 10 and greatly increases the bonding strength.
【００１８】以下に本発明で用いる各成分について、含
有させる目的と含有量について、説明する。
（１）Ｆｅベース（Ｆｅが原子％で５０％以上含有）と
する。
被接合材がＦｅ基材料（Ｆｅが原子％で５０％以上含有
する炭素鋼による鋼材）であり、Ｎｉベースとした場合
のようなＮｉ相の介在による組織の不均質がなく、接合
時間を短縮するとともに、接合強度を容易に確保でき
る。The purpose and content of each component used in the present invention will be described below. (1) Fe base (containing 50% or more of Fe in atomic%). The material to be joined is a Fe-based material (steel material made of carbon steel containing 50% or more of atomic% Fe), and there is no inhomogeneity in the structure due to the interposition of the Ni phase as in the case of Ni base, and the joining time is shortened In addition, the bonding strength can be easily secured.
【００１９】（２）Ｂは１．０〜２０．０％とする。
Ｂは液相拡散接合を達成するために必要な等温凝固を実
現するための拡散原子として、あるいは融点を被接合材
よりも低くするために必要な元素であり、それぞれの目
的のためには１．０％以上含有させることが必要である
が、本発明者らは詳細な研究によって２０．０％を超え
て含有させると、被接合材がＭｏ，Ｃｒを含有する場合
には接合部近傍のＭｏ，Ｃｒ含有合金側に粗大な硼化物
が生成し、接合部強度が低下するので、１．０〜２０．
０％とした。(2) B is 1.0 to 20.0%. B is an element necessary as a diffusion atom for achieving the isothermal solidification necessary for achieving liquid phase diffusion bonding or for lowering the melting point of the material to be bonded, and for each purpose, 1 It is necessary to contain 0.0% or more. However, the inventors of the present invention have conducted a detailed study to make the content of 20.0% or more. Coarse borides are formed on the side of the alloy containing Mo and Cr, and the strength of the joint decreases, so 1.0 to 20.
It was set to 0%.
【００２０】（３）Ｓｉは１．０〜１４．６９％とす
る。
Ｓｉは、融点を降下させための有効元素であり、Ｖを多
く含有することにより融点が比較的高くなって接合時間
が長くなることを防止する。１．０％未満ではその効果
は軽微である。１４．６９％超では、酸化雰囲気中での
液相拡散接合の際にインサートメタル中にＳｉを含む粗
大な酸化物を生成し、接合部強度および靱性を劣化させ
る。(3) Si is 1.0 to 14.69 %. Si is an effective element for lowering the melting point, and by containing a large amount of V, the melting point is prevented from becoming relatively high and the joining time becomes long. If it is less than 1.0%, the effect is slight. If it exceeds 14.69 %, a coarse oxide containing Si is generated in the insert metal during liquid phase diffusion bonding in an oxidizing atmosphere, and the joint strength and toughness are deteriorated.
【００２１】（４）Ｖは、０．１〜２０．０％する。
Ｖは、被接合材表面の酸化被膜物（Ｆｅ2 Ｏ3 ）を、低
融点複合酸化物Ｖ2 Ｏ5 −Ｆｅ2 Ｏ3 （融点約８００
℃）とする。したがって、接合温度（９００〜１２００
℃）では溶融し、液相中では表面張力の差によって球状
化することにより、Ｆｅ基材料と溶融インサートメタル
との濡れを良くする。拡散原子Ｂは、このため、表面酸
化皮膜の影響をほとんど受けることなく、球状化酸化物
の間を自由に拡散し、酸化雰囲気中における液相拡散接
合を実現させる極めて重要な元素である。０．１％未満
では酸化皮膜を溶融させるに不十分であるために効果が
なく、２０．０％を超えて添加するとインサートメタル
の融点が１３００℃を超えてしまい液相拡散接合が実質
的に不可能となる。(4) V is 0.1 to 20.0%. V, the oxidation film of the welded material surfaces (Fe 2 O 3), a low-melting composite oxide V 2 O 5 -Fe 2 O 3 ( melting point about 800
℃). Therefore, the bonding temperature (900 to 1200
In the liquid phase, it is melted, and in the liquid phase, it is made spherical due to the difference in surface tension, thereby improving the wettability between the Fe-based material and the molten insert metal. Therefore, the diffusion atom B is an extremely important element that freely diffuses between the spheroidized oxides and realizes liquid phase diffusion bonding in an oxidizing atmosphere without being affected by the surface oxide film. If it is less than 0.1%, it has no effect because it is insufficient to melt the oxide film, and if it is added in excess of 20.0%, the melting point of the insert metal exceeds 1300 ° C and liquid phase diffusion bonding is substantially performed. It will be impossible.
【００２２】（５）Ｃｒは０．１〜２０．０％とする。
Ｃｒは、主として耐食性、耐酸化性を高めるためのもの
である。０．１％未満では効果が不十分であり、２０．
０％を超えると合金箔の融点が著しく上昇してしまい、
製造性を悪化させ、液相拡散接合温度を実用的な範囲を
逸脱した極めて高い温度（１３００℃以上）に高めてし
まう。(5) Cr is 0.1 to 20.0%. Cr is mainly for enhancing corrosion resistance and oxidation resistance. If it is less than 0.1%, the effect is insufficient.
If it exceeds 0%, the melting point of the alloy foil will remarkably rise,
This deteriorates the manufacturability and raises the liquid phase diffusion bonding temperature to an extremely high temperature (1300 ° C. or higher) outside the practical range.
【００２３】（６）Ｎｉは０．１〜１５．０％とする。
Ｎｉは主として耐食性、耐酸化性を高めるためのもので
あり、０．１％未満ではその効果が不十分であり、１
５．０％超では、Ｎｉ相の介在により組織の均質性を阻
害する。接合時間が長くなり、また接合部強度の低下の
原因にもなる。(6) Ni is 0.1 to 15.0%. Ni is mainly for enhancing corrosion resistance and oxidation resistance, and if it is less than 0.1%, its effect is insufficient, and 1
If it exceeds 5.0%, the homogeneity of the structure is hindered by the inclusion of the Ni phase. Bonding time becomes long and also causes a decrease in the strength of the bonded portion.
【００２４】（７）Ｃｏは０．１〜１５．０％とする。
Ｃｏは、主として耐食性、耐酸化性を高め、強度を付与
するために含有させる。０．１％未満ではその効果が不
十分であり、１５．０％超では、インサートメタル中に
粗大な金属間化合物が生成して接合部靭性を阻害する。(7) Co is 0.1 to 15.0%. Co is mainly contained in order to enhance corrosion resistance and oxidation resistance and to impart strength. If it is less than 0.1%, its effect is insufficient, and if it exceeds 15.0%, a coarse intermetallic compound is generated in the insert metal to hinder the toughness of the joint.
【００２５】（８）Ｗ、Ｎｂ、Ｔｉはそれぞれ０．１〜
１０．０％とする。
Ｗは、接合部の強度を高めるためのものである。０．１
０％未満では効果がなく、１０．０％超では樹枝状晶間
偏析に起因する粗大Ｌａｖｅｓ相析出によって材料の高
温強度がかえって低下する。Ｎｂは、炭化物、窒化物あ
るいは炭窒化物として基材中に分散する場合、靭性向上
に効果がある。０．１％未満では効果不十分であり、１
０．０％超では粗大な硼化物が生成して接合部靭性を著
しく阻害する場合がある。Ｔｉは、接合部の強度を高め
るためのものであり、炭化物、窒化物として均一分散さ
せると靭性を高める。０．１％未満では効果不十分であ
り、１０．０％超では粗大な金属間化合物が生成して接
合部靭性を著しく阻害する場合がある。(8) W, Nb and Ti are each 0.1 to 0.1
It is 10.0%. W is for increasing the strength of the joint portion. 0.1
If it is less than 0%, there is no effect, and if it exceeds 10.0%, the high temperature strength of the material is rather reduced due to the coarse Laves phase precipitation due to interdendritic segregation. Nb is effective in improving toughness when dispersed in the substrate as a carbide, a nitride or a carbonitride. If it is less than 0.1%, the effect is insufficient and 1
If it exceeds 0.0%, coarse borides may be formed to significantly impair the toughness of the joint. Ti is for increasing the strength of the joint portion, and enhances the toughness when uniformly dispersed as a carbide or a nitride. If it is less than 0.1%, the effect is insufficient, and if it exceeds 10.0%, a coarse intermetallic compound may be formed to significantly impair the toughness of the joint.
【００２６】以上の成分組成からなる本発明の液相拡散
接合用合金箔は、良好な接合部を得るために、液相拡散
接合時に均一に溶融する必要がある。不均一な組成で、
合金成分の偏析がある場合には、インサートメタルの融
点が接合部の位置によって異なることになり、均質な接
合界面が得られず良好な接合部が得なれないことにな
る。実際には不均一な組成で、合金成分の偏析があると
いうことを考慮すると、結晶構造を非晶質にすることが
好ましい。均一な組成のものが容易に得られる場合に
は、結晶構造は非晶質であることは不可欠ではない。本
発明の液相拡散接合用合金箔は、インサートメタルとし
て種々の形状で提供することが可能である。The alloy foil for liquid phase diffusion bonding of the present invention having the above component composition is required to be melted uniformly during liquid phase diffusion bonding in order to obtain a good joint. With a non-uniform composition,
If there is segregation of the alloy components, the melting point of the insert metal will differ depending on the position of the joint, so that a uniform joint interface cannot be obtained and a good joint cannot be obtained. In consideration of the fact that the alloy composition is actually non-uniform and segregation of alloy components occurs, it is preferable to make the crystal structure amorphous. It is not essential that the crystal structure be amorphous if a uniform composition is easily obtained. The liquid phase diffusion bonding alloy foil of the present invention can be provided in various shapes as insert metal.
【００２７】第一の発明乃至第四の発明の何れかの成分
を有する合金は、例えば液体急冷法によって、容易に非
晶質の合金箔として製造することができる。ここで採用
される基本的製造方法としては、合金の溶湯をノズルを
介して冷却基板状に噴出し、熱的接触によって冷却凝固
させる液体急冷法のうち、冷却基板として一個の冷却ロ
ールを用いる、簡易な単ロール法が適している。The alloy having any of the components of the first invention to the fourth invention can be easily manufactured as an amorphous alloy foil by, for example, a liquid quenching method. As a basic manufacturing method adopted here, in a liquid quenching method in which a molten alloy is jetted through a nozzle in a cooling substrate shape and is cooled and solidified by thermal contact, one cooling roll is used as a cooling substrate, A simple single roll method is suitable.
【００２８】他に、ドラムの内壁を使う遠心急冷法やエ
ンドレスタイプのベルトを使用する方法や、これらの改
良型、例えば補助ロールや、ロール表面温度制御装置を
付属させた方法、あるいは減圧下ないし、真空中または
不活性ガス中での鋳造もそれに含まれる。また、一対の
ロール間に溶湯を注入して急冷凝固させる双ロール法も
適用できる。また、合金を、真空溶解して鋳造し、得ら
れた鋳片を通常の方法で圧延、焼鈍して、合金箔の形態
で提供することも可能である。Besides, a method of using a centrifugal quenching method using the inner wall of the drum or a method of using an endless type belt, a method improved with these methods, for example, a method in which an auxiliary roll or a roll surface temperature control device is attached, or under reduced pressure or Casting in vacuum or in an inert gas is also included. Also, a twin roll method in which a molten metal is injected between a pair of rolls and rapidly solidified can be applied. It is also possible to melt the alloy in a vacuum and cast it, and then roll and anneal the obtained slab by a usual method to provide it in the form of an alloy foil.
【００２９】上記のようにして得られる合金箔の厚み
は、薄いほど接合部近傍における機械的特性の変化が少
なく、接合に要する時間も短かくできるので、液相拡散
接合に有利であるが、３．０μｍ未満の場合にはＶの絶
対量が被接合材表面の酸化皮膜を無害化するに不十分と
なり、１００．０μｍ超では液相拡散接合終了までに要
する時間が１０時間以上となってしまい、実用的でない
ことから３．０〜１００μｍの厚みとすることが好まし
い。本発明は、液相拡散接合用の合金箔に関するもので
あるが、大気中で接合が可能であることから、拡散ろう
付けの接合法に応用しても有用である。The thinner the alloy foil obtained as described above, the smaller the change in mechanical properties in the vicinity of the joint and the shorter the time required for joining, which is advantageous for liquid phase diffusion joining. insufficient to harmless an oxide film of the absolute amount of material to be joined surfaces of the V in the case of less than 3.0 [mu] m, the time required to 100.0μm ultra the liquid phase diffusion bonding ends is equal to or more than 10 hours Since it is not practical, it is preferable to set the thickness to 3.0 to 100 μm. The present invention relates to an alloy foil for liquid phase diffusion bonding, but since it can be bonded in the air, it is also useful when applied to a diffusion brazing bonding method.
【００３０】[0030]
【実施例】本発明の液相拡散接合用合金を用い、Ｆｅ基
材料を被接合材とする液相拡散接合を実施した。実施条
件と実施結果を、比較例の場合とともに表、図を用いて
以下に説明する。本発明の第一の発明乃至第三の発明の
何れかの成分組成（原子％）有する、合金約１００ｇ
を、単ロール法（冷却ロール：Ｃｕ合金製３００mm径）
にて急冷して、板幅２〜２１５mm、板厚３〜１００μｍ
の実質的に非晶質の結晶構造を有する合金箔とした。Example Using the alloy for liquid phase diffusion bonding of the present invention, liquid phase diffusion bonding was carried out using a Fe-based material as a material to be bonded. The implementation conditions and implementation results will be described below with reference to the case of the comparative example, using tables and figures. About 100 g of an alloy having the composition (atomic%) of any of the first to third inventions of the present invention
A single roll method (cooling roll: Cu alloy 300 mm diameter)
Quenching, plate width 2 to 215 mm, plate thickness 3 to 100 μm
The alloy foil having a substantially amorphous crystal structure of
【００３１】この際の冷却ロールの周速は５．０〜１
５．０ｍ／ｓの間に保持した。この実施例での本発明合
金箔の成分組成（原子％）は表１に示す通り、何れもＦ
ｅを基材としており、表１中の各成分の和と１００％と
の差がＦｅと不可避の不純物の合計濃度を意味する。At this time, the peripheral speed of the cooling roll is 5.0 to 1
It was held between 5.0 m / s. The composition (atomic%) of the alloy foil of the present invention in this example is F as shown in Table 1.
Using e as a base material, the difference between the sum of each component in Table 1 and 100% means the total concentration of Fe and inevitable impurities.
【００３２】本発明合金箔に対する比較合金箔の成分組
成（原子％）は表２に示した。本発明合金箔と同様、何
れもＦｅを基材としており、表２中の各成分の和と１０
０％との差がＦｅと不可避の不純物の合計濃度を意味す
る。表２の比較合金箔は表１の本発明合金箔の場合と全
く同様にして製造したものである。The component composition (atomic%) of the comparative alloy foil with respect to the alloy foil of the present invention is shown in Table 2. Like the alloy foil of the present invention, each of them has Fe as a base material, and the sum of each component in Table 2 and 10
The difference from 0% means the total concentration of Fe and inevitable impurities. The comparative alloy foils in Table 2 were manufactured in exactly the same manner as the alloy foils of the present invention in Table 1.
【００３３】表１のNO．１〜１９９に示される、本発明
の第一の発明乃至第四の発明を満足する合金箔（以下
「本発明インサートメタル」という）および表２のNO．
２００〜２１２に示される比較合金箔（従来型インサー
トメタルを含み、以下「比較インサートメタル」とい
う）を用いて液相拡散接合を実施した。In Table 1, NO. 1 to 199, the alloy foils satisfying the first invention to the fourth invention of the present invention (hereinafter referred to as "the insert metal of the present invention") and NO.
Liquid phase diffusion bonding was performed using the comparative alloy foils 200 to 212 (including the conventional insert metal, hereinafter referred to as "comparative insert metal").
【００３４】この実施に際しては、本発明インサートメ
タルは３〜１００μｍ厚×２０mm径、比較インサートメ
タルは７．６７〜２３４．１０μｍ厚×２０mm径の円盤
状とし、図１に示すごとく被接合材であるＦｅ基材料
（成分組成は表２に示した）からなる丸鋼（径２０mm）
と丸鋼（径２０mm）間に挟み込んだ。図１において１、
２は被接合材（丸鋼）、３は液相拡散接合用合金（イン
サートメタル）である。In this embodiment, the insert metal of the present invention has a disk shape of 3 to 100 μm thickness × 20 mm diameter, and the comparative insert metal has a disk shape of 7.67 to 234.10 μm thickness × 20 mm, and as shown in FIG. Round steel (diameter 20 mm) made of a certain Fe-based material (composition of which is shown in Table 2)
It was sandwiched between and round steel (diameter 20 mm). 1, in FIG.
Reference numeral 2 is a material to be welded (round steel), and 3 is an alloy for liquid phase diffusion bonding (insert metal).
【００３５】液相拡散接合雰囲気は大気とし、接合温度
を各合金箔の融点直上〜融点＋５０℃の範囲とし、大型
加熱炉を用いて目標温度を実質的に１０５０〜１３００
℃に設定して液相拡散接合を実施した。この際、被接合
材２とインサートメタル３を、両者の密着性を良好にす
るため、２メガパスカル（ＭＰａ）の加圧力で加圧し
た。接合時間は全て１０分とし、被接合材の強度、耐食
性、靱性を確保するために接合後の熱処理を焼き鈍し、
焼き入れ＋焼き鈍し、焼き鈍し＋焼き戻し、焼き入れ＋
焼き鈍し＋焼き戻しを適宜単独で、あるいは組み合わせ
て施した。The liquid-phase diffusion bonding atmosphere is atmospheric air, the bonding temperature is in the range from directly above the melting point of each alloy foil to the melting point + 50 ° C., and the target temperature is substantially 1050 to 1300 using a large heating furnace.
Liquid phase diffusion bonding was carried out by setting the temperature to ℃. At this time, the material to be joined 2 and the insert metal 3 were pressed with a pressure of 2 megapascals (MPa) in order to improve the adhesion between them. The joining time is all 10 minutes, and the heat treatment after joining is annealed to secure the strength, corrosion resistance, and toughness of the materials to be joined,
Quenching + annealing, annealing + tempering, quenching +
Annealing + tempering was performed appropriately alone or in combination.
【００３６】これら熱処理の間に被接合材どうしの元素
の相互拡散が進行し、接合部の均質化が進んだが本発明
インサートメタル中の析出物の生成、増加、成長は殆ど
見られなかった。次にＪＩＳＡ２号サブサイズ丸鋼引張
試験装置により接合部の健全性を調査したが、本発明イ
ンサートメタルを用いた全ての試験片で非接合面積率は
０％であった。During these heat treatments, mutual diffusion of elements between the materials to be joined proceeded and homogenization of the joined portion proceeded, but almost no formation, increase or growth of precipitates in the insert metal of the present invention was observed. Next, the soundness of the joint was examined by a JIS A No. 2 subsize round steel tensile tester, and the non-joint area ratio was 0% in all the test pieces using the insert metal of the present invention.
【００３７】更に図２に示す要領で丸鋼の軸方向から、
図３のようなＪＩＳＡ２号引張試験片を切り出し、引張
試験機を用いて常温で接合部破断相対強度を調査した。
接合部の破断強度は、被接合材の材質、板厚、および使
用環境条件等で決定されるが、本実施例においては実用
上の制限から４００ＭＰａを最低必要強度として仮に設
定し、この値以上の破断強度が得られた場合に十分な接
合が実現したと判断した。実験結果を表１、表２に併記
して示した。Further, as shown in FIG. 2, from the axial direction of the round steel,
A JIS A No. 2 tensile test piece as shown in FIG. 3 was cut out, and the relative strength at break of the joint was investigated at room temperature using a tensile tester.
The breaking strength of the joint is determined by the material of the material to be joined, the plate thickness, the operating environment conditions, etc. However, in this embodiment, 400 MPa is provisionally set as the minimum required strength due to practical limitations, and this value or more It was judged that sufficient joining was realized when the breaking strength of 1 was obtained. The experimental results are shown in Tables 1 and 2 together.
【００３８】表１に示すように、本発明合金箔を用いた
液相拡散接合によって得られた接合部は、すべて目標レ
ベルの４００ＭＰａ以上の極めて良好な接合強度を示し
た。これに対して、本発明を満足しない比較合金箔を用
いた液相拡散接合によって得られた接合部は、すべて目
標レベルの４００ＭＰａ以下の接合強度を示し、全く満
足できるものではなかった。個別の結果は後述する。図
４〜図７は、本発明の拡散接合用合金箔で規定する成分
（原子％）および厚み、接合時間と接合部破断強度｛Ｍ
Ｐａで表す｝との関係で効果を確認するためのものであ
る。As shown in Table 1, all the joints obtained by the liquid phase diffusion bonding using the alloy foil of the present invention showed a very good joint strength of the target level of 400 MPa or more. On the other hand, all the joints obtained by the liquid phase diffusion bonding using the comparative alloy foil which does not satisfy the present invention showed the joint strength of the target level of 400 MPa or less and were not completely satisfactory. The individual results will be described later. 4 to 7 show the components (atomic%) and thickness defined by the diffusion bonding alloy foil of the present invention, the bonding time, and the joint breaking strength {M.
This is for confirming the effect in relation to the expression of “Pa”.
【００３９】図４は、接合部破断強度に与えるインサー
トメタル中のＶの濃度の影響を表している。Ｖ濃度が原
子％で０．１％未満の場合には被接合材合金表面の酸化
皮膜を十分に無害化できないために、接合部破断強度が
低いが、原子％で０．１〜２０．０％の範囲では接合部
破断強度が母材（被接合材）並みあるいは母材以上とな
っており、Ｖが効果的に作用して酸化皮膜を無害化して
いる。しかしＶが原子％で２０．０％を超えるとインサ
ートメタルの融点が上昇するために接合時間が不足して
接合部破断強度が低下する。図５はＢと接合部破断強度
の関係を示した図である。Ｂが１．０％未満の場合には
インサートメタルの融点が高いために、２０．０％超の
場合には接合界面近傍に生成する硼化物のために接合部
破断強度が低下する。１．０〜２０．０％のＢの場合に
は高い接合部引張強度が得られる。FIG. 4 shows the effect of the concentration of V in the insert metal on the joint breaking strength. When the V concentration is less than 0.1% in atomic%, the oxide film on the surface of the alloy to be joined cannot be made sufficiently harmless, so the fracture strength at the joint is low, but 0.1% to 20.0 in atomic%. In the range of%, the fracture strength at the joint is equal to or higher than that of the base material (material to be joined), and V acts effectively to render the oxide film harmless. However, when V is more than 20.0% in atomic%, the melting point of the insert metal rises, so that the joining time becomes insufficient and the fracture strength at the joint decreases. FIG. 5 is a diagram showing the relationship between B and the breaking strength of the joint. When B is less than 1.0%, the melting point of the insert metal is high, and when it exceeds 20.0%, the rupture strength of the joint is lowered due to the boride generated near the joint interface. In the case of B of 1.0 to 20.0%, a high joint tensile strength can be obtained.
【００４０】図６はインサートメタルの厚みと接合破断
強度との関係を示した図である。厚みが１００μｍ以上
の箔では、接合強度が不十分であることが明らかであ
る。図７は、拡散元素としてＢを用いた場合の接合部破
断強度（ＭＰａ）と接合時間の関係を実験で求め、その
結果を拡散元素としてＰを用いた場合と比較して示した
ものである。この実験の条件は、表３、表４に示した。
図７、表３、表４から、Ｂを拡散元素とした本発明で
は、Ｐを拡散元素とした場合より接合温度は高いが、よ
り短時間で目標の接合部破断強度４００（ＭＰａ）を実
現できることが確認できる。FIG. 6 is a view showing the relationship between the thickness of the insert metal and the joint breaking strength. It is apparent that the bonding strength is insufficient for the foil having a thickness of 100 μm or more. FIG. 7 shows the relationship between the joint breaking strength (MPa) and the joining time when B is used as the diffusing element, which is experimentally obtained, and the result is shown in comparison with the case where P is used as the diffusing element. . The conditions of this experiment are shown in Tables 3 and 4.
From FIG. 7 , Table 3, and Table 4, in the present invention in which B is a diffusing element, the bonding temperature is higher than in the case where P is a diffusing element, but a target bonding fracture strength of 400 (MPa) is achieved in a shorter time. You can see that you can.
【００４１】表２は本発明合金箔に対する比較合金箔の
化学成分組成と、得られた接合部引張破断強度を示した
ものである。表２に示すように、比較合金箔NO．２００
はＢ含有量が不足したために融点が１３００℃を超え、
結果として破断強度が著しく低くなった例、NO．２０１
はＢ含有量が高く、接合部近傍の被接合合金側に粗大な
硼化物が多数生成して接合部破断強度が低下した例であ
る。Table 2 shows the chemical composition of the comparative alloy foil with respect to the alloy foil of the present invention, and the tensile rupture strength of the joints thus obtained. As shown in Table 2, the comparative alloy foil NO. 200
Has a melting point exceeding 1300 ° C due to lack of B content,
As a result, the fracture strength was remarkably lowered, NO. 201
Is an example in which the B content is high and a large number of coarse borides are generated on the side of the alloy to be joined in the vicinity of the joint, and the fracture strength at the joint is lowered.
【００４２】NO．２０２はＳｉ量が不足して融点が１３
００℃以上になり、結果として接合部破断強度が著しく
低くなった例、NO．２０３はＳｉ量が過多となって接合
時に粗大なＳｉＯ2 系酸化物がインサートメタル中に生
成して接合部破断強度が低下した例である。NO. 202 has an insufficient amount of Si and has a melting point of 13
Example where NO. 203 is an example in which the amount of Si is excessive and coarse SiO 2 -based oxide is generated in the insert metal at the time of joining to lower the fracture strength at the joint.
【００４３】NO．２０４はＶ量が不足して被接合材合金
表面に生成した酸化皮膜が十分に無害化されず接合部破
断強度が低くなった例、NO．２０５はＶ量が過多となっ
て融点が極めて高くなり、液相拡散接合が十分に行われ
ず接合部破断強度が低くなった例である。NO. No. 204 is an example in which the amount of V was insufficient and the oxide film formed on the surface of the alloy to be joined was not sufficiently rendered harmless, and the fracture strength at the joint was low. 205 is an example in which the amount of V was excessive and the melting point was extremely high, liquid phase diffusion bonding was not sufficiently performed, and the fracture strength at the joint part was low.
【００４４】NO．２０６はＣｒを多量に含有しているた
め、融点が著しく高くなって、液相拡散接合が十分に行
われず接合部破断強度が低くなった例、NO．２０７はＮ
ｉを多く含有しているため、Ｆｅ相中にＮｉ相が介在し
て組織不均一を生じ靭性を低下させ、接合部破断強度が
低くなった例である。NO. Since 206 contains a large amount of Cr, its melting point becomes extremely high and liquid phase diffusion bonding is not sufficiently performed, resulting in a low joint rupture strength. 207 is N
This is an example in which since a large amount of i is contained, the Ni phase intervenes in the Fe phase to cause non-uniformity of the structure, lower the toughness, and the fracture strength at the joint portion.
【００４５】NO．２０８はＣｏ量が過多となり、粗大な
金属間化合物が生成して靭性が低下し、接合部破断強度
が低くなった例、NO．２０９はＷ量が過多となり、粗大
な金属間化合物が生成して靭性が低下し、接合部破断強
度が低くなった例、NO．２１０はＮｂ量が過多となり、
Ｆｅ−Ｎｂ系の金属間化合物が粗大析出して脆化し接合
部破断強度が低くなった例である。NO．２１１はＴｉ量
が過多となり、粗大な金属間化合物の過剰生成により粗
大な金属間化合物が生成して靭性が低下し、接合部破断
強度が低くなった例、NO．２１２は合金箔厚みが厚過ぎ
て接合部破断強度が低くなった例である。NO. No. 208 has an excessive amount of Co, a coarse intermetallic compound is formed, the toughness is lowered, and the joint rupture strength is lowered. No. 209 is an example in which the W content is excessive, coarse intermetallic compounds are formed, the toughness is lowered, and the joint rupture strength is lowered. 210 has too much Nb,
This is an example in which a Fe—Nb-based intermetallic compound coarsely precipitates, becomes brittle, and the joint rupture strength becomes low. NO. No. 211 has an excessive amount of Ti and excessive coarse formation of a coarse intermetallic compound produces a coarse intermetallic compound to lower the toughness, resulting in a low joint rupture strength. 212 is an example in which the alloy foil thickness is too thick and the joint breaking strength is low.
【００４６】上記のように、本発明の要件を部分的に満
足するが、本発明の要件のすべては満足していない比較
インサートメタルを用いた液相拡散接合によっては、目
標の接合部破断強度４００ＭＰａを実現することができ
なかった。As described above, although the requirements of the present invention are partially satisfied, but not all of the requirements of the present invention, the target joint rupture strength may be increased depending on the liquid phase diffusion bonding using the comparative insert metal. It was not possible to realize 400 MPa.
【００４７】[0047]
【表１】 [Table 1]
【００４８】[0048]
【表２】 [Table 2]
【００４９】[0049]
【表３】 [Table 3]
【００５０】[0050]
【表４】 [Table 4]
【００５１】[0051]
【表５】 [Table 5]
【００５２】[0052]
【表６】 [Table 6]
【００５３】[0053]
【表７】 [Table 7]
【００５４】[0054]
【表８】 [Table 8]
【００５５】[0055]
【表９】 [Table 9]
【００５６】[0056]
【表１０】 [Table 10]
【００５７】[0057]
【表１１】 [Table 11]
【００５８】[0058]
【発明の効果】本発明は、各種のＦｅ基材料（厚鋼板、
鋼管、条鋼、鉄筋、棒鋼等）を接合対象として、酸化雰
囲気中での液相拡散接合を可能とし、短時間で破断強度
の高い接合部を確保することを可能にするものであり、
液相拡散接合の特長をＦｅ基材料の接合にも有効に生か
すことができ、接合施工の工期を大幅に短縮することが
可能になった。The present invention provides various Fe-based materials (thick steel plates,
Steel pipes, bar steel, reinforcing bars, steel bars, etc.) can be joined by liquid phase diffusion joining in an oxidizing atmosphere, and a joint with high breaking strength can be secured in a short time.
The advantages of liquid phase diffusion bonding can be effectively utilized for bonding Fe-based materials, and the construction period for bonding can be significantly shortened.
【図１】丸鋼接合試験片を被接合材とする、液相拡散接
合用合金箔（インサートメタル）による液相拡散接合例
を示す平面説明図。FIG. 1 is an explanatory plan view showing an example of liquid phase diffusion bonding using an alloy foil for liquid phase diffusion bonding (insert metal), which uses a round steel bonding test piece as a material to be bonded.
【図２】液相拡散接合により得られた丸鋼試験片と引張
試験片採取状態例を示す平面説明図。FIG. 2 is an explanatory plan view showing an example of collecting a round steel test piece and a tensile test piece obtained by liquid phase diffusion bonding.
【図３】引張試験片採取装置により採取された引張試験
片例を示す平面説明図。FIG. 3 is an explanatory plan view showing an example of a tensile test piece collected by a tensile test piece collecting device.
【図４】Ｆｅ基材料を被接合材とした液相拡散接合での
Ｆｅベースのインサートメタル中のＶ量と接合部破断強
度の関係を表わす説明図。FIG. 4 is an explanatory view showing the relationship between the V content in the Fe-based insert metal and the fracture strength at the joint portion in liquid phase diffusion bonding using an Fe-based material as the material to be bonded.
【図５】Ｆｅ基材料を被接合材とした液相拡散接合での
Ｆｅベースのインサートメタル中のＢ量と接合部破断強
度の関係を表わす説明図。FIG. 5 is an explanatory view showing the relationship between the amount of B in the Fe-based insert metal and the fracture strength at the joint portion in liquid-phase diffusion bonding using a Fe-based material as the material to be joined.
【図６】Ｆｅ基材料を被接合材とした液相拡散接合での
Ｆｅベースのインサートメタルの厚みと接合部破断強度
との関係を表わす説明図。FIG. 6 is an explanatory view showing the relationship between the thickness of the Fe-based insert metal and the fracture strength at the joint portion in liquid phase diffusion bonding using an Fe-based material as the material to be bonded.
【図７】Ｆｅ基材料を被接合材とした液相拡散接合での
Ｆｅベースのインサートメタルによる接合時間と接合部
引張破断強度との関係を表わす説明図で、Ｂ系インサー
トメタルを用いた場合とＰ系インサートメタルを用いた
場合を比較して示したものである。FIG. 7 is an explanatory diagram showing the relationship between the joining time by the Fe-based insert metal and the tensile fracture strength of the joint in the liquid phase diffusion bonding using the Fe-based material as the material to be joined, in the case of using the B-based insert metal. 3 shows a comparison between the case of using P-type insert metal and the case of using P-type insert metal.
１ 被接合材（丸鋼） ２ 液相拡散接合用合金箔（インサートメタル） ３ 接合済み丸鋼試験片 ４ 接合衝合線 ５ ＪＩＳＡ２号サブサイズ丸鋼引張試験片の採取位置 ６ 丸鋼の軸線方向および引張り試験片採取方向 ７ 丸鋼試験片ネジ部 ８ ＪＩＳＡ２号サブサイズ丸鋼引張試験片 ９ Ｖ溝（切欠き）の加工位置 1 Materials to be joined (round steel) 2 Alloy foil for liquid phase diffusion bonding (insert metal) 3 Bonded round steel test piece 4 junction line 5 JISA No. 2 Sub-size Round Steel Tensile Test Piece Collection Position 6 Round steel axial direction and tensile test piece sampling direction 7 Round steel test piece screw part 8 JIS A No. 2 Subsize Round Steel Tensile Test Piece 9 V groove (notch) processing position
フロントページの続き (72)発明者 尾崎 茂克 千葉県富津市新富20−１ 新日本製鐵株 式会社 技術開発本部内 (56)参考文献 特開 平２−151377（ＪＰ，Ａ) 特開 平５−15982（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B23K 20/00,35/30 Front page continuation (72) Inventor Shigekatsu Ozaki 20-1 Shintomi, Futtsu City, Chiba Nippon Steel Co., Ltd. Technology Development Division (56) Reference JP-A-2-151377 (JP, A) JP-A 5-15982 (JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) B23K 20 / 00,35 / 30
Claims (4)
散接合用合金箔であって、原子％で、 Ｂ ：１．０〜２０．０％、 Ｓｉ：１．０〜１４．６９％、 Ｖ ：０．１〜２０．０％ を含有し、残部は実質的にＦｅおよび不可避の不純物か
らなる組成を有し、厚さが３．０〜１００μｍであるこ
とを特徴とする酸化雰囲気中で接合可能な液相拡散接合
用合金箔。1. Liquid phase expansion for joining Fe-based materials together
It is an alloy foil for powder bonding, containing B: 1.0 to 20.0%, Si: 1.0 to 14.69 %, and V: 0.1 to 20.0% in atomic%, and the balance. substantially Fe and having a composition consisting of unavoidable impurities, bondable liquid phase diffusion bonding alloy foil in an oxidizing atmosphere, wherein the thickness is 3.0~100μm is.
項１記載の酸化雰囲気中で接合可能な液相拡散接合用合
金箔。2. A further atomic%, Cr: 0.1~20%, Ni : 0.1~15.0%, Co: 0.1~15.0% of one or to contain two or more Claims characterized by
Item 1. An alloy foil for liquid phase diffusion bonding, which can be bonded in an oxidizing atmosphere.
項１又は２記載の酸化雰囲気中で接合可能な液相拡散接
合用合金箔。3. Atomic% further contains one or more of W: 0.1 to 10.0%, Nb: 0.1 to 10.0%, Ti: 0.1 to 10.0%. Claims characterized by
Item 1. An alloy foil for liquid phase diffusion bonding which can be bonded in an oxidizing atmosphere according to item 1 or 2 .
ことを特徴とする請求項１〜３のいずれか１項に記載の
酸化雰囲気中で接合可能な液相拡散接合用合金箔。4. The crystal structure of the tissue is substantially amorphous.
Bondable liquid phase diffusion bonding alloy foil in an oxidizing atmosphere according to any one of claims 1-3, characterized in that.
Priority Applications (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14203896A JP3434126B2 (en) | 1996-06-04 | 1996-06-04 | Liquid phase diffusion bonding alloy foil that can be bonded in oxidizing atmosphere |
| CN97190924A CN1198116A (en) | 1996-06-04 | 1997-06-04 | Iron-base alloy foils for liquid-phase diffusion bonding of iron-base material bondable in oxidizing atmosphere |
| PCT/JP1997/001900 WO1997046347A1 (en) | 1996-06-04 | 1997-06-04 | Iron-base alloy foils for liquid-phase diffusion bonding of iron-base material bondable in oxidizing atmosphere |
| US09/011,583 US5919577A (en) | 1996-06-04 | 1997-06-04 | Fe-based alloy foil for liquid-phase diffusion bonding of Fe-based materials by enabling bonding in oxidizing atmospheres |
| EP97924317A EP0854002A1 (en) | 1996-06-04 | 1997-06-04 | Iron-base alloy foils for liquid-phase diffusion bonding of iron-base material bondable in oxidizing atmosphere |
| KR1019980700819A KR19990036151A (en) | 1996-06-04 | 1997-06-04 | Fe-based alloy foil for liquid phase diffusion bonding of Fe-based materials that can be bonded in an oxidizing atmosphere |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14203896A JP3434126B2 (en) | 1996-06-04 | 1996-06-04 | Liquid phase diffusion bonding alloy foil that can be bonded in oxidizing atmosphere |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH09323190A JPH09323190A (en) | 1997-12-16 |
| JP3434126B2 true JP3434126B2 (en) | 2003-08-04 |
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ID=15305942
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|---|---|---|---|---|
| JP4854754B2 (en) * | 2009-03-09 | 2012-01-18 | 新日本製鐵株式会社 | Liquid phase diffusion bonding method for machine parts |
| US8419869B1 (en) * | 2012-01-05 | 2013-04-16 | The Nanosteel Company, Inc. | Method of producing classes of non-stainless steels with high strength and high ductility |
| CN112496518B (en) * | 2020-11-11 | 2022-03-22 | 核工业西南物理研究院 | Diffusion bonding method of tungsten and low-activation steel |
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