JP5438464B2 - Dissimilar material joint - Google Patents
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- JP5438464B2 JP5438464B2 JP2009248955A JP2009248955A JP5438464B2 JP 5438464 B2 JP5438464 B2 JP 5438464B2 JP 2009248955 A JP2009248955 A JP 2009248955A JP 2009248955 A JP2009248955 A JP 2009248955A JP 5438464 B2 JP5438464 B2 JP 5438464B2
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- 239000000463 material Substances 0.000 title claims description 103
- 230000009466 transformation Effects 0.000 claims description 63
- 239000007769 metal material Substances 0.000 claims description 49
- 229910000734 martensite Inorganic materials 0.000 claims description 32
- 238000005304 joining Methods 0.000 claims description 17
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 9
- 239000010935 stainless steel Substances 0.000 claims description 7
- 229910001220 stainless steel Inorganic materials 0.000 claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 6
- 239000000919 ceramic Substances 0.000 claims description 6
- 239000010959 steel Substances 0.000 claims description 6
- 238000004881 precipitation hardening Methods 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910001240 Maraging steel Inorganic materials 0.000 claims description 3
- 239000011195 cermet Substances 0.000 claims description 3
- 230000035882 stress Effects 0.000 description 50
- 239000012071 phase Substances 0.000 description 27
- 238000010438 heat treatment Methods 0.000 description 10
- 238000005336 cracking Methods 0.000 description 9
- 238000001816 cooling Methods 0.000 description 8
- 230000008646 thermal stress Effects 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000005219 brazing Methods 0.000 description 5
- 238000004364 calculation method Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 3
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 3
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- 238000003483 aging Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000014509 gene expression Effects 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 230000002040 relaxant effect Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
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Description
本発明は、ステンレス鋼等の金属材料と、セラミックスや焼結合金等の硬質材料とを接合して構成される異材接合体に関するものであり、特に接合時の熱処理中の応力発生を抑制し、硬質材料の割れや接合界面の剥離を防止するように構成された異材接合体に関するものである。 The present invention relates to a dissimilar material joint formed by joining a metal material such as stainless steel and a hard material such as ceramics or a sintered alloy, particularly suppressing the generation of stress during heat treatment during joining, The present invention relates to a dissimilar material joined body configured to prevent cracking of a hard material and peeling of a joining interface.
耐摩耗性が要求される機械部品、例えばタービンローター、タペット等においては、耐摩耗性が求められる部位（タービンローターの場合は軸部）に、セラミックスや焼結合金等の硬質材料を適用し、それ以外の部位（タービンローターの場合はインペラ）は、金属材料からなるような異材接合体が用いられている。 In machine parts that require wear resistance, such as turbine rotors and tappets, hard materials such as ceramics and sintered alloys are applied to the parts that require wear resistance (shafts in the case of turbine rotors). Other parts (impellers in the case of a turbine rotor) use a dissimilar material joined body made of a metal material.
上記のような異材接合体においては、ステンレス鋼等の金属材料とセラミックス等の硬質材料を接合するに際しては、ろう付けや固相拡散、熱間静水圧加圧（ＨＩＰ）等の接合熱処理が行われるのが一般的である。異材接合体に用いられる材料の多くは、上記の接合熱処理後の冷却中にマルテンサイト変態を生じることが知られている。 In the above dissimilar material joined body, when joining a metal material such as stainless steel and a hard material such as ceramics, joining heat treatment such as brazing, solid phase diffusion, and hot isostatic pressing (HIP) is performed. It is common. It is known that many of the materials used for the dissimilar material bonded body cause martensitic transformation during cooling after the above-mentioned bonding heat treatment.
そして、上記のような接合に際しては、金属材料と硬質材料との熱収縮量の違いによって、両者間に熱応力が発生し、特に硬質材料側に変形や割れが生じたり、接合部が剥離する等、健全な接合部分を形成できないことがある。 When joining as described above, a thermal stress is generated between the metal material and the hard material due to the difference in thermal shrinkage between them, especially deformation or cracking occurs on the hard material side, or the joint is peeled off. In some cases, a sound joint cannot be formed.
このような問題を解決するための、これまでにも様々な技術が提案されている。例えば特許文献１には、「オーステナイト相の冷却によって所定の相変態を生じ得る第一の金属材料からなる第一の板状部材と、その温度−熱収縮率曲線が、第一の金属材料の温度−熱収縮率曲線と交差し得る第二の金属材料からなる第二の板状部材を用意し、接合に関するパラメータから反り量を予測しつつ第一の板状部材と第二の板状部材を接合する方法」が提案されている。 Various techniques for solving such problems have been proposed so far. For example, Patent Document 1 discloses that “a first plate-like member made of a first metal material capable of causing a predetermined phase transformation by cooling of an austenite phase, and a temperature-heat shrinkage rate curve of the first metal material. A second plate member made of a second metal material that can intersect the temperature-heat shrinkage rate curve is prepared, and the first plate member and the second plate member are predicted while predicting the amount of warpage from the parameters related to joining. Has been proposed.
また、特許文献２には、「少なくとも炭化タングステンを含む炭化タングステン基超硬合金から構成された第一の板状部材と、オーステナイト相の冷却によってマルテンサイト変態、ベイナイト変態、およびパーライト変態の少なくとも一つの変態を起こし得る金属体から構成された第二の板状部材を積層して接合するに際し、第一の板状部材と第二の板状部材との接合面に生じる引張り、および圧縮応力が１５００ＭＰａ以下となるように第二の板状部材を構成する金属体にいずれかの相変態を生じさせるようにする」ことが提案されている。 Patent Document 2 discloses that “at least one of a first plate-like member made of a tungsten carbide-based cemented carbide containing at least tungsten carbide and martensitic transformation, bainite transformation, and pearlite transformation by austenite phase cooling. When the second plate-shaped member composed of a metal body capable of causing one transformation is laminated and bonded, the tensile and compressive stress generated on the bonding surface between the first plate-shaped member and the second plate-shaped member is It has been proposed that any one of the phase transformations is generated in the metal body constituting the second plate member so that the pressure is 1500 MPa or less.
上記した各技術は、いずれも異材接合時の熱応力を緩和することによって、変形や割れが生じたり、接合部が剥離する等の問題を解消するものであり、それなりの効果が得られている。しかしながら、これらの技術によっても、異材接合時の熱応力を完全に緩和することができないことがあり、場合によっては上記の様な問題が生じてしまい、健全な接合部分が形成できないことがある。 Each of the above-mentioned technologies alleviates problems such as deformation and cracking, and peeling of the bonded portion by relaxing the thermal stress at the time of joining different materials, and a certain effect is obtained. . However, even with these techniques, the thermal stress at the time of bonding different materials may not be completely relieved, and in some cases, the above-described problems may occur, and a sound bonded portion may not be formed.
本発明は上記の様な事情に着目してなされたものであって、その目的は、金属材料と硬質材料を接合して異材接合体を構成するに際して、熱収縮量の違いによる両者間の熱応力を極力低減し、変形や割れが生じたり接合部が剥離する等の問題を解消し、健全な接合部分が形成できるような異材接合体を提供することにある。 The present invention has been made paying attention to the above-mentioned circumstances, and its purpose is to form a heat treatment between the two due to a difference in heat shrinkage when a metal material and a hard material are joined to form a dissimilar material joined body. An object of the present invention is to provide a dissimilar material joined body that can reduce stress as much as possible, solve problems such as deformation and cracking, and peeling of a joint, and can form a sound joint.
上記目的を達成し得た本発明の異材接合体とは、マルテンサイト変態を生じる特性を有する金属材料と、マルテンサイト変態を生じる硬質材料とを接合することによって構成される異材接合体であって、（ａ）前記金属材料は、該金属材料の相変態温度域を前記硬質材料の相変態温度に応じて設定されるように選ばれているか、または（ｂ）前記硬質材料は、該硬質材料の相変態温度域を前記金属材料の相変態温度に応じて設定されるように選ばれているものである点に要旨を有するものである。 The dissimilar material joined body of the present invention that can achieve the above-mentioned object is a dissimilar material joined body constituted by joining a metal material having a characteristic that causes martensitic transformation and a hard material that causes martensitic transformation. (A) the metal material is selected such that the phase transformation temperature range of the metal material is set according to the phase transformation temperature of the hard material, or (b) the hard material is the hard material The phase transformation temperature range is selected so as to be set according to the phase transformation temperature of the metal material.
本発明の異材接合体におけるより具体的な構成としては、温度−伸び曲線に基づいて求められる体積分率を相当体積分率としたとき、前記金属材料におけるマルテンサイト組織の相当体積分率が１０％となる温度［Ｍ１０］Mと、前記硬質材料におけるマルテンサイト組織の相当体積分率が５０％となる温度［Ｍ５０］Sが、下記（１）式の関係を満足するものが挙げられる。
０≦［Ｍ１０］M−［Ｍ５０］S …（１）
As a more specific structure in the dissimilar material joined body of the present invention, when the volume fraction obtained based on the temperature-elongation curve is an equivalent volume fraction, the equivalent volume fraction of the martensite structure in the metal material is 10 % [M10] M and the temperature [M50] S at which the equivalent volume fraction of the martensite structure in the hard material reaches 50% satisfy the relationship of the following formula (1).
0 ≦ [M10] M − [M50] S (1)
また、前記金属材料のマルテンサイト組織の相当体積分率が９０％となる温度［Ｍ９０］Mと、前記硬質材料のマルテンサイト組織の相当体積分率が１０％となる温度［Ｍ１０］Sが、下記（２）式の関係を満足することも、好ましい要件として挙げられる。
０≧［Ｍ９０］M−［Ｍ１０］S …（２）
Further, a temperature [M90] M at which the equivalent volume fraction of the martensite structure of the metal material becomes 90%, and a temperature [M10] S at which the equivalent volume fraction of the martensite structure of the hard material becomes 10%, Satisfying the relationship of the following formula (2) is also mentioned as a preferable requirement.
0 ≧ [M90] M − [M10] S (2)
本発明の異材接合体において用いる前記金属材料としては、マルエージング鋼、析出硬化系ステンレス鋼、またはニッケル鋼のいずれかが例示できる。また前記硬質材料としては、セラミックス、サーメット、または超硬合金のいずれかが例示できる。 Examples of the metal material used in the dissimilar material joined body of the present invention include maraging steel, precipitation hardening stainless steel, and nickel steel. Examples of the hard material include ceramic, cermet, and cemented carbide.
本発明の異材接合体によれば、マルテンサイト変態を生じる特性を有する金属材料と、マルテンサイト変態を生じる硬質材料とを接合することによって構成される異材接合体において、両者の相変態温度域を調整することにより、熱収縮量の違いによる両者間の熱応力を極力低減し、変形や割れが生じたり接合部が剥離する等の問題を解消し、健全な接合部分が形成できるような異材接合体が実現できた。 According to the dissimilar material joined body of the present invention, in a dissimilar material joined body formed by joining a metal material having a characteristic that causes martensitic transformation and a hard material that causes martensitic transformation, the phase transformation temperature range of both is set. By adjusting, the thermal stress between the two due to the difference in heat shrinkage is reduced as much as possible, and problems such as deformation and cracking and peeling of the joint are eliminated, and a dissimilar material joint that can form a sound joint The body was realized.
本発明者らは、マルテンサイト変態を生じる特性を有する金属材料と、マルテンサイト変態を生じる硬質材料を接合して異材接合体を構成するに際して、熱収縮量の違いによる両者間の熱応力を極力低減し得るような異材接合体を目指して様々な角度から検討した。その結果、（ａ）前記金属材料は、該金属材料の相変態温度域を前記硬質材料の相変態温度に応じて設定されるように選ばれているか、または（ｂ）前記硬質材料は、該硬質材料の相変態温度域を前記金属材料の相変態温度に応じて設定されるように選ばれているものとすれば、上記目的に適う異材接合体が実現できることを見出し、本発明を完成した。以下、本発明が完成された経緯に沿って、本発明の作用効果について説明する。 The inventors of the present invention, when joining a metal material having the property of causing martensite transformation and a hard material causing martensite transformation to form a dissimilar material joined body, minimizes the thermal stress between the two due to the difference in thermal shrinkage. Aiming at a joint with dissimilar materials that can be reduced, we examined it from various angles. As a result, (a) the metal material is selected such that the phase transformation temperature range of the metal material is set according to the phase transformation temperature of the hard material, or (b) the hard material is When the phase transformation temperature range of the hard material is selected so as to be set according to the phase transformation temperature of the metal material, it has been found that a dissimilar material joined body suitable for the above-described purpose can be realized, and the present invention has been completed. . Hereinafter, the operational effects of the present invention will be described along the background of the completion of the present invention.
本発明者らは、相変態時の「変態塑性」現象に着目して、変態塑性を考慮した有限要素法による熱応力解析を実施した。図１（異材接合体の形状例を示す概略説明図）に示した形状、金属材料本体に対して硬質材料をロウ付けした異材接合体について、中央（図中、評価点Ａ）に発生する応力（最大主応力）の経時変化を求めた。 The inventors focused on the “transformation plasticity” phenomenon during phase transformation and conducted thermal stress analysis by a finite element method considering transformation plasticity. Stress generated at the center (evaluation point A in the figure) of the dissimilar material joined with a hard material brazed to the shape shown in FIG. The change with time of (maximum principal stress) was determined.
このとき、実験に用いた各材料の強度特性として、ヤング率と温度の関係の例を図２に示す。また、金属材料および硬質材料の温度と熱歪の関係（これを「温度−伸び曲線」と呼んでいる）の例を図３に示す。 FIG. 2 shows an example of the relationship between the Young's modulus and the temperature as the strength characteristics of each material used in the experiment. Further, FIG. 3 shows an example of the relationship between the temperature of metal material and hard material and thermal strain (this is called “temperature-elongation curve”).
まず、各材料のマルテンサイト組織の「相当体積分率」の定義について説明する。相変態の厳密な開始温度や終了温度を、上記のような温度−伸び曲線だけで求めることは困難なこと、および材料によっては、常温でもマルテンサイト組織１００％とならないことから、厳密な「体積分率」ではなく、熱応力への影響を評価するための「相当体積分率」という概念を採用したものである。 First, the definition of “equivalent volume fraction” of the martensitic structure of each material will be described. Since it is difficult to obtain the exact start temperature and end temperature of the phase transformation only by the temperature-elongation curve as described above, and depending on the material, the martensite structure does not become 100% even at room temperature. Instead of “fraction”, the concept of “equivalent volume fraction” for evaluating the influence on thermal stress is adopted.
常温におけるマルテンサイトの「相当体積分率」を１（１００％）とし、相当体積分率が１における温度−伸び曲線を図４（ｂ）の実線で示す。この線は、熱処理後の材料の温度−熱歪の測定で得ることができる。 The temperature-elongation curve when the “corresponding volume fraction” of martensite at room temperature is 1 (100%) and the equivalent volume fraction is 1 is shown by the solid line in FIG. This line can be obtained by measuring the temperature-thermal strain of the material after heat treatment.
尚、温度−伸び曲線は、基準となる温度Ｔ0での長さＬT0の試験片（一般的に円柱状）を加熱または冷却したときの歪と温度の関係を示したものであり、温度Ｔでの熱歪ＥTは、温度Ｔのときの長さをＬTとすると、ＥT＝（ＬT−ＬT0）／ＬT0で表されるものである（温度−伸び曲線における傾きは、線膨張係数とよばれる）。 The temperature - elongation curve, which shows the strain versus temperature when heated or cooled specimen length L T0 at a temperature T 0 as a reference (typically cylindrical), Temperature The thermal strain E T at T is represented by E T = (L T −L T0 ) / L T0, where L T is the length at temperature T (the slope in the temperature-elongation curve is Called linear expansion coefficient).
一方、相当体積分率がゼロのときの温度−熱歪の関係は、図４（ｂ）の破線で示される。変態進行中の温度−熱歪の関係は、相当体積分率の変化に応じて、図４（ａ）の実線のようになる。このとき、変態進行時の各温度Ｔにおけるマルテンサイトの相当体積分率は、図４（ａ）、（ｂ）の各線を用い、図４（ｃ）に示すように、相当体積分率＝ｂ／（ａ＋ｂ）のように定義される。 On the other hand, the relationship between temperature and thermal strain when the equivalent volume fraction is zero is indicated by a broken line in FIG. The relationship between the temperature and the thermal strain during the transformation is as shown by the solid line in FIG. 4A according to the change in the equivalent volume fraction. At this time, the equivalent volume fraction of martensite at each temperature T at the time of transformation progress is shown in FIG. 4C using the lines in FIGS. 4A and 4B. / (A + b).
「ＩＳＩＪ Ｉｎｔｅｒｎａｔｉｏｎａｌ，ｖｏｌ．４２（２００２），Ｎｏ．２，ｐｐ．２００−２００５」によれば、変態塑性歪（変態塑性歪増分）ｄεｔｒは、下記（３）式のように定義される。
ｄεｔｒ＝Ｋ×（１−ξ）ｄξ×σ …（３）
但し、ｄεｔｒ：変態塑性歪増分、Ｋ：材料ごとに決まる係数、ξはマルテンサイトの体積分率、ｄξ：マルテンサイトの体積分率の増分、σ：負荷応力の夫々を示す。
According to “ISIJ International, vol. 42 (2002), No. 2, pp. 200-2005”, transformation plastic strain (transformation plastic strain increment) dεtr is defined as the following equation (3).
dεtr = K × (1−ξ) dξ × σ (3)
Where dεtr: transformation plastic strain increment, K: coefficient determined for each material, ξ represents martensite volume fraction, dξ: martensite volume fraction increment, and σ: load stress.
計算では、硬質材料の係数Ｋを２×１０-5（１／ＭＰａ）とした。また、熱処理中の応力緩和（クリープ）を考慮し、クリープを無視できる４８０℃以下で発生する応力(最大主応力)を求めた。上記係数Ｋは材料、応力は熱処理条件によって変化するが、これらの変化は本発明の効果に何らの影響を与えるものでは無い。尚、上記係数Ｋは、応力と変態歪の関係で、５０ＭＰａ以下程度の直線部分の傾きとして求められるものである（「ＣＡＭＰ−ＩＳＩＪ ｖｏｌ．１８（２００５）−００００」）。 In the calculation, the coefficient K of the hard material was set to 2 × 10 −5 (1 / MPa). Further, in consideration of stress relaxation (creep) during the heat treatment, the stress (maximum principal stress) generated at 480 ° C. or less at which creep can be ignored was obtained. The coefficient K varies depending on the material and the stress varies depending on the heat treatment conditions, but these changes do not affect the effects of the present invention. The coefficient K is determined as the slope of the straight line portion of about 50 MPa or less due to the relationship between stress and transformation strain (“CAMP-ISIJ vol. 18 (2005) -0000”).
本発明者らは、各種異材接合体について、各接合体に発生する応力（最大主応力）と、硬質材料と金属材料の相変態温度差の関係について調査した。このとき用いた各異材接合体における硬質材料と金属材料の、夫々のマルテンサイト組織の相当体積分率が１０％となる温度（［Ｍ１０］S、［Ｍ１０］M）、マルテンサイト組織の相当体積分率が５０％となる温度（［Ｍ５０］S、［Ｍ５０］M）、マルテンサイト組織の相当体積分率が９０％となる温度（［Ｍ９０］S、［Ｍ９０］M）を、下記表１、２に示す。 The present inventors investigated the relationship between the stress (maximum principal stress) generated in each bonded body and the phase transformation temperature difference between the hard material and the metal material for various bonded bodies. The temperature ([M10] S , [M10] M ) at which the equivalent volume fraction of each martensite structure of the hard material and metal material in each dissimilar material joint used at this time becomes 10%, the equivalent volume of the martensite structure The temperature at which the fraction becomes 50% ([M50] S , [M50] M ) and the temperature at which the equivalent volume fraction of the martensite structure becomes 90% ([M90] S , [M90] M ) are shown in Table 1 below. 2 shows.
実験結果の代表例として、表１に示した接合体Ｓ０について説明する。この接合体の場合には、ろう付け接合温度からの冷却過程で、図５のような応力変化をしていた。本体に用いた金属材料の変態膨張によって、硬質材料の薄板内の引張応力が増大し、割れや剥離が発生することになる。 As a representative example of the experimental results, the joined body S0 shown in Table 1 will be described. In the case of this joined body, the stress changes as shown in FIG. 5 during the cooling process from the brazing joining temperature. Due to the transformation expansion of the metal material used for the main body, the tensile stress in the thin plate of the hard material increases, and cracking and peeling occur.
一方、接合体Ｓ１８の場合には、硬質材料の相変態温度域内で、金属材料の相変態が進んでいたため、応力変化は図６のようになっていた。金属材料の相変態が始まると、相変態時の膨張に伴って硬質材料内の引張応力が増加していくが、硬質材料も相変態中であるため、変態塑性歪が発生して引張応力が図５より減少していることが分かる。 On the other hand, in the case of the joined body S18, the phase change of the metal material was advanced within the phase transformation temperature range of the hard material, and thus the stress change was as shown in FIG. When the phase transformation of the metal material begins, the tensile stress in the hard material increases with the expansion during the phase transformation, but since the hard material is also in the phase transformation, transformation plastic strain occurs and the tensile stress is increased. It can be seen from FIG.
表１、２に示した各種接合体に発生する応力（最大主応力）と、硬質材料と金属材料の相変態温度差［（［Ｍ１０］M−［Ｍ５０］S）、または（［Ｍ９０］M−［Ｍ１０］S）］の関係をまとめると、図７および図８に示す結果が得られた。 The stress (maximum principal stress) generated in the various joined bodies shown in Tables 1 and 2 and the phase transformation temperature difference between the hard material and the metal material [([M10] M − [M50] S ), or ([M90] M -[M10] S )], the results shown in FIG. 7 and FIG. 8 were obtained.
尚、図７、８に示した割れリスク指数は、次のようにして定義されるものである。例えば、チタンカーバイド（ＴｉＣ）を含む焼結合金の場合には、引張強さより低い値である５５０ＭＰａになると、割れが発生するリスクが高くなることが、本発明者らの接合試験の結果から判明している。そこで、計算で求めた最大主応力のピーク値を５５０ＭＰａで正規化した値（最大主応力が５５０ＭＰａのときを１．００としたときの相対値）を定義して計算結果をまとめた。即ち、最大主応力が５５０ＭＰａを超えるときには、割れリスク指数の値が１．００より大きくなり、割れが生じにくくなることを意味する。 The crack risk index shown in FIGS. 7 and 8 is defined as follows. For example, in the case of a sintered alloy containing titanium carbide (TiC), it becomes clear from the results of the present inventors' joint test that the risk of cracking increases at a value lower than the tensile strength of 550 MPa. doing. Therefore, the calculation results are summarized by defining a value obtained by normalizing the peak value of the maximum main stress obtained by calculation at 550 MPa (relative value when 1.00 MPa is set when the maximum main stress is 550 MPa). That is, when the maximum principal stress exceeds 550 MPa, the value of the crack risk index is greater than 1.00, which means that cracks are less likely to occur.
計算結果を、５５０ＭＰａ以上の引張強さである、ジルコニアやアルミナを含む材料、タングステンカーバイド（ＷＣ）を含む焼結合金に適用した場合は、安全側の評価となり、同等に用いることができる。 When the calculation result is applied to a material containing zirconia or alumina and a sintered alloy containing tungsten carbide (WC), which has a tensile strength of 550 MPa or more, it becomes an evaluation on the safety side and can be used equally.
図７から、硬質材料のマルテンサイト組織の相当体積分率が５０％以下のときに、金属材料の変態がはじまって（相当体積分率１０％以上）いることを示す。即ち、下記（１）式の関係を満足するときに、その後の金属材料の変態膨張による応力の上昇を、硬質材料が変態終了するまでに生じる変態塑性の効果で低減できることが分かった。
０≦［Ｍ１０］M−［Ｍ５０］S …（１）
FIG. 7 shows that when the equivalent volume fraction of the martensite structure of the hard material is 50% or less, the transformation of the metal material starts (equivalent volume fraction of 10% or more). That is, when the relationship of the following formula (1) is satisfied, it has been found that the increase in stress due to the transformation expansion of the metal material thereafter can be reduced by the effect of transformation plasticity generated until the transformation of the hard material is completed.
0 ≦ [M10] M − [M50] S (1)
逆に、（１）式の右辺が負のとき、最大主応力のピーク値のばらつきは大きくなり、多くの組み合わせでリスクが高く（指数が１以上）なることが分かった。 Conversely, when the right side of the formula (1) is negative, the peak value of the maximum principal stress varies greatly, and it is found that the risk is high (index is 1 or more) in many combinations.
上記（１）式の関係を満足する接合体について更に検討したところ、図８に示す結果が得られた。硬質材料のマルテンサイト変態がほとんど進んでいない（即ち、硬質材料の相当体積分率が１０％以下）ときに、金属材料の変態がほぼ終了（金属材料の相当体積分率９０％以上）すれば、つまり下記（２）式の関係を満足しない場合には、硬質材料の変態塑性が起こる前に、金属材料の変態膨張による応力の上昇が大きくなってしまうことが分かった。即ち、下記（２）式の関係を満足することで、より割れ発生リスクを低くできることが判明した。
０≧［Ｍ９０］M−［Ｍ１０］S …（２）
When the joined body satisfying the relationship of the above formula (1) was further examined, the result shown in FIG. 8 was obtained. If the martensitic transformation of the hard material is hardly advanced (that is, the equivalent volume fraction of the hard material is 10% or less), the transformation of the metal material is almost completed (the equivalent volume fraction of the metal material is 90% or more). That is, when the relationship of the following formula (2) is not satisfied, it has been found that the stress increase due to the transformation expansion of the metal material becomes large before the transformation plasticity of the hard material occurs. That is, it has been found that the risk of cracking can be further reduced by satisfying the relationship of the following formula (2).
0 ≧ [M90] M − [M10] S (2)
以上の検討結果、前記（１）式の関係を満足する硬質材料と金属材料の組み合わせを選択することで、熱処理時のクラック発生を防止した、高接合強度の異材接合体を得ることができる。また前記（２）式の関係を満足させることによって、熱処理時のクラック発生リスクは更に低いものとなる。 As a result of the above examination, by selecting a combination of a hard material and a metal material that satisfies the relationship of the above formula (1), it is possible to obtain a dissimilar material bonded body with high bonding strength that prevents the occurrence of cracks during heat treatment. Further, by satisfying the relationship of the above formula (2), the risk of crack generation during heat treatment is further reduced.
本発明の異材接合体で用いられる金属部材としては、マルテンサイト変態する特性を有するものであれば、特に限定するものではなく、例えばマルエージング鋼、析出硬化系ステンレス鋼、またはニッケル鋼等が代表的なものとしてあげられるが、これらに限定されるものではない。尚、この金属材料は、通常、焼戻し、焼ならし、時効硬化等の処理が施され、夫々の処理に応じた組織（焼戻し組織、焼ならし組織、または時効硬化組織）となっている。 The metal member used in the dissimilar material joined body of the present invention is not particularly limited as long as it has martensitic transformation properties, and representative examples thereof include maraging steel, precipitation hardening stainless steel, or nickel steel. However, the present invention is not limited to these examples. This metal material is usually subjected to treatments such as tempering, normalizing, age hardening, etc., and has a structure (tempered structure, normalized structure, or age hardened structure) corresponding to each treatment.
また本発明の異材接合体で用いられる硬質材料としては、マルテンサイト変態するものであれば、特に限定するものではなく、例えばセラミックス、サーメットまたは超硬合金等が代表的なものとしてあげられるが、これらに限定するものではない。 In addition, the hard material used in the dissimilar material joined body of the present invention is not particularly limited as long as it undergoes martensitic transformation, and examples thereof include ceramics, cermet, cemented carbide and the like. It is not limited to these.
要するに、（ａ）金属材料が、該金属材料の相変態温度域を前記硬質材料の相変態温度に応じて設定されるように選ばれているか、または（ｂ）硬質材料が、該硬質材料の相変態温度域を前記金属材料の相変態温度に応じて設定されるように選ばれているものであれば良い。 In short, (a) the metal material is selected such that the phase transformation temperature range of the metal material is set according to the phase transformation temperature of the hard material, or (b) the hard material is made of the hard material. Any phase transformation temperature region may be selected as long as it is set according to the phase transformation temperature of the metal material.
尚、例えば鋼の場合、相変態温度域の調整は、成分調整することによって行うことができる（例えば、「鋼の冷却変態と熱処理」（住金テクノロジー株式会社），邦武立郎，P.１１６（１９９３））。具体的には、鋼の化学成分を下記（３）式に従って調整し、目標のマルテンサイト開始温度（Ｍｓ）とする。
Ｍｓ＝５２１−３５３×［Ｃ］−２２×［Ｓｉ］−２４×［Ｍｎ］−８×［Ｃｕ］−１７×［Ｎｉ］−１８×［Ｃｒ］−２６×［Ｍｏ］ …（３）
但し、［Ｃ］，［Ｓｉ］，［Ｍｎ］，［Ｃｕ］,［Ｎｉ］,［Ｃｒ］および［Ｍｏ］は、夫々Ｃ，Ｓｉ，Ｍｎ，Ｃｕ，Ｎｉ，ＣｒおよびＭｏの含有量（質量％）を示し、その元素を含有しない場合には、その項がないものとして計算する。
For example, in the case of steel, the phase transformation temperature range can be adjusted by adjusting the components (for example, “Cooling Transformation and Heat Treatment of Steel” (Sumikin Technology Co., Ltd.), Kunitake Tatsuro, P. 116 (1993). )). Specifically, the chemical composition of the steel is adjusted according to the following formula (3) to obtain the target martensite start temperature (Ms).
Ms = 521-353 * [C] -22 * [Si] -24 * [Mn] -8 * [Cu] -17 * [Ni] -18 * [Cr] -26 * [Mo] (3)
However, [C], [Si], [Mn], [Cu], [Ni], [Cr] and [Mo] are the contents (mass of C, Si, Mn, Cu, Ni, Cr and Mo, respectively). %), And when the element is not contained, it is calculated that the term is not present.
以下、実施例を挙げて本発明をより具体的に説明するが、本発明はもとより下記実施例によって制限を受けるものではなく、前・後記の趣旨に適合し得る範囲で適当に変更を加えて実施することも勿論可能であり、それらはいずれも本発明の技術的範囲に包含される。 EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not limited by the following examples, but may be appropriately modified within a range that can meet the purpose described above and below. Of course, it is possible to implement them, and they are all included in the technical scope of the present invention.
硬質材料Ａはチタンカーバイド焼結合金、金属材料Ｂ，Ｃは析出硬化系ステンレス（異なる２種類）からなる異材接合体の残留応力を測定して比較した。各材料の変態開始温度および前記（１）式、（２）式の適否を下記表３に、温度−熱歪の関係を図９に示す。 The hard material A was measured by comparing the residual stresses of the dissimilar material joints made of titanium carbide sintered alloy, and the metal materials B and C made of precipitation hardening stainless steel (two different types). The transformation start temperature of each material and the suitability of the equations (1) and (2) are shown in Table 3 below, and the relationship between temperature and thermal strain is shown in FIG.
どちらも、ろう付け接合し、このとき接合温度は両材料のオーステナイト化温度以上とし、常温まで炉冷した。接合体の形状は、前記図１（大型）に示した形状の他、図１０（中型）に示した形状のものも使用した。 Both were joined by brazing, and at this time, the joining temperature was set to the austenitizing temperature of both materials or more, and the furnace was cooled to room temperature. As the shape of the joined body, the shape shown in FIG. 10 (medium size) was used in addition to the shape shown in FIG. 1 (large size).
常温まで冷却した後、Ｘ線残留応力測定装置（微小部Ｘ線応力測定装置「ＣＮ２９０５Ｇ３」リガク社製）にて硬質材料表面の残留応力を測定した。残留応力の測定に当たっては、図１０に示した硬質材料Ａの中央部から長手方向（図１０の左右方向：「ｘ方向」と呼ぶ）と幅方向（図１０の上下方向：「ｙ方向」と呼ぶ）の２通りで測定した。夫々の異材接合体の残留応力（σx：ｘ方向の残留応力、σy：ｙ方向の残留応力）を、下記表４に示す。 After cooling to room temperature, the residual stress on the surface of the hard material was measured with an X-ray residual stress measurement device (micro part X-ray stress measurement device “CN2905G3” manufactured by Rigaku Corporation). In the measurement of the residual stress, the longitudinal direction (left and right direction in FIG. 10: called “x direction”) and the width direction (up and down direction in FIG. 10: “y direction”) from the center of the hard material A shown in FIG. Measured in two ways. Table 4 below shows the residual stresses (σ x : residual stress in the x direction, σ y : residual stress in the y direction) of each bonded dissimilar material.
尚、板厚表面では、厚み方向応力がゼロであるため、残留応力は二次元の問題と考えてよく、最大主応力σ1は、下記（４）式のように表される。
σ1＝（σx＋σy）／２＋{[（σx−σy）2＋４τxy 2]／２}1/2 …（４）
但し、σx：ｘ方向の残留応力、σy：ｙ方向の残留応力、４τxy：ｘｙ面の剪断応力
Since the stress in the thickness direction is zero on the surface of the plate thickness, the residual stress may be considered as a two-dimensional problem, and the maximum principal stress σ 1 is expressed by the following equation (4).
σ 1 = (σ x + σ y ) / 2 + {[(σ x −σ y ) 2 + 4τ xy 2 ] / 2} 1/2 (4)
Where σ x : residual stress in the x direction, σ y : residual stress in the y direction, 4τ xy : shear stress in the xy plane
本発明で想定する異材接合体では、剪断応力τxyは主応力に比べて無視できるほど小さいので、上記（４）式は下記（５）式のように変形できることになる。即ち、残留応力σxとσyのうち、大きいほうが最大主応力とほぼ一致するものとなる。
σ1＝{（σx＋σy）／２}＋{｜σx−σy｜／２} …（５）
In the dissimilar material joint assumed in the present invention, the shear stress τ xy is negligibly small as compared with the main stress, and thus the above equation (4) can be transformed into the following equation (5). That is, the larger one of the residual stresses σ x and σ y substantially coincides with the maximum principal stress.
σ 1 = {(σ x + σ y ) / 2} + {| σ x −σ y | / 2} (5)
硬質材料Ａを用いた場合に、一般的な析出硬化系ステンレス鋼である金属材料Ｂを用いると発生応力（残留応力）は高くなり、大型である図１の接合体では、図１１（図面代用写真）に示すような、硬質材料面に割れが発生した。また中型の接合体（図１０）の場合でも、残留応力は約４００ＭＰａ程度となっている。 When the hard material A is used and the metal material B, which is a general precipitation hardening stainless steel, is used, the generated stress (residual stress) becomes high, and the large joined body of FIG. Cracks occurred on the hard material surface as shown in the photo. Even in the case of a medium-sized joined body (FIG. 10), the residual stress is about 400 MPa.
一方、前記（１）式および（２）式の関係を満足する金属材料Ｃと硬質材料Ａとの組み合わせでは、中型の接合体に発生する残留応力は、金属材料Ｂと硬質材料Ａの組み合わせの１／２以下まで低減しており、図１に示した大型の形状のものについても割れ発生の無い良好な接合体が得られた。 On the other hand, in the combination of the metal material C and the hard material A satisfying the relationship of the expressions (1) and (2), the residual stress generated in the medium-sized joined body is the combination of the metal material B and the hard material A. It was reduced to ½ or less, and a good joined body with no cracking was obtained even for the large shape shown in FIG.
以上のように、前記（１）式や（２）式の関係を満足する材料を組み合わせて接合体を構成することによって、接合時のクラック発生の無い、高接合強度の異材接合体を得ることができることが分かる。 As described above, by forming a joined body by combining materials satisfying the relations of the above formulas (1) and (2), it is possible to obtain a dissimilar joint body with high joint strength that does not generate cracks during joining. You can see that
Claims (4)
（ａ）前記金属材料は、該金属材料の相変態温度域を前記硬質材料の相変態温度に応じて設定されるように選ばれているか、または（ｂ）前記硬質材料は、該硬質材料の相変態温度域を前記金属材料の相変態温度に応じて設定されるように選ばれているものであり、
且つ温度−伸び曲線に基づいて求められる相当体積分率を用い、前記金属材料におけるマルテンサイト組織の相当体積分率が１０％となる温度［Ｍ１０］Mと、前記硬質材料におけるマルテンサイト組織の相当体積分率が５０％となる温度［Ｍ５０］Sが、下記（１）式の関係を満足するものであることを特徴とする異材接合体。
０≦［Ｍ１０］M−［Ｍ５０］S …（１） It is a dissimilar material joined body constituted by joining a metal material having a characteristic that causes martensitic transformation and a hard material that causes martensitic transformation,
(A) The metal material is selected such that the phase transformation temperature range of the metal material is set according to the phase transformation temperature of the hard material, or (b) the hard material is made of the hard material. The phase transformation temperature range is selected to be set according to the phase transformation temperature of the metal material,
And using the equivalent volume fraction obtained based on the temperature-elongation curve, the temperature [M10] M at which the equivalent volume fraction of the martensite structure in the metal material becomes 10%, and the equivalent of the martensite structure in the hard material A dissimilar material joined body characterized in that the temperature [M50] S at which the volume fraction becomes 50% satisfies the relationship of the following formula (1).
0 ≦ [M10] M − [M50] S (1)
０≧［Ｍ９０］M−［Ｍ１０］S …（２） The temperature [M90] M at which the equivalent volume fraction of the martensite structure of the metal material is 90% and the temperature [M10] S at which the equivalent volume fraction of the martensite structure of the hard material is 10% are as follows: The dissimilar material joined body according to claim 1 , which satisfies the relationship of the formula (2).
0 ≧ [M90] M − [M10] S (2)
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