JP2006297398A - Friction-welded member having excellent fatigue resistant property, and method for improving fatigue resistant property - Google Patents
Friction-welded member having excellent fatigue resistant property, and method for improving fatigue resistant property Download PDFInfo
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Abstract
Description
本発明は、耐疲労特性に優れた摩擦圧接接合部品およびその疲労特性向上方法に関する。 The present invention relates to a friction welded part having excellent fatigue resistance and a method for improving the fatigue characteristics thereof.
プロペラシャフト等の鋼材の接合方法として、接合部材を突き合わせて、一方を高速で回転させて押しつけることにより発生する摩擦熱で、接合面間で生じる原子の拡散を利用して接合する摩擦圧接接合法が知られており、異鋼種間の接合や機械加工では加工できない部品形状の部品を作成する際に用いられている。
この摩擦圧接接合法は、例えば、特許文献1に開示されている。
As a method of joining steel materials such as propeller shafts, friction welding method is used to join by joining the joining members and rotating one of them at high speed and pressing it using the diffusion of atoms generated between the joining surfaces. Is known, and is used when creating parts with parts that cannot be machined by joining or machining between different steel types.
This friction welding method is disclosed in Patent Document 1, for example.
摩擦圧接を行う際に問題となる点は、摩擦圧接により生じるバリが切り欠き形状であるため応力集中を生じ亀裂の発生点となり易いため、接合部の疲労強度が低下するという点であった。
前述の特許文献1では、接合するパイプの内径を規定することにより、バリの形状を制御し、接合部品の疲労強度の低下を防止する方法が開示されている。
しかし、特許文献1に記載された発明では、バリ自体は存在するため、バリによる応力集中がなくならず、十分な疲労強度を確保することは困難であるという問題点があった。
In the above-mentioned Patent Document 1, a method for controlling the shape of the burr by regulating the inner diameter of the pipe to be joined and preventing the fatigue strength of the joined part from being lowered is disclosed.
However, in the invention described in Patent Document 1, since burrs themselves exist, there is a problem that stress concentration due to burrs is not lost and it is difficult to ensure sufficient fatigue strength.
本発明は、前述のような従来技術の問題点を解決することのできる、耐疲労特性に優れた摩擦圧接接合部品およびその疲労特性向上方法を提供することを目的とする。 An object of the present invention is to provide a friction welded part excellent in fatigue resistance and a method for improving the fatigue characteristics, which can solve the above-described problems of the prior art.
本発明は、前述の課題を解決するために鋭意検討の結果なされたものであり、その要旨とするところは、特許請求の範囲に記載した通りの下記内容である。
(1) 質量%で、C:0.1〜0.8%、Si:0.05〜2.5%、Mn:0.2〜3%、Al:0.005〜0.1%、N:0.001〜0.02%を含有し、残部がFeおよび不可避的不純物からなり、かつ、引張強さが600MPa以上の鋼材からなる部材を摩擦圧接接合した摩擦圧接接合部品であって、前記摩擦圧接接合部の表面における圧縮残留応力が、前記鋼材の引張強さの50〜90%であることを特徴とする、耐疲労特性に優れた摩擦圧接接合部品。
(2) 前記鋼材が、さらに、質量%で、Cr:0.1〜2%、Ni:0.1〜2%、Mo:0.1〜2%、Cu:0.1〜2%、Ti:0.003〜0.05%、V:0.05〜0.5%、Nb:0.01〜0.1%の1種または2種以上を含有することを特徴とする、上記(1)に記載の耐疲労特性に優れた摩擦圧接接合部品。
(3) 上記(1)または(2)に記載の成分組成を有する鋼材からなる部材を摩擦圧接接合した部品の接合部の表面を振動数10〜60kHz、振幅0.3〜50μmで振動する超音波振動端子で打撃して、前記接合部における段差およびバリを低減することにより該接合部における応力集中を緩和することを特徴とする、摩擦圧接接合部品の疲労特性向上方法。
The present invention has been made as a result of intensive studies in order to solve the above-mentioned problems, and the gist of the present invention is the following contents as described in the claims.
(1) In mass%, C: 0.1-0.8%, Si: 0.05-2.5%, Mn: 0.2-3%, Al: 0.005-0.1%, N : Friction welding joint component comprising 0.001 to 0.02%, the balance consisting of Fe and inevitable impurities, and a member made of steel material having a tensile strength of 600 MPa or more, which is friction welding joined, A friction welding joint part having excellent fatigue resistance, wherein the compressive residual stress on the surface of the friction welding joint is 50 to 90% of the tensile strength of the steel material.
(2) The steel material is further mass%, Cr: 0.1-2%, Ni: 0.1-2%, Mo: 0.1-2%, Cu: 0.1-2%, Ti : 0.003 to 0.05%, V: 0.05 to 0.5%, Nb: 0.01 to 0.1%, or one or more of the above (1) Friction welded parts with excellent fatigue resistance as described in).
(3) Ultra-vibrating the surface of the joint part of a component obtained by friction welding the member made of the steel material having the composition described in (1) or (2) at a frequency of 10 to 60 kHz and an amplitude of 0.3 to 50 μm. A method for improving the fatigue characteristics of a friction-welded joint, wherein the stress concentration in the joint is reduced by striking with a sonic vibration terminal to reduce steps and burrs in the joint.
本発明によれば、高能率でしかも疲労強度に優れた摩擦圧接接合部品の疲労特性向上方法および摩擦圧接接合部品を提供することができ、その結果、摩擦圧接接合法を疲労強度の要求される強度部材の接合に適用することが可能となり、摩擦圧接接合の適用範囲が拡大するなど、産業上有用な著しい効果を奏する。 According to the present invention, it is possible to provide a method for improving the fatigue characteristics of a friction welded part having high efficiency and excellent fatigue strength and a friction welded part, and as a result, the friction welded method is required to have fatigue strength. It can be applied to the joining of strength members, and there are significant industrially useful effects such as expansion of the application range of friction welding.
本発明を実施するための最良の形態について図1および図2を用いて詳細に説明する。
図1は、被接合材を摩擦圧接接合した摩擦圧接部材を例示する図であり、図1の上段(a)は側面図を示し、下段(b)はその斜視図を示す。
図1において、1および2は被接合部材、3は接合部を示す。
摩擦圧接接合では、被接合材1および2を突き合わせる際の突き合わせ部分ずれ、あるいは被接合材1および2の寸法精度の違いにより、接合後に図1に示すような数10μm程度の段差Gが発生する。
このように、接合部に段差Gがあると摩擦圧接部材に荷重がかかった時に応力集中が生じ、疲労強度が著しく低下する。
図2は、バリが生成した場合の摩擦圧接接合材を例示する側面図である。段差が1μm以下の無視できる大きさであった場合においても、バリが存在するため疲労強度が著しく低下する。
この疲労強度低下を防止するためには、接合部の段差Gを低減して応力集中部をなくすか、あるいは接合部の表面部に圧縮の残留応力を導入するかの2点の対策が考えられる。
The best mode for carrying out the present invention will be described in detail with reference to FIGS.
FIG. 1 is a diagram illustrating a friction welding member in which materials to be joined are friction-welded. An upper part (a) of FIG. 1 shows a side view and a lower part (b) shows a perspective view thereof.
In FIG. 1, 1 and 2 are members to be joined, and 3 is a joint.
In the friction welding, a stepped portion G of about several tens of μm as shown in FIG. 1 is generated after joining due to a deviation in the butt portion when the materials 1 and 2 are joined or a difference in dimensional accuracy between the materials 1 and 2 to be joined. To do.
Thus, if there is a level difference G at the joint, stress concentration occurs when a load is applied to the friction welding member, and the fatigue strength is significantly reduced.
FIG. 2 is a side view illustrating the friction welding material when burrs are generated. Even when the step is a negligible size of 1 μm or less, fatigue strength is significantly reduced due to the presence of burrs.
In order to prevent this decrease in fatigue strength, two measures are conceivable: reducing the step G of the joint portion to eliminate the stress concentration portion, or introducing compressive residual stress to the surface portion of the joint portion. .
本発明者等は、超音波振動する超音波振動端子で鋼材を打撃することにより、上記2点の対策を共に満足することが可能であることを見いだした。すなわち、接合部3の表面に大きな圧縮の残留応力を付与し、かつ応力集中部となる段差を低減しバリを除去することにより摩擦圧接接合部品の疲労強度を大幅に向上できることを見出した。
そこで、本発明は、摩擦圧接接合した部品の接合部3の表面を振動数10〜60kHz、振幅0.3〜50μmで振動する超音波振動端子で打撃して、前記接合部における段差を低減し、バリを除去することにより該接合部における応力集中を緩和することを特徴とする。
The present inventors have found that it is possible to satisfy both of the above-mentioned two measures by hitting a steel material with an ultrasonic vibration terminal that vibrates ultrasonically. That is, it has been found that the fatigue strength of the friction-welded parts can be significantly improved by applying a large compressive residual stress to the surface of the
Therefore, the present invention reduces the level difference at the joint by hitting the surface of the
図3および図4は、本発明の摩擦圧接接合部品の疲労特性向上方法の実施形態を例示する図であり、図3は段差の低減を図4はバリの除去を例示している。図3、図4は、それぞれ左側(a)が打撃処理前を示し、右側(b)が打撃処理後を示す。
図3および図4において、1および2は被接合部材、3は接合部、4はバリ、5は超音波振動端子を示す。
図3に示すように、超音波振動端子5により摩擦圧接接合の接合部3の表面を打撃することによって、接合部3の段差Gを低減することにより接合部3の応力集中がなくなるので摩擦圧接接合部品の疲労強度を大幅に向上できる。
また、図4に示すように、超音波振動端子5により摩擦圧接接合の接合部3の表面を打撃することによって、接合部3のバリをたたきつぶして除去することにより接合部3の応力集中がなくなるので摩擦圧接接合部品の疲労強度を大幅に向上できる。
段差およびバリが同時に生成している場合にも、本発明は有効である。
3 and 4 are diagrams illustrating an embodiment of the method for improving the fatigue characteristics of a friction welded part according to the present invention. FIG. 3 illustrates reduction of a step and FIG. 4 illustrates removal of a burr. In FIGS. 3 and 4, the left side (a) shows before the hitting process, and the right side (b) shows after the hitting process.
3 and 4, 1 and 2 are members to be joined, 3 is a joint, 4 is a burr, and 5 is an ultrasonic vibration terminal.
As shown in FIG. 3, by striking the surface of the
Further, as shown in FIG. 4, by hitting the surface of the
The present invention is also effective when steps and burrs are generated simultaneously.
以下に本発明の限定理由を述べる。
超音波打撃処理行う部位を摩擦圧接の接合部3の表面に限定したのは、摩擦圧接接合部品において疲労破壊が主たる問題となるのが、接合部であるからであり、特に、応力集中が生じる段差部およびバリ部等の極狭い領域に超音波打撃処理を行なうことが有効である。
超音波振動端子5の振動数を10〜60kHzと限定したのは、鋼材に与えられる圧縮の残留応力がこの領域で大きくなるからである。同様に、超音波振動するピン先端の振幅を0.3μm以上と限定したのも、これ以下の振幅では十分な圧縮残留応力を鋼材に与えることができないからである。振幅は大きいほど残留応力が増すが、50μm以上では塑性変形が大きくなり過ぎ、部品の寸法精度が低下するとともに疲労強度も低下するため、振幅の上限を50μmに限定する。
The reasons for limiting the present invention will be described below.
The reason why the portion subjected to the ultrasonic hammering treatment is limited to the surface of the friction welded
The reason why the frequency of the ultrasonic vibration terminal 5 is limited to 10 to 60 kHz is that the compressive residual stress applied to the steel material increases in this region. Similarly, the amplitude of the tip of the pin that vibrates ultrasonically is limited to 0.3 μm or more because sufficient compressive residual stress cannot be applied to the steel material with an amplitude below this. Although the residual stress increases as the amplitude increases, the plastic deformation becomes too large at 50 μm or more, and the dimensional accuracy of the parts decreases and the fatigue strength also decreases. Therefore, the upper limit of the amplitude is limited to 50 μm.
超音波振動端子5の先端の形状は問わないが、半球状、蒲鉾状、鞍状等が考えられるが本発明においては特に限定しない。ただし、半球状の先端形状では、丸棒−丸棒接合の接合部を処理する時に、凸と凸をつきあわせることになるので処理が不安定になる可能性がある。最良は、凸と凹を組み合わせることになる鞍状であるが、超音波振動端子の製造コストが高くなるので図3または図4に示すような凸状のピンが好ましい。
超音波振動端子4の先端の曲率は、大きいほど処理完了後の接合部の応力集中係数が減るが、つぶす体積が増大するために処理に時間が掛かる。このため、曲率は1mm〜20mmが望ましいが特に限定しない。ピン先端の曲率が段差より大きい時は、処理開始時にピン先端が段差の底に届かないが、処理が進むにつれ塑性変形により段差の形状が変化し、ピン先端の曲率と等しくなる。
被接合材が図1に例示したような丸棒の場合は、接合部全周にわたって打撃処理するのが望ましい。
前述の超音波振動端子により打撃処理を施す対象となる摩擦圧接接合部品を構成する鋼材成分、強度、残留応力の好ましい範囲の限定理由を以下に示す。
The shape of the tip of the ultrasonic vibration terminal 5 is not limited, but a hemispherical shape, a bowl shape, a bowl shape, and the like are conceivable, but there is no particular limitation in the present invention. However, in the case of the hemispherical tip shape, when processing the joint portion of the round bar-round bar joint, the projections and the projections are brought together, so the processing may become unstable. The best is a bowl-like shape that combines a convex and a concave, but a convex pin as shown in FIG. 3 or FIG. 4 is preferable because the manufacturing cost of the ultrasonic vibration terminal increases.
As the curvature of the tip of the
When the material to be joined is a round bar as illustrated in FIG. 1, it is desirable to perform a striking process over the entire circumference of the joint.
The reasons for limiting the preferable ranges of the steel material component, strength, and residual stress constituting the friction welded part to be subjected to the impact treatment by the ultrasonic vibration terminal described above will be described below.
<鋼材成分の限定理由>
Cは、鋼を強化するのに有効な元素であるが、0.1%未満では充分な強度が得られない。一方、過多に添加すると靭性が低下するため、添加量の上限を0.8%とする。
Siは、鋼の強化元素として有効であるが、0.05%未満ではその効果がない。一方、過多に添加すると靭性および被削性が低下するため、添加量の上限を2.5%とする。
Mnは、鋼の強化に有効な元素であるが、0.2%未満では充分な効果が得られない。一方、過多に添加すると靭性および被削性が低下するため、添加量の上限を3%とする。
Alは、鋼の脱酸および結晶粒の微細化のために有効な元素であるが、0.005%未満ではその効果がない。一方、過多に添加すると被削性が低下するため、添加量の上限を0.1%とする。
Nは、V炭窒化物やNb炭窒化物を生成し析出強化のために必要な元素であるが、0.001%未満では充分な効果が得られない。一方、過多に添加すると靭性が劣化するため、添加量の上限を0.02%とする。
<Reason for limiting steel components>
C is an element effective for strengthening steel, but if it is less than 0.1%, sufficient strength cannot be obtained. On the other hand, if added excessively, toughness decreases, so the upper limit of the amount added is 0.8%.
Si is effective as a steel strengthening element, but less than 0.05% has no effect. On the other hand, if added in excess, the toughness and machinability deteriorate, so the upper limit of the amount added is 2.5%.
Mn is an element effective for strengthening steel, but if it is less than 0.2%, a sufficient effect cannot be obtained. On the other hand, if added in excess, the toughness and machinability deteriorate, so the upper limit of the amount added is 3%.
Al is an element effective for deoxidation of steel and refinement of crystal grains, but if it is less than 0.005%, there is no effect. On the other hand, if added in excess, the machinability decreases, so the upper limit of the amount added is 0.1%.
N is an element required for precipitation strengthening by generating V carbonitride or Nb carbonitride, but if it is less than 0.001%, a sufficient effect cannot be obtained. On the other hand, if added excessively, the toughness deteriorates, so the upper limit of the amount added is 0.02%.
Cr,Ni,Mo,Cuはいずれも適量の添加においては靱性を損なうことなく強度を増大する元素である。Cr,Ni,Mo,Cuは、いずれも0.1%未満ではその効果はなく、2%を越えると靱性が大きく劣化するため、その添加量の下限をそれぞれ0.1%、上限を2%とする。
Tiは,窒化物・炭化物を生成し、析出強化により強度が上昇するため有効な元素である。さらにTiの窒化物は高温まで固溶せずに残るため、加熱時のオーステナイト粗大化を防止するのに有効である。0.003%未満ではこれらの効果は現れず、0.05%を越えると靱性が劣化するため、その添加量の下限を0.003%、上限を0.05%とする。
Vも、Ti同様窒化物・炭化物を生成し、析出強化により強度が上昇するため有効な元素であるが、効果を享受するためには0.05%以上の添加が必要である。一方、過多に添加すると靭性が劣化するため、添加量の上限を0.5%とする。
Cr, Ni, Mo, and Cu are all elements that increase strength without impairing toughness when added in appropriate amounts. Cr, Ni, Mo and Cu are all less than 0.1%, and there is no effect, and if over 2%, the toughness is greatly deteriorated. Therefore, the lower limit of the addition amount is 0.1% and the upper limit is 2%. And
Ti is an effective element because it produces nitrides and carbides and increases the strength by precipitation strengthening. Furthermore, since the Ti nitride remains without dissolving at high temperatures, it is effective in preventing austenite coarsening during heating. If the content is less than 0.003%, these effects do not appear. If the content exceeds 0.05%, the toughness deteriorates, so the lower limit of the amount added is 0.003% and the upper limit is 0.05%.
V is also an effective element because it produces nitrides and carbides as well as Ti, and the strength is increased by precipitation strengthening. However, in order to enjoy the effect, addition of 0.05% or more is necessary. On the other hand, if added excessively, the toughness deteriorates, so the upper limit of the amount added is 0.5%.
Nbも、Ti同様窒化物・炭化物を生成し、析出強化により強度が上昇するため有効な元素であるが、効果を享受するためには0.01%未満では充分な効果が得られない。一方、過多に添加すると靭性が劣化するため、添加量の上限を0.1%とする。
また、これらの元素以外にも、被削性を向上させる元素として、Pb、S、Bi等を添加してもよく、その場合も本発明に含まれる。
なお、上記の元素以外に、P、S等の不可避的不純物が含まれるが、その場合も本発明に含まれる。
Nb is also an effective element because it produces nitrides and carbides as well as Ti, and the strength is increased by precipitation strengthening. However, if it is less than 0.01%, sufficient effects cannot be obtained in order to enjoy the effect. On the other hand, if added excessively, toughness deteriorates, so the upper limit of the amount added is 0.1%.
In addition to these elements, Pb, S, Bi and the like may be added as elements for improving machinability, and such cases are also included in the present invention.
In addition to the above elements, unavoidable impurities such as P and S are included, but such cases are also included in the present invention.
<引張強度>
本発明の摩擦圧接接合部品を構成する鋼材の引張強さの限定理由を以下に示す。
引張強さが600MPa以下の鋼材では、接合部の圧縮残留応力の下限規定である50%では十分な疲労強度向上効果が得られないため、その下限値を600MPaとした。
<残留応力>
本発明の摩擦圧接接合部品を構成する鋼材の接合部における残留応力の限定理由を以下に示す。
600MPa以上の強度を持つ鋼材において、引張強さの50%以下の圧縮残留応力では十分な疲労強度向上が認められないことおよび、引張強さの90%以上の圧縮残留応力を付与することは、本発明では困難であることから、その上限を90%とした。
<Tensile strength>
The reasons for limiting the tensile strength of the steel materials constituting the friction welded parts of the present invention will be described below.
In steel materials having a tensile strength of 600 MPa or less, a sufficient fatigue strength improvement effect cannot be obtained at 50%, which is the lower limit of the compressive residual stress of the joint, so the lower limit was set to 600 MPa.
<Residual stress>
The reason for limiting the residual stress in the joint portion of the steel material constituting the friction welding component of the present invention will be described below.
In a steel material having a strength of 600 MPa or more, a sufficient fatigue strength improvement cannot be observed with a compressive residual stress of 50% or less of the tensile strength, and imparting a compressive residual stress of 90% or more of the tensile strength, Since this is difficult in the present invention, the upper limit was made 90%.
表1に示す成分の鋼から、小野式回転曲げ試験片(JIS Z 2274、1号試験片、記号1−6)を切り出し、1/2L位置で切断した。切断面を鏡面研磨し、窒素雰囲気、面圧10MPa、一方の試験片を2000rpmで回転し10秒保持で接合した。試験片の接合部には70μmから150μmの段差および20〜100μmのバリが生じていた。
この試験片に本発明の超音波処理を施したもの、および無処理ないしは範囲外処理を施した比較材を用意し、小野式回転曲げ疲労試験を行ない疲労強度を求めた。表2に示す。表2中の残留応力測定値は、疲労試験を行っていない試験片を別途用意し接合部表層の残留応力を測定したものである。なお、残留応力の測定はX線を用いて行ない、回折X線の強度を測定しピーク強度の半値幅から求めている。
また、表2における段差Gは、試験片を周方向に均等に分割した5点における段差を測定したうちの最大値を示す。
超音波打撃処理無しの試料は、引張強度の1/4弱の疲労強度しか得られていない。これは、摩擦圧接接合近傍の残留応力が引張の残留応力であることと、および、摩擦圧接接合により生じた段差およびバリが疲労強度を低下させていることが原因である。適正な超音波打撃処理を行うことにより、段差およびバリをなくし、圧縮の残留応力を導入することにより、引張強度の約半分の疲労強度を得ることが可能となっている。
以上のことから、本発明は比較材に比べ、大幅な疲労強度向上が認めら、有効であることが判明した。
A specimen subjected to the ultrasonic treatment of the present invention and a comparative material subjected to no treatment or out-of-range treatment were prepared for this test piece, and an Ono-type rotary bending fatigue test was conducted to determine the fatigue strength. It shows in Table 2. The residual stress measurement values in Table 2 are obtained by separately preparing a test piece that has not been subjected to a fatigue test and measuring the residual stress of the joint surface layer. The residual stress is measured using X-rays, and the intensity of diffracted X-rays is measured and obtained from the half-value width of the peak intensity.
Further, the step G in Table 2 indicates the maximum value among the measured steps at five points obtained by equally dividing the test piece in the circumferential direction.
The sample without ultrasonic impact treatment has only obtained a fatigue strength that is less than ¼ of the tensile strength. This is because the residual stress in the vicinity of the friction welding joint is a tensile residual stress, and the steps and burrs generated by the friction welding joint reduce the fatigue strength. By performing an appropriate ultrasonic striking treatment, it is possible to eliminate steps and burrs and introduce a compressive residual stress to obtain a fatigue strength of about half the tensile strength.
From the above, it has been found that the present invention is effective when a significant improvement in fatigue strength is observed as compared with the comparative material.
1、2 被接合部材
3 接合部
4 バリ
5 超音波振動端子
G 接合部の段差
1, 2 To-
Claims (3)
C :0.1〜0.8%、
Si:0.05〜2.5%、
Mn:0.2〜3%、
Al:0.005〜0.1%、
N :0.001〜0.02%
を含有し、残部がFeおよび不可避的不純物からなり、かつ、引張強さが600MPa以上の鋼材からなる部材を摩擦圧接接合した摩擦圧接接合部品であって、前記摩擦圧接接合部の表面における圧縮残留応力が、前記鋼材の引張強さの50〜90%であることを特徴とする、耐疲労特性に優れた摩擦圧接接合部品。 % By mass
C: 0.1-0.8%
Si: 0.05 to 2.5%,
Mn: 0.2-3%,
Al: 0.005 to 0.1%,
N: 0.001 to 0.02%
A friction welding joint part obtained by friction welding welding a member made of a steel material having a balance of Fe and inevitable impurities and having a tensile strength of 600 MPa or more, and compressive residual on the surface of the friction welding joint A friction welding component having excellent fatigue resistance, wherein the stress is 50 to 90% of the tensile strength of the steel material.
Cr:0.1〜2%、
Ni:0.1〜2%、
Mo:0.1〜2%、
Cu:0.1〜2%、
Ti:0.003〜0.05%、
V :0.05〜0.5%、
Nb:0.01〜0.1%
の1種または2種以上を含有することを特徴とする、請求項1に記載の耐疲労特性に優れた摩擦圧接接合部品。 The steel material is further in mass%,
Cr: 0.1 to 2%,
Ni: 0.1 to 2%,
Mo: 0.1 to 2%,
Cu: 0.1 to 2%,
Ti: 0.003 to 0.05%,
V: 0.05-0.5%
Nb: 0.01 to 0.1%
The friction-welded part having excellent fatigue resistance according to claim 1, comprising one or more of the following.
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CN106493467B (en) * | 2016-12-26 | 2018-11-30 | 重庆派馨特机电有限公司 | A kind of stirring-head thermal fatigue resistance material |
WO2021033647A1 (en) | 2019-08-20 | 2021-02-25 | 日本製鉄株式会社 | Coupling joint, automobile member, and method for manufacturing coupling joint |
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