JP4510515B2 - Hollow parts with excellent fatigue characteristics - Google Patents
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- 230000006698 induction Effects 0.000 claims description 20
- 229910000831 Steel Inorganic materials 0.000 claims description 18
- 239000010959 steel Substances 0.000 claims description 18
- 230000006835 compression Effects 0.000 claims description 3
- 238000007906 compression Methods 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 claims 1
- 230000000694 effects Effects 0.000 description 9
- 230000006866 deterioration Effects 0.000 description 8
- 239000002344 surface layer Substances 0.000 description 6
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000005255 carburizing Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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Description
本発明は疲労特性が要求される自動車および機械構造用の部品として用いられる疲労特性に優れる中空部品に関する。 The present invention relates to a hollow part having excellent fatigue characteristics used as a part for automobiles and mechanical structures that require fatigue characteristics.
自動車および機械構造用として使用される部品に要求される特性には疲労がある。近年、自動車等の性能向上に伴い一段と高い疲労特性が要求されるようになってきた。疲労特性向上には一般的に硬さや強度を高めることと、残留応力が圧縮であることが効果的である。部品の疲労特性向上を目的として、部品の表層部のみを焼き入れする浸炭焼き入れがある。これまでに浸炭焼き入れにより表層部の硬さや強度を高めことで疲労特性向上を図る試みがなされている。特許文献１などに見られるように合金元素の組み合わせを工夫することで表層部の硬さを高めることで疲労特性の向上を図るものである。しかし、このように製造した部品においても、近年の自動車等の性能向上に伴う高い疲労特性を安定かつ十分に確保できるものではない。 Fatigue is a characteristic required for parts used for automobiles and machine structures. In recent years, with the improvement in performance of automobiles and the like, higher fatigue characteristics have been required. In general, it is effective to increase the hardness and strength and to compress the residual stress to improve the fatigue characteristics. For the purpose of improving the fatigue characteristics of parts, there is a carburizing quenching in which only the surface layer of the part is quenched. Attempts have been made to improve the fatigue characteristics by increasing the hardness and strength of the surface layer by carburizing and quenching. As seen in Patent Document 1, the fatigue characteristics are improved by increasing the hardness of the surface layer by devising a combination of alloy elements. However, even in the parts manufactured in this way, it is not possible to ensure a stable and sufficient high fatigue characteristic due to the recent performance improvement of automobiles and the like.
自動車および機械構造用の部品には疲労特性が要求されている。本発明では電縫鋼管を冷間加工して所定の形状に成形し、高周波焼き入れ後の中空部品において、疲労特性に優れた中空部品を提供することを目的としている。 Fatigue properties are required for automotive and machine structural components. An object of the present invention is to provide a hollow part excellent in fatigue characteristics in a hollow part after induction-hardened steel pipe is cold worked and formed into a predetermined shape and induction-hardened.
本発明は以下の構成を要旨とするものである。
（１）質量％でＣ：０．２５〜０．５０％、Ｓｉ：０．３５％以下、Ｍｎ：０．６０〜１．５０％、Ｓ：０．００２５％以下、Ｐ：０．０１０％以下を含み、残部Ｆｅ及び不可避不純物である電縫鋼管を冷間加工して所定の形状に成形し、高周波焼き入れ後の中空部品の肉厚方向と周方向の全域において硬さがＨｖで５００以上で、かつ、
当該中空部品断面の外表面側と内表面側の硬さの差がＨｖ１５０以下で、更に、
当該外表面と内表面が共に残留応力が圧縮で５０ＭＰａ以上
であることを特徴とする中空部品。
（２）質量％でＣｒ：０．０５〜１．００％、Ｍｏ：０．０５〜１．００％、Ｎｉ：０．１０〜２．００％、Ｃｕ：０．１０〜２．００％、Ｔｉ：０．０１〜０．２０％、Ｂ：０．０００５〜０．００３０％以下、Ｍｇ：０．００５０％以下、Ｃａ：０．００１０〜０．０１００％のうち一種または二種以上を含む（１）記載の中空部品。
The gist of the present invention is as follows.
(1) By mass% C: 0.25 to 0.50%, Si: 0.35% or less, Mn: 0.60 to 1.50%, S: 0.0025 % or less, P: 0.010% look including the following, an electric resistance welded steel pipe is a balance of Fe and unavoidable impurities was cold worked and molded into a predetermined shape, hardness in the hollow part of the thickness direction and the circumferential direction of the entire area after the induction hardening is at Hv 500 or more , and
The difference in hardness between the outer surface side and the inner surface side of the hollow part cross section is Hv150 or less,
A hollow part, wherein both the outer surface and the inner surface have a residual stress of 50 MPa or more in compression .
(2) Cr: 0.05 to 1.00%, Mo: 0.05 to 1.00%, Ni: 0.10 to 2.00%, Cu: 0.10 to 2.00% by mass% Ti: 0.01 to 0.20%, B: 0.0005 to 0.0030% or less, Mg: 0.0050% or less, Ca: 0.0010 to 0.0100%, including one or more (1) The hollow part as described.
以上に説明した如く、この発明によれば、優れた疲労特性を有する中空部品が得られ、自動車および機械構造用部品として満足できる中空部品が提供可能となる。 As described above, according to the present invention, a hollow part having excellent fatigue characteristics can be obtained, and a hollow part that can be satisfied as an automobile and a machine structural part can be provided.
以下、本発明を詳細に説明する。 Hereinafter, the present invention will be described in detail.
本発明では化学成分、硬さおよび残留応力を特定条件下で組み合わせているが、以下各要件ごとに説明する。はじめに、化学成分の限定理由について説明する。 In the present invention, chemical components, hardness, and residual stress are combined under specific conditions. Each requirement will be described below. First, the reasons for limiting chemical components will be described.
Ｃは自動車および機械構造用部品としての強度確保及び高周波焼き入れ性を確保するために必要な元素であるが、０．２５％未満では最終製品の強度が不足し、高周波焼き入れ性も確保できない。また、０．５０％を超えるとむしろ硬くなって冷間加工性の劣化を招く。従って、Ｃは０．２５〜０．５０％とする。 C is an element necessary for securing strength and induction hardenability as parts for automobiles and mechanical structures, but if it is less than 0.25%, the strength of the final product is insufficient and induction hardenability cannot be ensured. . Moreover, when it exceeds 0.50%, it will become hard rather and will cause deterioration of cold workability. Therefore, C is 0.25 to 0.50%.
Ｓｉは固溶体強化により硬さの上昇を招き冷間加工性が劣化する。従って、Ｓｉは０．３５％以下とした。 Si causes an increase in hardness due to solid solution strengthening, and cold workability deteriorates. Therefore, Si is set to 0.35% or less.
Ｍｎは高周波焼き入れ性の確保に有効な元素であるが、０．６０％未満ではこの効果が不十分である。一方、１．５０％を超えるとむしろ硬くなって冷間加工性の劣化を招く。従って、Ｍｎは０．６０〜１．５０％とする。 Mn is an element effective for ensuring induction hardenability, but if less than 0.60%, this effect is insufficient. On the other hand, if it exceeds 1.50%, it becomes rather hard and causes deterioration of cold workability. Therefore, Mn is 0.60 to 1.50%.
ＳはＭｎと結合してＭｎＳを形成する。ＭｎＳは冷間加工において割れの発生起点となりかねない。このため、Ｓ量はできるだけ少ないことが望ましい。従って、Ｓは０．００２５％以下とする。 S combines with Mn to form MnS. MnS can be a starting point for cracks in cold working. For this reason, it is desirable that the amount of S is as small as possible. Therefore, S is made 0.0025% or less.
Ｐは鋼中に不可避的に含有される成分であるが、Ｐは鋼中で粒界偏析や中心偏析を起こし、延性劣化の原因となるので、０．０１０％以下とする。 P is a component inevitably contained in the steel, but P causes grain boundary segregation and center segregation in the steel and causes ductility deterioration, so the content is made 0.010% or less.
Ｃｒは高周波焼き入れ性の確保に有効な元素であるが、０．０５％未満ではこの効果が不十分である。一方、１．００％を超えるとむしろ硬くなって冷間加工性の劣化を招く。従って、Ｃｒは０．０５〜１．００％とする。 Cr is an effective element for ensuring high-frequency hardenability, but if it is less than 0.05%, this effect is insufficient. On the other hand, if it exceeds 1.00%, it becomes rather hard and causes deterioration of cold workability. Therefore, Cr is made 0.05 to 1.00%.
Ｍｏは高周波焼き入れ性の確保に有効な元素であるが、０．０５％未満ではこの効果が不十分である。一方、１．００％を超えるとむしろ硬くなって冷間加工性の劣化を招く。従って、Ｍｏは０．０５〜１．００％とする。 Mo is an element effective for ensuring high-frequency hardenability, but if it is less than 0.05%, this effect is insufficient. On the other hand, if it exceeds 1.00%, it becomes rather hard and causes deterioration of cold workability. Therefore, Mo is set to 0.05 to 1.00%.
Ｎｉは高周波焼き入れ性の確保に有効な元素であるが、０．１０％未満ではこの効果が不十分である。一方、２．００％を超えるとむしろ硬くなって冷間加工性の劣化を招く。従って、Ｎｉは０．１０〜２．００％とする。 Ni is an element effective for ensuring high frequency hardenability, but if less than 0.10%, this effect is insufficient. On the other hand, if it exceeds 2.00%, it becomes rather hard and causes deterioration of cold workability. Therefore, Ni is set to 0.10 to 2.00%.
Ｃｕは高周波焼き入れ性の確保に有効な元素であるが、０．１０％未満ではこの効果が不十分である。一方、２．００％を超えるとむしろ硬くなって冷間加工性の劣化を招く。従って、Ｃｕは０．１０〜２．００％とする。 Cu is an element effective for ensuring induction hardenability, but if less than 0.10%, this effect is insufficient. On the other hand, if it exceeds 2.00%, it becomes rather hard and causes deterioration of cold workability. Therefore, Cu is made 0.10 to 2.00%.
ＴｉはＮとの親和力が強いためにＢ添加した場合にＢＮの析出を防止し、固溶Ｂが確保できる。ＴｉはＢ添加する場合に必要に応じて添加するが、０．０１％未満では効果が不十分である。一方、０．２０％を超えるとＴｉＣの析出硬化が顕著となり、冷間加工性の劣化を招く。従って、Ｔｉは０．０１〜０．２０％とする。 Since Ti has a strong affinity for N, when B is added, precipitation of BN is prevented and solid solution B can be secured. Ti is added as necessary when B is added, but if less than 0.01%, the effect is insufficient. On the other hand, if it exceeds 0.20%, precipitation hardening of TiC becomes remarkable, which causes deterioration of cold workability. Therefore, Ti is set to 0.01 to 0.20%.
Ｂは高周波焼き入れ性の確保に有効な元素であるが、０．０００５％未満ではこの効果が不十分である。一方、０．００３０％を超えると粒界脆化を招く場合がある。従って、Ｂは０．０００５〜０．００３０％とする。 B is an element effective for ensuring induction hardenability, but if less than 0.0005%, this effect is insufficient. On the other hand, if it exceeds 0.0030%, grain boundary embrittlement may be caused. Therefore, B is 0.0005 to 0.0030%.
Ｍｇは脱酸元素であり、酸化物を生成する。酸化物はＭｎＳの析出核になりＭｎＳの微細均一分散に効果がある。０．００５０％を超えても歩留まりが極端に悪くなるばかりで効果は飽和する。従って、Ｍｇは０．００５０％以下とする。 Mg is a deoxidizing element and generates an oxide. The oxide becomes a precipitation nucleus of MnS and is effective in finely and uniformly dispersing MnS. Even if it exceeds 0.0050%, the yield is extremely deteriorated and the effect is saturated. Therefore, Mg is 0.0050% or less.
Ｃａは、母材および電縫溶接部の介在物の形態を調整し、冷間加工性を向上するのに有効である。Ｃａは多すぎると鋼中の介在物が増し逆に冷間加工性を劣化させる。従って、Ｃａは０．００１０〜０．０１００％とする。 Ca is effective in adjusting the form of inclusions in the base metal and the electric-welded weld and improving the cold workability. When there is too much Ca, inclusions in the steel increase and conversely the cold workability deteriorates. Therefore, Ca is 0.0010 to 0.0100%.
次に、硬さの限定理由について説明する。 Next, the reason for limiting the hardness will be described.
鋼管を冷間加工して所定の形状に成形し、高周波焼き入れが施されて、所望の特性を有する自動車および機械構造用の部品に仕上げられる。この高周波焼き入れの方法は特に規定されるものではなく、通常の方法で行えばよい。 The steel pipe is cold-worked and formed into a predetermined shape and subjected to induction hardening to finish parts for automobiles and machine structures having desired characteristics. This induction hardening method is not particularly defined, and may be performed by a normal method.
冷間加工後に高周波焼き入れした鋼材の中空部品の捩じり疲労強度は部品の硬さと相関があり、捩じり疲労強度向上には硬さを高くする必要がある。本発明の記載の化学成分を有する鋼材は通常の高周波焼き入れ後の中空部品の肉厚方向と周方向の全域において硬さがＨｖで５００以上を達成することができる。高周波焼き入れ後の中空部品の肉厚方向と周方向の全域において硬さがＨｖで５００未満であると、近年の捩じり疲労の高寿命化に対して、安定した捩じり疲労特性が得られない。従って、電縫鋼管を冷間加工して所定の形状に成形し、高周波焼き入れ後の中空部品の肉厚方向と周方向の全域において硬さがＨｖで５００以上とした。また、中空部品の高周波焼き入れにおいて、肉厚方向に対して均一に焼き入れが行われずに、内面側は焼き入れ不足により硬さが低下する場合がある。中空部品の捩じり疲労においては、硬さの低下した内面側が破壊の発生起点となりかねない。高周波焼き入れ後の中空部品の外面側と内面側の硬さの差がＨｖ１５０を超えると、従来よりも高いトルクが負荷された場合、内面側が破壊の発生起点となる可能性が非常に高く、近年の捩じり疲労の高寿命化に対して、安定した捩じり疲労特性が得られない。従って、鋼管を冷間加工して所定の形状に成形し、高周波焼き入れ後の中空部品の外面側と内面側の硬さの差がＨｖ１５０以下とした。 The torsional fatigue strength of a hollow steel part that has been induction-hardened after cold working has a correlation with the hardness of the part, and it is necessary to increase the hardness in order to improve the torsional fatigue strength. The steel material having the chemical components described in the present invention can achieve a hardness of 500 or more in Hv in the entire thickness direction and circumferential direction of the hollow part after normal induction hardening. When the hardness is less than 500 in the thickness direction and the circumferential direction of the hollow part after induction hardening, the torsional fatigue characteristic is stable for the longer life of torsional fatigue in recent years. I can't get it. Therefore, the ERW steel pipe was cold-worked and formed into a predetermined shape, and the hardness was Hv of 500 or more in the entire thickness direction and circumferential direction of the hollow part after induction hardening. Further, in the induction hardening of the hollow part, the inner surface side may be hardened due to insufficient quenching without being uniformly hardened in the thickness direction. In torsional fatigue of hollow parts, the inner surface side with reduced hardness can be the starting point of fracture. When the difference in hardness between the outer surface side and the inner surface side of the hollow part after induction hardening exceeds Hv150, when a higher torque is applied than before, the inner surface side is very likely to be a starting point of fracture, Stable torsional fatigue characteristics cannot be obtained for the longer life of torsional fatigue in recent years. Therefore, the steel pipe was cold worked and formed into a predetermined shape, and the difference in hardness between the outer surface side and the inner surface side of the hollow part after induction hardening was set to Hv 150 or less.
尚、上記断面の硬さを測定するには管軸方向に垂直の断面において内表面あるいは外表面からそれぞれ０．２ｍｍのところを測定した。 In addition, in order to measure the hardness of the said cross section, the place 0.2 mm from an inner surface or an outer surface was measured in the cross section perpendicular | vertical to a pipe-axis direction, respectively.
次に、残留応力の限定理由について説明する。 Next, the reason for limiting the residual stress will be described.
一般的に繰り返し応力を受ける部品に圧縮残留応力が存在しているときは、その部品の疲労特性は向上する。特に、中空部品の捩じり疲労においては、表面側の応力が高く表面側の残留応力が圧縮となることが必要である。また、高周波焼き入れ条件によっては、内面側の硬さの低下を招く場合があり、硬さの低下した内面側が破壊の発生起点となりかねない。中空部品の捩じり疲労の高寿命化に対しては中空部品の外表面と内表面の残留応力を圧縮にすると効果的である。中空部品の外表面と内表面の残留応力の絶対値が５０ＭＰａ未満では捩じり疲労における高寿命化の効果が発揮できない。従って、鋼管を冷間加工して所定の形状に成形し、高周波焼き入れ後の中空部品の外表面と内表面の残留応力の絶対値が５０ＭＰａ以上であり、その残留応力が圧縮とする。 In general, when a compressive residual stress exists in a part that receives repeated stress, the fatigue characteristics of the part are improved. In particular, in torsional fatigue of hollow parts, it is necessary that the stress on the surface side is high and the residual stress on the surface side is compressed. Further, depending on the induction hardening conditions, there may be a decrease in the hardness on the inner surface side, and the inner surface side with the decreased hardness may be the starting point of the fracture. To increase the life of torsional fatigue of hollow parts, it is effective to compress the residual stress on the outer surface and inner surface of the hollow part. If the absolute value of the residual stress on the outer surface and inner surface of the hollow part is less than 50 MPa, the effect of extending the life in torsional fatigue cannot be exhibited. Therefore, the steel pipe is cold worked and formed into a predetermined shape, and the absolute value of the residual stress on the outer surface and inner surface of the hollow part after induction hardening is 50 MPa or more, and the residual stress is compression.
尚、内表面及び外表面を残留応力５０ＭＰａ以上とするためには例えば（高周波誘導加熱により加熱後、直ぐに水冷する高周波焼き入れ）により製造すれば良い。 In order to make the inner surface and the outer surface have a residual stress of 50 MPa or more, for example, the inner surface and the outer surface may be manufactured by (high-frequency quenching that is heated by high-frequency induction heating and then immediately water-cooled).
表１に鋼帯を連続的に管状に成形し、この管状鋼帯のエッジ部を高周波溶接によって溶接し、その後Ａc3変態点以上に再加熱した電縫鋼管の化学成分を示す。表２に電縫鋼管を冷間加工し、高周波焼き入れ後の中空部品の硬さを示す。硬さはビッカ−ス硬度計による表面硬さを示す。荷重は９．８Ｎである。表３に電縫鋼管を冷間加工し、高周波焼き入れ後の中空部品の外表面と内表面の残留応力状態と残留応力の絶対値を示す。残留応力はＸ線により測定した。外表面は外表層から０．２ｍｍ下まで電解研磨し、その面を測定した。内表面は内表層から０．２ｍｍ上まで外表層から電解研磨し、その面を測定した。表４に本発明により製造された中空部品および比較で製造された中空部品の特性を示す。製造された中空部品は捩じり疲労試験により回転トルクを変化させて、繰り返し回数で評価した。本発発明による中空部品は優れた疲労特性を有していることがわかる。 Table 1 was formed into a continuous tubular steel strip, the edge portions of the tubular steel strip was welded by high frequency welding, showing a subsequent A c3 chemical components of the re-heated electric resistance welded steel pipe transformation point or higher. Table 2 shows the hardness of the hollow parts after cold working the ERW steel pipe and induction hardening. Hardness indicates the surface hardness measured by a Vickers hardness tester. The load is 9.8N. Table 3 shows the residual stress state and the absolute value of the residual stress on the outer and inner surfaces of the hollow part after cold-working the ERW steel pipe and induction hardening. Residual stress was measured by X-ray. The outer surface was electropolished to 0.2 mm below the outer surface layer, and the surface was measured. The inner surface was electropolished from the outer surface layer up to 0.2 mm above the inner surface layer, and the surface was measured. Table 4 shows the characteristics of the hollow parts manufactured according to the present invention and the comparatively manufactured hollow parts. The manufactured hollow parts were evaluated by the number of repetitions by changing the rotational torque by a torsional fatigue test. It can be seen that the hollow part according to the present invention has excellent fatigue properties.
Claims (2)
当該中空部品断面の外表面側と内表面側の硬さの差がＨｖ１５０以下で、更に、
当該外表面と内表面が共に残留応力が圧縮で５０ＭＰａ以上
であることを特徴とする疲労特性に優れた中空部品。 Steel component in mass%: C: 0.25 to 0.50%, Si: 0.35% or less, Mn: 0.60 to 1.50%, S: 0.0025 % or less, P: 0.010% look including the following, an electric resistance welded steel pipe is a balance of Fe and unavoidable impurities was cold worked and molded into a predetermined shape, a hollow part after induction hardening, the hardness in the vertical cross section throughout in the axial direction of the tube Hv is 500 or more , and
The difference in hardness between the outer surface side and the inner surface side of the hollow part cross section is Hv150 or less,
A hollow part excellent in fatigue characteristics, characterized in that the residual stress is 50 MPa or more in compression on both the outer surface and the inner surface .
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| HUE040155T2 (en) * | 2012-05-25 | 2019-02-28 | Nippon Steel & Sumitomo Metal Corp | Hollow stabilizer, and steel pipe for hollow stabilizers and method for production thereof |
| WO2014119802A1 (en) * | 2013-01-31 | 2014-08-07 | Ｊｆｅスチール株式会社 | Electric-resistance-welded steel pipe |
| EP3088553A4 (en) | 2014-02-04 | 2017-08-23 | Nippon Steel & Sumitomo Metal Corporation | Steel pipe |
| JP6287363B2 (en) * | 2014-03-06 | 2018-03-07 | 新日鐵住金株式会社 | Hollow material with excellent fatigue characteristics and method for producing the same |
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| JP2000234141A (en) * | 1999-02-10 | 2000-08-29 | Ntn Corp | Power transmission shaft |
| WO2002070767A1 (en) * | 2001-03-07 | 2002-09-12 | Nippon Steel Corporation | Electric welded steel tube for hollow stabilizer |
| JP2003193198A (en) * | 2001-12-26 | 2003-07-09 | Sumitomo Pipe & Tube Co Ltd | Electric resistance welded tube for machine structure and heat treatment method therefor |
| JP2003321713A (en) * | 2002-04-30 | 2003-11-14 | Jfe Steel Kk | Method of producing steel pipe |
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| JP2000234141A (en) * | 1999-02-10 | 2000-08-29 | Ntn Corp | Power transmission shaft |
| WO2002070767A1 (en) * | 2001-03-07 | 2002-09-12 | Nippon Steel Corporation | Electric welded steel tube for hollow stabilizer |
| JP2003193198A (en) * | 2001-12-26 | 2003-07-09 | Sumitomo Pipe & Tube Co Ltd | Electric resistance welded tube for machine structure and heat treatment method therefor |
| JP2003321713A (en) * | 2002-04-30 | 2003-11-14 | Jfe Steel Kk | Method of producing steel pipe |
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