JP2006045592A - Steel material excellent in fatigue characteristic and producing method therefor - Google Patents
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Abstract
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本発明は自動車の補強部材や足周り部材等に使用される疲労特性に優れた鋼材およびその製造方法に関する。 The present invention relates to a steel material excellent in fatigue characteristics used for a reinforcing member, a foot circumference member, and the like of an automobile, and a manufacturing method thereof.
近年、自動車の軽量化は足周りのような疲労部材にも求められている。疲労特性は母材強度に応じて向上するが、高強度鋼材は成形性が低下するため、設計限界が低い。そこで、低強度材を加熱して焼き入れる技術が改めて注目されている。例えば、特許文献1には鋼板にZnなどの合金を被覆し、加熱した後型打ちと同時に焼き入れる方法、あるいは冷間加工後に焼き入れる方法などが記載されている。これらの方法によれば、鋼材全体の強度を上昇させるため、疲労特性も向上すると考えられる。
In recent years, a reduction in weight of automobiles has been demanded for fatigue members such as legs. Fatigue properties are improved according to the strength of the base material, but the design limit of low-strength steel is low because formability is reduced. Therefore, attention is paid to the technique of heating and quenching low-strength materials. For example,
しかし、型打ちと同時に焼き入れるためには、金型に特別な冷却構造が必要であり、大幅なコストアップになる。また、鋼管を液圧バルジ成形する場合、成形水の沸点以下の温度で成形する必要があり、型打ちと同時に焼き入れることは実質的に不可能である。
また、冷間加工後に焼き入れを行う場合、曲げが厳しい部位に表面欠陥を生じることがある。疲労部材では、これらの表面欠陥から疲労が進展するため、焼き入れによる強度上昇から期待されるほどの疲労特性が得られない問題があった。
However, in order to quench at the same time as stamping, a special cooling structure is required for the mold, which greatly increases the cost. Further, when forming a steel pipe by hydraulic bulge forming, it is necessary to form the steel pipe at a temperature below the boiling point of the forming water, and it is practically impossible to quench the mold at the same time as stamping.
In addition, when quenching is performed after cold working, surface defects may occur in parts that are severely bent. In the fatigue member, fatigue progresses from these surface defects, and thus there is a problem that the fatigue characteristics as expected from the strength increase due to quenching cannot be obtained.
疲労特性は鋼材の表面状態に強く依存することはよく知られている。例えば非特許文献2に記載されているように、浸炭処理や窒化処理は鋼材の表層硬さを高めて疲労特性を大きく改善する。しかし、これらの技術も厳密な炉の雰囲気管理が必要であり、設備費が高いため、適用範囲は限られていた。
本発明は上記の問題点を解決し、冷間加工後に焼き入れる疲労特性に優れた鋼材の製造方法およびこの方法により得られた疲労特性に優れた鋼材を提供するためになされたものである。 The present invention has been made to solve the above-mentioned problems and to provide a method for producing a steel material having excellent fatigue characteristics that are quenched after cold working and a steel material having excellent fatigue characteristics obtained by this method.
上記課題を解決するためになされた本発明は、
(1)10g/m2以上の亜鉛メッキを施した鋼板または鋼管を曲率半径が板厚の5倍以下の曲げ部を有する形状に成形した後、800 ℃以上1000℃以下の温度に加熱後急冷して、表面の鉄亜鉛合金層直下の鋼に炭素濃化層を形成する、疲労特性に優れた鋼材の製造方法、
(2)鋼板または鋼管を曲率半径が板厚の5倍以下の曲げ部を有する形状に成形した後、鋼材の一部または全面に亜鉛が10g/m2以上付着するように亜鉛粉末含有塗料を塗布した後、800 ℃以上1000℃以下の温度に加熱後急冷して、表面の鉄亜鉛合金層直下の鋼に炭素濃化層を形成する、疲労特性に優れた鋼材の製造方法、
(3)曲率半径が板厚の5倍以下の曲げ部を有し、表面の鉄亜鉛合金層と鋼との界面から鋼の内面に向かって50μmまでの炭素濃度のピークが、鋼の平均炭素含有濃度の1.3 倍以上であることを特徴とする、疲労特性に優れた鋼材、
である。
The present invention made to solve the above problems
(1) Zinc-plated steel plate or steel pipe of 10g / m 2 or more is formed into a shape with a bent part whose radius of curvature is 5 times or less of the plate thickness, and then heated to a temperature of 800 ° C or higher and 1000 ° C or lower and then rapidly cooled. A method for producing a steel material with excellent fatigue properties, which forms a carbon enriched layer on the steel immediately below the iron-zinc alloy layer on the surface,
(2) After forming a steel sheet or steel pipe into a shape with a bent part with a radius of curvature of 5 times or less of the plate thickness, a paint containing zinc powder is applied so that 10 g / m 2 or more of zinc adheres to part or the entire surface of the steel material. After applying, heating to a temperature of 800 ° C or more and 1000 ° C or less and then rapidly cooling to form a carbon concentrated layer on the steel immediately below the iron-zinc alloy layer on the surface, a method for producing a steel material with excellent fatigue properties,
(3) It has a bent portion whose radius of curvature is less than 5 times the plate thickness, and the peak of the carbon concentration from the interface between the iron-zinc alloy layer on the surface and the steel to the inner surface of the steel is up to 50 μm. A steel material with excellent fatigue characteristics, characterized by being at least 1.3 times the content concentration,
It is.
本発明によれば、疲労特性に優れた鋼材を安価に提供することができるようになり、自動車、産業機械の軽量化、安全性向上を押し進めることに大きく貢献でき、産業上の寄与は大きい。 According to the present invention, a steel material having excellent fatigue characteristics can be provided at a low cost, which can greatly contribute to the promotion of weight reduction and safety improvement of automobiles and industrial machines, and the industrial contribution is great.
本発明者らは、疲労特性の優れた鋼材を得るためには、浸炭のように表面近傍の硬度を上げればよいことに着目し、検討を重ねた結果、表面に亜鉛をメッキした鋼を焼き入れると、最表面は母材中心より柔らかいにも関わらず、疲労特性が改善されることを見出した。焼き入れた鋼材の断面を詳細に観察すると、表層は柔らかい鉄亜鉛合金層であるが、鉄亜鉛合金層直下の鋼材の硬さが、鋼材の炭素濃度から推定された硬さに比べて大きく上昇していることがわかった。これは800 ℃以上に鋼材が加熱されると、表面の亜鉛が鋼材内面に向かって拡散するが、亜鉛は強力なフェライト安定化元素であるため、鋼材表面に柔らかいフェライト相を生成し、その内面側に隣接するオーステナイト相中に炭素が排出されて炭素の濃化層を形成し、その後の急冷によって生じるマルテンサイトの硬さも炭素の濃化に応じて高くなるためと考えられた。 In order to obtain a steel material with excellent fatigue characteristics, the present inventors have focused on increasing the hardness in the vicinity of the surface like carburizing. As a result of repeated studies, the inventors have baked steel with zinc plated on the surface. It was found that the fatigue characteristics were improved even though the outermost surface was softer than the center of the base metal. When the cross section of the hardened steel material is observed in detail, the surface layer is a soft iron-zinc alloy layer, but the hardness of the steel material directly below the iron-zinc alloy layer is greatly increased compared to the hardness estimated from the carbon concentration of the steel material I found out. This is because when the steel is heated to 800 ° C or higher, the surface zinc diffuses toward the inner surface of the steel, but since zinc is a strong ferrite stabilizing element, a soft ferrite phase is generated on the surface of the steel, and the inner surface It was thought that carbon was discharged into the austenite phase adjacent to the side to form a concentrated layer of carbon, and the hardness of martensite generated by the subsequent rapid cooling increased with the concentration of carbon.
さらに、くの字状に曲げた試験片で繰り返し曲げ疲労試験を行った結果、亜鉛メッキを施した後に焼き入れた場合、亜鉛メッキのない鋼材を焼き入れた場合に比べて、疲労特性が大幅に向上することを見出した。これは板厚の5倍以下の曲率半径を有する曲げ成形では、鋼材表層に数μmから数十μmの欠陥が生じて疲労強度を低下させるが、表面に亜鉛が存在すると、焼き入れのための加熱中に鉄亜鉛合金層が鋼材内面に進展して新たに平滑な界面を生成するため、曲げ成形で生じた欠陥を実質的に無害化する効果と、前述した炭素の濃化層の効果が重畳して発揮されるためと考えられた。板厚の5倍を超える曲げ成形では欠陥は生じにくいため、効果が小さい。 Furthermore, as a result of repeated bending fatigue tests with test pieces bent in a square shape, the fatigue characteristics are significantly greater when quenched after galvanizing than when steel without galvanizing is quenched. Found to improve. This is because bending with a curvature radius of 5 times the plate thickness or less causes defects of several μm to several tens of μm in the steel surface layer and reduces fatigue strength. However, if zinc is present on the surface, During heating, the iron-zinc alloy layer progresses to the inner surface of the steel material and creates a new smooth interface. This was thought to be due to being superimposed. Defects are less likely to occur in bending molding exceeding 5 times the plate thickness, so the effect is small.
なお、上記の現象は亜鉛が十分に付着していることが必要であり、亜鉛の付着量が10g/m2未満では表面の欠陥を改善するだけの鉄亜鉛合金層の進展が見られない。また、加熱温度は800 ℃未満では鋼の変態点を超えないだけでなく、鉄亜鉛固溶体が十分に成長しないが、1000℃を超えると加熱設備の付帯コストが増加するため、800 ℃以上1000℃以下とする。 Note that the above phenomenon requires that zinc is sufficiently adhered, and if the amount of zinc deposited is less than 10 g / m 2 , the progress of the iron-zinc alloy layer that only improves surface defects is not observed. Also, if the heating temperature is less than 800 ° C, not only does the steel transformation point not be exceeded, but the iron-zinc solid solution does not grow sufficiently, but if it exceeds 1000 ° C, the incidental costs of the heating equipment increase, so 800 ° C or more and 1000 ° C The following.
従って、10g/m2以上の亜鉛メッキを施した鋼板または鋼管を曲率半径が板厚の5倍以下の曲げ部を有する形状に成形した後に、800 ℃以上1000℃以下の温度に加熱後急冷して、表面の鉄亜鉛合金層直下の鋼に炭素濃化層を形成するか、鋼板または鋼管を曲率半径が板厚の5倍以下の曲げ部を有する形状に成形した後に、鋼材の一部または全面に亜鉛が10g/m2以上付着するように亜鉛粉末含有塗料を塗布した後、800 ℃以上1000℃以下の温度に加熱後急冷して、表面の鉄亜鉛合金層直下の鋼に炭素濃化層を形成することが必要であり、このような方法によって得られた鋼材は、曲率半径が板厚の5倍以下の曲げ部を有し、表面の鉄亜鉛合金層と鋼との界面から鋼の内面に向かって50μmまでの炭素濃度のピークが、鋼の平均炭素含有濃度の1.3 倍以上であって、疲労特性に優れたものとなる。 Therefore, a steel plate or steel pipe plated with 10g / m 2 or more galvanized is formed into a shape with a bent portion whose radius of curvature is 5 times or less of the plate thickness, and then heated to a temperature of 800 ° C or higher and 1000 ° C or lower and then rapidly cooled. Then, after forming a carbon-enriched layer on the steel immediately below the iron-zinc alloy layer on the surface, or forming a steel plate or a steel pipe into a shape having a bent portion whose curvature radius is 5 times or less of the plate thickness, After applying a coating containing zinc powder so that zinc adheres to the entire surface at 10 g / m 2 or more, it is heated to a temperature of 800 ° C or higher and 1000 ° C or lower and then rapidly cooled to concentrate the carbon in the steel immediately below the iron-zinc alloy layer on the surface. It is necessary to form a layer, and the steel material obtained by such a method has a bent portion whose radius of curvature is not more than 5 times the plate thickness, and the steel material is formed from the interface between the surface iron-zinc alloy layer and the steel. The peak of carbon concentration up to 50 μm toward the inner surface of the steel is 1.3 times the average carbon content of steel Te, and is excellent in fatigue characteristics.
次に、実施例について述べる。
質量%にて、C:0.2%、Si:0.18 %、Mn:1.2%、P:0.1%以下、S:0.02 %以下、Cr:0.3%を含有する鋼をラボにて溶解し、板厚2.0mm の鋼板とした後、一部はメッキシミュレータにて亜鉛メッキを施し、図1に示す疲労試験片形状として、大気雰囲気にて900 ℃に5分保持した後、水冷してから曲げ疲労試験を施した。応力は600MPa一定として、20Hzで負荷し、破断までの回数を測定した。試験結果を図2に示す。曲げ部曲率半径が板厚の5倍を超えた場合、亜鉛メッキ付着量による疲労特性の差異は不明確である。しかし、曲げ部曲率半径が板厚の5倍以下では10g/m2以上の亜鉛メッキを施した試料の破断までの繰り返し数は亜鉛付着量が少ない場合や亜鉛メッキを施さない場合に比べて明らかに大きい。
Next, examples will be described.
In a mass%, C: 0.2%, Si: 0.18%, Mn: 1.2%, P: 0.1% or less, S: 0.02% or less, Cr: 0.3% steel was melted in the laboratory, and the plate thickness was 2.0 After making a steel plate of mm, a part is galvanized with a plating simulator, and the fatigue test piece shape shown in Fig. 1 is held at 900 ° C for 5 minutes in the air atmosphere. gave. The stress was fixed at 600 MPa, the load was applied at 20 Hz, and the number of times until fracture was measured. The test results are shown in FIG. When the bending radius of curvature exceeds 5 times the plate thickness, the difference in fatigue characteristics due to the amount of galvanized coating is unclear. However, when the radius of curvature of the bent part is less than 5 times the plate thickness, the number of repetitions until rupture of the galvanized sample with 10g / m 2 or more is clear compared with the case where the amount of zinc adhesion is small or galvanized. Big.
亜鉛メッキを施した疲労試験前の試料の断面をEPMAで線分析した結果を図3に示す。表面のFe−Zn固溶体と接する鋼に炭素の明確な濃化が確認できる。なお、表面のFe−Zn合金層中の炭素が極めて高い値を示しているが、これは表面のFe−Zn合金層中に存在する亀裂中の汚れなどを検出してしまったものと考えられる。 FIG. 3 shows the result of a line analysis of the cross section of the sample before the fatigue test on which galvanization has been performed, using EPMA. Clear enrichment of carbon can be confirmed in the steel in contact with the Fe-Zn solid solution on the surface. In addition, although the carbon in the surface Fe-Zn alloy layer shows an extremely high value, it is considered that this has detected dirt in a crack existing in the surface Fe-Zn alloy layer. .
質量%にて、C:0.3%、Si:0.1%、Mn:1.5%、P:0.1%以下、S:0.02 %以下、Ti:0.02 %、B:15ppmを含有する鋼をラボにて溶解し、板厚2.5mm の鋼板とした後、図4に示す疲労試験片形状に加工した。この後、一部は亜鉛粉末を含有する塗料を刷毛で塗布した。亜鉛粉末の塗布量は同様に塗布した試料の断面観察を行って決定した。この後、試料を表1に示す条件で熱処理してから曲げ疲労試験を施した。応力は700MPa一定として、20Hzで負荷し、破断までの回数を測定した。 In a mass%, steel containing C: 0.3%, Si: 0.1%, Mn: 1.5%, P: 0.1% or less, S: 0.02% or less, Ti: 0.02%, B: 15ppm was melted in the laboratory. After forming a steel plate having a thickness of 2.5 mm, it was processed into the shape of a fatigue test piece shown in FIG. Thereafter, a paint partially containing zinc powder was applied with a brush. The amount of zinc powder applied was similarly determined by observing the cross-section of the coated sample. Thereafter, the sample was heat-treated under the conditions shown in Table 1 and then subjected to a bending fatigue test. The stress was fixed at 700 MPa, loaded at 20 Hz, and the number of times until fracture was measured.
Claims (3)
It has a bend with a radius of curvature of 5 times or less the plate thickness, and the peak of the carbon concentration from the interface between the iron-zinc alloy layer and the steel to the inner surface of the steel is up to 50 μm. Steel material with excellent fatigue characteristics, characterized by 1.3 times or more.
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RU2496909C1 (en) * | 2012-06-13 | 2013-10-27 | Общество с ограниченной ответственностью "Вика Гал 2" | Thermodiffusion zinc coating |
WO2014046007A1 (en) | 2012-09-20 | 2014-03-27 | 新日鐵住金株式会社 | Hardened steel tube member, automobile axle beam using hardened steel tube member, and method for manufacturing hardened steel tube member |
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RU2451109C1 (en) * | 2011-03-04 | 2012-05-20 | Закрытое Акционерное Общество "Мзва" | Zinc impregnation method of metal parts surface |
RU2496909C1 (en) * | 2012-06-13 | 2013-10-27 | Общество с ограниченной ответственностью "Вика Гал 2" | Thermodiffusion zinc coating |
WO2014046007A1 (en) | 2012-09-20 | 2014-03-27 | 新日鐵住金株式会社 | Hardened steel tube member, automobile axle beam using hardened steel tube member, and method for manufacturing hardened steel tube member |
KR20150034210A (en) | 2012-09-20 | 2015-04-02 | 신닛테츠스미킨 카부시키카이샤 | Hardened steel tube member, automobile axle beam using hardened steel tube member, and method for manufacturing hardened steel tube member |
US9702019B2 (en) | 2012-09-20 | 2017-07-11 | Nippon Steel & Sumitomo Metal Corporation | Quenched steel pipe member, vehicle axle beam using quenched steel pipe member, and method for manufacturing quenched steel pipe member |
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