JP4015208B2 - Steel for cold forging with excellent fatigue properties after cold forging and method for producing the same - Google Patents
Steel for cold forging with excellent fatigue properties after cold forging and method for producing the same Download PDFInfo
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- JP4015208B2 JP4015208B2 JP23570895A JP23570895A JP4015208B2 JP 4015208 B2 JP4015208 B2 JP 4015208B2 JP 23570895 A JP23570895 A JP 23570895A JP 23570895 A JP23570895 A JP 23570895A JP 4015208 B2 JP4015208 B2 JP 4015208B2
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- cold forging
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【0001】
【発明の属する技術分野】
本発明は、冷間鍛造用鋼に関し、さらに詳しくは自動車部品等に好適な冷間鍛造後の疲労特性に優れた冷間鍛造用鋼およびその製造方法に関する。
【0002】
【従来技術】
自動車部品や建設機械用部品等の多くは、機械構造用炭素鋼を熱間鍛造し、その後、焼入れ焼きもどしを行うことによって製造されている。しかしながら、このような工程でこれら部品を製造する場合には、何度も加熱を行うため、多大な熱エネルギーを要し、コストを上昇させる原因となっている。
【0003】
このため、近時、加熱工程を省略し、圧延まま材を冷間鍛造することにより部品を製造することが検討されている。例えば、特開昭60−5821号公報、特開平4−228519号公報には、圧延制御によって組織の微細化を図り、圧延ままでの冷間加工性を向上させる技術が開示されており、また特開昭61−257452号公報には、S,P,Mnを低減し、変形能、変形抵抗を改善する技術が開示されている。
【0004】
【発明が解決しようとする課題】
しかしながら、これらの技術はいずれも、冷間加工性という製造時の問題を解決することだけを念頭において提案されたもので、製品として要求される特性、特に、自動車部品等で必要とされる疲労特性については全く考慮されていない。
【0005】
本発明はかかる事情に鑑みてなされたものであって、圧延ままで冷間鍛造性に優れ、かつ、冷間鍛造後の疲労特性に優れた冷間鍛造用鋼およびその製造方法を提供することを目的とする。
【0006】
【課題を解決するための手段】
本発明者らは、圧延まま材の冷間鍛造性を向上させ、かつ冷間鍛造後の疲労特性を向上させるべく鋭意研究を重ねた結果、以下の知見を得るに至った。
(1)圧延まま材の冷間鍛造性向上のためには、フェライト主体の組織を有する鋼では、フェライト分率の増大(Mn/Cの増大)、フェライトの軟化(低Si、低P)、介在物の低減(低S、低O)が有効である。
【0007】
(2)一方、冷間鍛造後の疲労特性向上のためには、パーライト分率の増大(C量の増大)が有効である。
(3)上記(1)及び(2)は相反することであるが、C量、Mn/C、及び炭素当量を適切に規定することにより両特性を満足する鋼が得られる。
【0008】
本発明はこのような知見に基づいて完成されたものであって、重量%で、C:0.19〜0.38%、Si:0.10%以下、Mn:0.5〜1.4%、Cr:0.05〜0.50、P:0.01%以下、S:0.015%以下、O:0.0015%以下を含有し、残部Feおよび不可避的不純物からなり、Mn/C=1.5〜6.0を満たし、かつ以下に示すC当量が0.37〜0.49%であることを特徴とする冷間鍛造後の疲労特性に優れた冷間鍛造用鋼を提供するものである。
【0009】
C当量=C+(Si/24)+(Mn/6)+(Cr/5)
また、上記鋼を製造するに当たり、圧延時の仕上げ圧延温度を900℃以下にすることを特徴とする冷間鍛造後の疲労特性に優れた冷間鍛造用鋼の製造方法を提供するものである。
【0010】
なお、冷間鍛造後の疲労特性を一層向上させる観点からは、C:0.23〜0.38%、Mn:0.6〜1.3%、Mn/C:1.5〜5.0%、C当量:0.42〜0.49%であることが好ましい。
【0011】
【発明の実施の形態】
以下、本発明について具体的に説明する。
まず、本発明における成分等の限定理由について述べる。
C:0.19〜0.38%
Cは疲労特性向上に必要な元素であるが、0.19%未満では十分な疲労特性が得られず、また0.38%を超えると冷間鍛造性が劣化する。従って、C量を0.19〜0.38%とする。冷間鍛造後の疲労特性を一層向上させる観点からは、0.23〜0.38%の範囲が好ましい。
【0012】
Si:0.10%以下
Siはフェライトに固溶し、フェライトを強化する成分であるため、0.10%を超えると冷間鍛造性を著しく劣化させる。従って、Si量を0.10%以下とする。
【0013】
Mn:0.5〜1.4%
Mnは鋼に必要な強度を付与する元素であるが、その量が0.5%未満では必要強度が得られず、また、1.4%を超えるとベイナイト組織が出現し、冷間鍛造性が劣化する。従って、Mn量を0.5〜1.4%とする。良好な疲労特性を得る観点からは0.6〜1.3%の範囲が好ましい。
【0014】
Cr:0.05〜0.5%
Crは、少量添加により加工硬化を抑制し、冷間鍛造性を向上させる。しかし、0.05%未満ではその効果がなく、0.5%を超えると固溶硬化が大きくなり、また冷間鍛造性が劣化する。従って、Cr量を0.05〜0.5%とする。
【0015】
P:0.01%以下
Pはフェライトに固溶してフェライトを強化し、0.01%を超えると冷間鍛造性を劣化させるので、0.01%以下とする。
【0016】
S:0.015%以下
SはMnSを形成し、0.015%を超えると冷間鍛造性を劣化させるので、0.015%以下とする。
【0017】
O:0.0015%以下
Oは酸化物を形成し、冷間鍛造性を劣化させるため、0.0015%以下とする。
【0018】
Mn/C:1.5〜6.0
Mn/Cはフェライト分率に影響を及ぼすが、その値が1.5未満ではフェライト分率が少なく、冷間鍛造性が劣化する。また、6.0を超えるとフェライト分率が多くなり、疲労強度が劣化する。従って、Mn/Cを1.5〜6.0とする。より一層疲労特性を向上させる観点からは、1.5〜5.0が好ましい。
【0019】
C当量:0.37〜0.49%
C当量はC+(Si/24)+(Mn/6)+(Cr/5)で表され、必要な強度および疲労特性を確保するために規定されるが、その値が0.37%未満では強度が低くかつ疲労特性が劣り、0.49%を超えると冷間鍛造性が劣る。従って、C当量を0.37〜0.49%とする。疲労特性を向上させる観点からは0.42〜0.49%の範囲が好ましい。
【0020】
以上のような成分組成を有する本発明の鋼は、圧延ままで用いることを前提としているが、その後に熱処理を行うことを排除するものではない。この圧延の際に、仕上げ圧延温度を900℃以下にすることが好ましい。仕上げ圧延温度が900℃を超えると圧延後の組織が大きくなり、冷間鍛造性のみならず、疲労特性も劣化する。仕上げ圧延温度が900℃以下であれば、冷間鍛造性および疲労特性の両方が優れたものとなる。
【0021】
【実施例】
(実施例1)
表1に示す成分組成を有する鋼を150kg真空溶解炉にて溶製し、得られた鋼塊を1050℃に加熱し、40mm丸棒に圧延した。表1中No.1〜10は本発明鋼であり、No.11〜23は比較鋼である。また、No.24はS43C鋼であり、球状化焼鈍を行って試験に供した。
【0022】
【表1】
【0023】
これら圧延ままの丸棒からJIS4号試験片(平行部14mmφ、標点距離50mm)、圧縮試験片(14mmφ×21mm溝付き)を採取し、引張試験及び圧縮試験を行った。なお、圧縮試験片の詳細を図1に示す。
【0024】
また、冷間鍛造後の疲労特性をシミュレートするために40%引抜き材の疲労特性を調べた。この場合に、40%引抜き材(31mmφ)からJIS4号引張試験片、小野式回転曲げ疲労試験片(平行部10mmφ)を採取し、引張、疲労試験を行った。その結果を表2に示す。なお、表2の「限界圧縮率」は圧縮試験における割れ発生限界圧縮率を示し、この値で冷間鍛造性を評価した。また、40%引抜き材の疲労強度は107 回での疲労限で評価した。
【0025】
【表2】
【0026】
表2に示すように、本発明鋼であるNo.1〜10は、割れ発生限界圧縮率が40%を超える高い値を示しており、また40%引抜き材の疲労強度も350N/mm2 以上であって、いずれもNo.24のS43Cの球状化焼鈍材よりも優れていることが確認された。すなわち、圧延ままの冷間鍛造性および疲労強度がいずれも、従来材であるS43Cの球状化焼鈍材よりも優れていた。
【0027】
これに対して、比較鋼のNo.11〜23は冷間鍛造性及び疲労特性のうち少なくとも一方が劣っていた。すなわち、No.11はC量が少ないため、冷間鍛造性は良好であるが疲労強度が劣っていた。No.12はC量が多いため、冷間鍛造性が劣っていた。なお、No.12以降、冷間鍛造性が劣っていた鋼は40%引抜き材の疲労試験は行わなかった。また、No.13はSiが高いため、No.14は各成分の範囲は本発明の範囲であるがC当量が高いため、No.16はMn量が高いため、No.17はP量が高いため、No.18はS量が高いため、No.19は各成分の範囲は本発明の範囲であるがMn/Cが低いため、No.22はCrが高くC当量が高いため、さらにNo.23はO量が高いため、いずれも冷間鍛造性が劣っていた。No.15はMnが低いため、No.20は各成分の範囲は本発明の範囲であるがMn/Cが高いため、No.21は各成分の範囲は本発明の範囲であるがC当量が低いため、冷間鍛造性は良好であるものの、疲労強度が劣っていた。
【0028】
(実施例2)
表3に示す本発明を満たす組成を有する鋼を実施例1と同様な方法にて製造した。この際に、圧延時の仕上げ温度を950℃、880℃、850℃の3水準とした。その後の試験も実施例1と同様に行った。その結果を表4に示す。
表4に示すように、仕上げ圧延温度を900℃以下にすることにより、冷間鍛造性および疲労特性の両者が優れた値を示すことが確認された。
【0029】
【表3】
【0030】
【表4】
【0031】
【発明の効果】
以上のように、本発明によれば、圧延ままで冷間鍛造性に優れ、かつ冷間鍛造後の疲労特性に優れた冷間鍛造用鋼およびその製造方法が提供される。従って、自動車部品等の製造時に軟化焼鈍を必要とせず、圧延ままでの冷間鍛造できるのでコスト低減に寄与することができ、また、冷間鍛造を施した製品の疲労強度を向上させることができる。
【図面の簡単な説明】
【図1】圧縮試験片を説明するための図。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a steel for cold forging, and more particularly to a steel for cold forging excellent in fatigue characteristics after cold forging suitable for automobile parts and the like, and a method for producing the same.
[0002]
[Prior art]
Many automobile parts and construction machine parts are manufactured by hot forging machine structural carbon steel, followed by quenching and tempering. However, when these parts are manufactured in such a process, since heating is performed many times, a great amount of heat energy is required, which increases the cost.
[0003]
For this reason, recently, it has been studied to manufacture a part by omitting the heating step and cold forging the material as it is rolled. For example, JP-A-60-5821 and JP-A-4-228519 disclose techniques for reducing the microstructure by rolling control and improving the cold workability as it is rolled. Japanese Patent Application Laid-Open No. 61-257452 discloses a technique for reducing S, P, and Mn and improving deformability and deformation resistance.
[0004]
[Problems to be solved by the invention]
However, all of these technologies have been proposed only with a view to solving the manufacturing problem of cold workability, and the characteristics required for products, particularly the fatigue required for automobile parts, etc. The characteristics are not considered at all.
[0005]
The present invention has been made in view of such circumstances, and provides a cold forging steel excellent in cold forging while being rolled, and excellent in fatigue characteristics after cold forging, and a method for producing the same. With the goal.
[0006]
[Means for Solving the Problems]
As a result of intensive studies to improve the cold forgeability of the as-rolled material and improve the fatigue characteristics after cold forging, the present inventors have obtained the following knowledge.
(1) In order to improve the cold forgeability of the as-rolled material, in a steel having a structure mainly composed of ferrite, increase in ferrite fraction (increase in Mn / C), softening of ferrite (low Si, low P), Reduction of inclusions (low S, low O) is effective.
[0007]
(2) On the other hand, increasing the pearlite fraction (increasing the amount of C) is effective for improving the fatigue characteristics after cold forging.
(3) Although the above (1) and (2) are contradictory, steel satisfying both characteristics can be obtained by appropriately defining the C content, Mn / C, and carbon equivalent.
[0008]
This invention was completed based on such knowledge, Comprising: In weight%, C: 0.19-0.38%, Si: 0.10% or less, Mn: 0.5-1.4 %, Cr: 0.05 to 0.50, P: 0.01% or less, S: 0.015% or less, O: 0.0015% or less, the balance being Fe and inevitable impurities, Mn / A cold forging steel excellent in fatigue characteristics after cold forging, characterized in that C = 1.5 to 6.0 and the C equivalent shown below is 0.37 to 0.49% It is to provide.
[0009]
C equivalent = C + (Si / 24) + (Mn / 6) + (Cr / 5)
Further, in producing the steel, a method for producing a cold forging steel excellent in fatigue characteristics after cold forging, characterized in that the finish rolling temperature during rolling is 900 ° C. or lower. .
[0010]
From the viewpoint of further improving the fatigue characteristics after cold forging, C: 0.23 to 0.38%, Mn: 0.6 to 1.3%, Mn / C: 1.5 to 5.0 %, C equivalent: 0.42 to 0.49% is preferable.
[0011]
DETAILED DESCRIPTION OF THE INVENTION
Hereinafter, the present invention will be specifically described.
First, the reasons for limiting the components and the like in the present invention will be described.
C: 0.19 to 0.38%
C is an element necessary for improving the fatigue characteristics, but if it is less than 0.19%, sufficient fatigue characteristics cannot be obtained, and if it exceeds 0.38%, the cold forgeability deteriorates. Therefore, the C content is 0.19 to 0.38%. From the viewpoint of further improving the fatigue characteristics after cold forging, the range of 0.23 to 0.38% is preferable.
[0012]
Si: 0.10% or less Since Si is a component that dissolves in ferrite and strengthens ferrite, if it exceeds 0.10%, cold forgeability is significantly deteriorated. Therefore, the Si amount is set to 0.10% or less.
[0013]
Mn: 0.5 to 1.4%
Mn is an element that imparts the necessary strength to steel, but if the amount is less than 0.5%, the required strength cannot be obtained, and if it exceeds 1.4%, a bainite structure appears and cold forgeability Deteriorates. Therefore, the amount of Mn is set to 0.5 to 1.4%. From the viewpoint of obtaining good fatigue characteristics, the range of 0.6 to 1.3% is preferable.
[0014]
Cr: 0.05-0.5%
Cr is added in a small amount to suppress work hardening and improve cold forgeability. However, if it is less than 0.05%, there is no effect, and if it exceeds 0.5%, solid solution hardening increases, and cold forgeability deteriorates. Therefore, the Cr content is 0.05 to 0.5%.
[0015]
P: 0.01% or less P dissolves in ferrite to strengthen the ferrite, and if it exceeds 0.01%, cold forgeability deteriorates, so 0.01% or less.
[0016]
S: 0.015% or less S forms MnS. If it exceeds 0.015%, the cold forgeability deteriorates, so the content is made 0.015% or less.
[0017]
O: 0.0015% or less O forms an oxide and degrades cold forgeability, so 0.0015% or less.
[0018]
Mn / C: 1.5 to 6.0
Mn / C affects the ferrite fraction, but if the value is less than 1.5, the ferrite fraction is small and the cold forgeability deteriorates. Moreover, when it exceeds 6.0, a ferrite fraction will increase and fatigue strength will deteriorate. Therefore, Mn / C is set to 1.5 to 6.0. From the viewpoint of further improving the fatigue characteristics, 1.5 to 5.0 is preferable.
[0019]
C equivalent: 0.37 to 0.49%
The C equivalent is expressed by C + (Si / 24) + (Mn / 6) + (Cr / 5), and is defined to ensure necessary strength and fatigue characteristics. However, when the value is less than 0.37% The strength is low and the fatigue characteristics are inferior, and if it exceeds 0.49%, the cold forgeability is inferior. Therefore, the C equivalent is set to 0.37 to 0.49%. From the viewpoint of improving fatigue characteristics, a range of 0.42 to 0.49% is preferable.
[0020]
The steel of the present invention having the above component composition is premised on being used as it is rolled, but does not exclude the subsequent heat treatment. In this rolling, the finish rolling temperature is preferably 900 ° C. or lower. When the finish rolling temperature exceeds 900 ° C., the structure after rolling becomes large, and not only cold forgeability but also fatigue characteristics are deteriorated. When the finish rolling temperature is 900 ° C. or lower, both cold forgeability and fatigue characteristics are excellent.
[0021]
【Example】
Example 1
Steel having the composition shown in Table 1 was melted in a 150 kg vacuum melting furnace, and the resulting steel ingot was heated to 1050 ° C. and rolled into a 40 mm round bar. No. in Table 1 Nos. 1 to 10 are steels of the present invention. 11 to 23 are comparative steels. No. 24 is S43C steel, which was subjected to spheroidizing annealing and used for the test.
[0022]
[Table 1]
[0023]
A JIS No. 4 test piece (
[0024]
In addition, the fatigue characteristics of 40% drawn material were examined to simulate the fatigue characteristics after cold forging. In this case, JIS No. 4 tensile test pieces and Ono-type rotary bending fatigue test pieces (parallel portion 10 mmφ) were sampled from 40% drawn material (31 mmφ), and subjected to tensile and fatigue tests. The results are shown in Table 2. “Limit compression ratio” in Table 2 indicates the crack compression limit compression ratio in the compression test, and the cold forgeability was evaluated based on this value. The fatigue strength of the 40% drawn material was evaluated by the fatigue limit at 10 7 times.
[0025]
[Table 2]
[0026]
As shown in Table 2, no. Nos. 1 to 10 show high values in which the crack initiation limit compression ratio exceeds 40%, and the fatigue strength of the 40% drawn material is 350 N / mm 2 or more. It was confirmed that it was superior to the S43C spheroidized annealing material of 24. That is, both the cold forgeability and the fatigue strength as-rolled were superior to the conventional spheroidized annealing material of S43C.
[0027]
In contrast, No. of comparative steel. As for 11-23, at least one was inferior among cold forgeability and fatigue characteristics. That is, no. Since No. 11 had a small amount of C, the cold forgeability was good but the fatigue strength was inferior. No. Since No. 12 had a large amount of C, the cold forgeability was inferior. In addition, No. From 12 onwards, the steel with poor cold forgeability was not subjected to a 40% drawn material fatigue test. No. No. 13 is high in Si. No. 14 is the range of the present invention, but the C equivalent is high. No. 16 has a high Mn content. No. 17 has a high P content. No. 18 has a high amount of S. No. 19 is the range of the present invention, but the Mn / C is low. No. 22 has a high Cr and a high C equivalent. Since No. 23 had a high amount of O, all of them had poor cold forgeability. No. No. 15 has a low Mn. No. 20 is the range of the present invention, but the Mn / C is high. Although the range of each
[0028]
(Example 2)
Steel having a composition satisfying the present invention shown in Table 3 was produced in the same manner as in Example 1. At this time, the finishing temperature during rolling was set to three levels of 950 ° C., 880 ° C., and 850 ° C. Subsequent tests were performed in the same manner as in Example 1. The results are shown in Table 4.
As shown in Table 4, it was confirmed that by setting the finish rolling temperature to 900 ° C. or lower, both the cold forgeability and the fatigue characteristics show excellent values.
[0029]
[Table 3]
[0030]
[Table 4]
[0031]
【The invention's effect】
As described above, according to the present invention, a steel for cold forging having excellent cold forgeability as it is rolled and excellent fatigue characteristics after cold forging and a method for producing the same are provided. Therefore, it does not require soft annealing during the production of automobile parts, etc., and can be cold forged as it is rolled, thus contributing to cost reduction and improving the fatigue strength of products subjected to cold forging. it can.
[Brief description of the drawings]
FIG. 1 is a view for explaining a compression test piece.
Claims (2)
C当量=C+(Si/24)+(Mn/6)+(Cr/5)By weight, C: 0.19 to 0.38%, Si: 0.10% or less, Mn: 0.5 to 1.4%, Cr: 0.05 to 0.50, P: 0.01% Hereinafter, S: 0.015% or less, O: 0.0015% or less, comprising the balance Fe and inevitable impurities , satisfying Mn / C = 1.5 to 6.0, and C equivalent shown below Is a steel for cold forging excellent in fatigue characteristics after cold forging, characterized by being 0.37 to 0.49%.
C equivalent = C + (Si / 24) + (Mn / 6) + (Cr / 5)
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JP23570895A JP4015208B2 (en) | 1995-09-13 | 1995-09-13 | Steel for cold forging with excellent fatigue properties after cold forging and method for producing the same |
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JP23570895A JP4015208B2 (en) | 1995-09-13 | 1995-09-13 | Steel for cold forging with excellent fatigue properties after cold forging and method for producing the same |
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JPH0978181A JPH0978181A (en) | 1997-03-25 |
JP4015208B2 true JP4015208B2 (en) | 2007-11-28 |
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JP (1) | JP4015208B2 (en) |
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1995
- 1995-09-13 JP JP23570895A patent/JP4015208B2/en not_active Expired - Lifetime
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JPH0978181A (en) | 1997-03-25 |
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