JP2006225701A - Steel wire rod excellent in cold-forgeability after spheroidizing-treatment and producing method therefor - Google Patents
Steel wire rod excellent in cold-forgeability after spheroidizing-treatment and producing method therefor Download PDFInfo
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Abstract
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本発明は、ボルト、ナット、ねじ、歯車その他の機械部品を冷間加工によって製造する際に、冷間加工前に素材に施される球状化焼鈍時間を短縮し、かつ、球状化処理後の冷間加工性に優れさせた鋼線材とその製造方法に関するものである。なお、本発明の対象とする鋼線材の概念には、所謂「バーインコイル」も含むものとする。 The present invention reduces the spheroidizing annealing time applied to the material before cold working when manufacturing bolts, nuts, screws, gears, and other mechanical parts by cold working, and after spheroidizing treatment. The present invention relates to a steel wire rod having excellent cold workability and a manufacturing method thereof. It should be noted that the concept of the steel wire that is the subject of the present invention includes a so-called “burn-in coil”.
冷間加工は、生産性が高く製品の寸法精度に優れ、鋼材の歩留が良いことから幅広い分野で利用されている。このような冷間加工に供される鋼材は、局部的に大きな変形を受けるため、引張強さが低く延性が高いことが求められている。これは鋼材の冷間加工性が悪い場合、材料割れによる不良品の発生や、工具ダイスの破損などが生じ、経済性が悪化するからである。こうしたことから、冷間加工性を向上させる方策の一つとして球状化焼鈍を実施している。
球状化焼鈍の目的は、鋼中の炭化物を球状化して微細かつ均一に分散させ、これにより冷間加工性、被削性、および最終製品の耐磨耗性を向上させることにある。しかしながら、球状化焼鈍は一般的に１０〜２０時間の処理時間を要し、生産性の向上やエネルギーコストの低減という観点から、短時間化が求められている。但し、球状化焼鈍のための時間短縮を実施する場合、球状化処理後の基本特性である優れた冷間加工性を有することは必要条件である。
Cold working is used in a wide range of fields because of its high productivity, excellent dimensional accuracy of products, and good yield of steel materials. The steel material used for such cold working is required to have low tensile strength and high ductility because it undergoes large deformation locally. This is because, when the cold workability of the steel material is poor, generation of defective products due to material cracking, breakage of the tool die, and the like occur, and the economic efficiency deteriorates. For these reasons, spheroidizing annealing is performed as one of the measures for improving the cold workability.
The purpose of spheroidizing annealing is to spheroidize and uniformly disperse carbides in the steel, thereby improving cold workability, machinability, and wear resistance of the final product. However, spheroidizing annealing generally requires a processing time of 10 to 20 hours, and a reduction in time is required from the viewpoint of improving productivity and reducing energy costs. However, in order to shorten the time for spheroidizing annealing, it is a necessary condition to have excellent cold workability, which is a basic characteristic after spheroidizing treatment.
鋼材の球状化焼鈍の短時間化に関する技術はこれまでにも様々開発されており、例えば以下に記載の特許文献１には、球状化処理前の組織をベイナイト単相にする方法が提案されている。この技術は、球状化処理前の組織をベイナイト単相とすることによって、セメンタイトの球状化を促進し、短時間化を図ろうとするものである。
一方、初析フェライト分率が５〜３０面積％、残りの組織をベイナイト主体とし、かつベイナイトのラス間隔の平均値が０．３μm以上という手段が以下の特許文献２に開示されている。これにより、球状化処理後の加工性能の向上、及び変形抵抗の低減が可能である。
On the other hand, Patent Document 2 below discloses a means in which the pro-eutectoid ferrite fraction is 5 to 30% by area, the remaining structure is mainly bainite, and the average value of lath spacing of bainite is 0.3 μm or more. Thereby, the processing performance after spheroidizing treatment can be improved and the deformation resistance can be reduced.
先の特許文献１に記載の技術によって、球状化焼鈍の短時間化は達成されるが、ベイナイト単相組織では、球状化処理後の冷間加工時の変形抵抗が高くなってしまい、工具ダイス寿命が低下するという問題は依然として解消されない。
先の特許文献２に記載の技術は、熱間圧延後の熱処理で徐冷を施すことによって当該組織を実現するため、生産性の低下とコスト上昇を招いている。また、ベイナイト分率が過剰となった場合は、球状化処理後の冷間加工時の変形抵抗が高くなってしまうという問題もある。
Although the technique described in Patent Document 1 shortens the time for spheroidizing annealing, the bainite single-phase structure has a high deformation resistance during cold working after spheroidizing treatment, resulting in a tool die. The problem of reduced life is still not solved.
The technique described in the above-mentioned Patent Document 2 realizes the structure by performing gradual cooling in the heat treatment after hot rolling, which leads to a decrease in productivity and an increase in cost. In addition, when the bainite fraction becomes excessive, there is a problem that deformation resistance at the time of cold working after spheroidizing treatment becomes high.
本発明はこのような状況下でなされたものであり、その目的は、球状化焼鈍時間の短縮と、球状化処理後の加工性能の向上と変形抵抗の低減を実現する鋼線材、及びこうした鋼線材を製造する為の有用な方法を提供することにある。 The present invention has been made under such circumstances. The purpose of the present invention is to shorten the spheroidizing annealing time, improve the processing performance after spheroidizing treatment and reduce deformation resistance, and such steel. It is to provide a useful method for producing a wire.
本発明は上記目的を達成するものであって、その要旨とするところは次の通りである。
（１）上記の目的を達成し得た本発明の鋼線材は、Ｃ：０．００５〜０．６％（質量％、以下同じ）を含み、擬似パーライトが１０面積％以上、ベイナイトが７５面積％以下、フェライトが６０面積％以下、（擬似パーライト面積％＋ベイナイト面積％＋フェライト面積％）≧９０面積％の関係を満足することを特徴とする。
（２）上述した本発明の鋼線材に、その他の元素を添加する場合の具体的な化学成分としては、Ｓｉ：０．５０％以下、Ｍｎ：０．２０〜１．００％、Ａｌ：０．０１〜０．０６％、Ｐ：０．０２％以下、Ｓ：０．０２％以下、Ｎ：０．０１％以下に夫々抑制したものが挙げられる。
（３）更に、本発明の鋼線材においては、Ｃｒ：１．５０％以下、Ｍｏ：０．５０％以下、Ｎｉ：１．００％以下、Ｖ：０．５０％以下、Ｂ：０．００５％以下、Ｔｉ：０．０５％以下よりなる群から選ばれる１種以上の元素を含有し、残余がＦｅ及び不可避不純物を含むものを適用することができる。
The present invention achieves the above object, and the gist thereof is as follows.
(1) The steel wire rod of the present invention capable of achieving the above object includes C: 0.005 to 0.6% (mass%, hereinafter the same), pseudo pearlite is 10 area% or more, and bainite is 75 area. % Or less, ferrite is 60 area% or less, and (pseudo pearlite area% + bainite area% + ferrite area%) ≧ 90 area% is satisfied.
(2) Specific chemical components when other elements are added to the steel wire rod of the present invention described above are as follows: Si: 0.50% or less, Mn: 0.20-1.00%, Al: 0 0.01% to 0.06%, P: 0.02% or less, S: 0.02% or less, and N: 0.01% or less.
(3) Furthermore, in the steel wire rod of the present invention, Cr: 1.50% or less, Mo: 0.50% or less, Ni: 1.00% or less, V: 0.50% or less, B: 0.005 % Or less, Ti: containing one or more elements selected from the group consisting of 0.05% or less, and the remainder containing Fe and inevitable impurities can be applied.
（４）本発明の鋼線材を製造するに当たっては、熱間圧延後、７５０〜１０００℃の捲取温度とした後、７５０〜１０００℃から４００〜５５０℃までを２０℃／ｓ以上の速度で冷却し、４００〜５５０℃において２０秒以上保持し、恒温変態を完了させたのち冷却することが好ましい。 (4) In manufacturing the steel wire rod of the present invention, after hot rolling, the temperature is set to 750 to 1000 ° C., and the temperature from 750 to 1000 ° C. to 400 to 550 ° C. is increased at a rate of 20 ° C./s or more. It is preferable to cool, hold at 400 to 550 ° C. for 20 seconds or longer, complete the isothermal transformation, and then cool.
本発明は以上の様に構成されており、球状化焼鈍時間の短縮を可能とし、かつ、球状化処理後における加工性能の向上と変形抵抗の低減を達成し、優れた冷間鍛造性を発揮する鋼線材が実現できる。
本発明においては、疑似パーライトとベイナイトとフェライトの面積％を規定して望ましい範囲としたので、加工性能と変形抵抗のバランスをとることができ、優れた冷間鍛造性を発揮する鋼線材を得ることができる。
The present invention is configured as described above, and can shorten the spheroidizing annealing time, achieve improved processing performance and reduced deformation resistance after spheroidizing treatment, and exhibits excellent cold forgeability. Steel wire rod can be realized.
In the present invention, the area percentage of pseudo pearlite, bainite and ferrite is defined as a desirable range, so that it is possible to balance processing performance and deformation resistance, and obtain a steel wire rod exhibiting excellent cold forgeability. be able to.
また、本発明においては、望ましい温度と条件で処理し、恒温変態を完了させた後に冷却することにより、球状化焼鈍時間の短縮を可能とし、かつ、球状化処理後における加工性能の向上と変形抵抗の低減を達成し、優れた冷間鍛造性を発揮する鋼線材を製造することができる効果を奏する。 Further, in the present invention, it is possible to shorten the spheroidizing annealing time by processing at a desired temperature and conditions, and cooling after completing the isothermal transformation, and improving the processing performance and deformation after the spheroidizing process. There is an effect that a reduction in resistance can be achieved and a steel wire rod exhibiting excellent cold forgeability can be manufactured.
以下に本発明について最良の形態に基づいて詳細に説明する。
本発明者らが、鋼材の球状化焼鈍時間の短縮、及び、球状化後における加工性能の向上と変形抵抗の低減の両方を満足させるための最適な前組織を検討した結果、擬似パーライトが１０面積％以上、ベイナイトが７５面積％以下、フェライトが６０面積％以下、（擬似パーライト面積％＋ベイナイト面積％＋フェライト面積％）≧９０面積％とすることが、球状化焼鈍時間の短縮に対して有効であると判明した。
The present invention will be described in detail below based on the best mode.
As a result of studying the optimum front structure for satisfying both the reduction of the spheroidizing annealing time of the steel material and the improvement of the processing performance and the reduction of the deformation resistance after the spheroidization, the present inventors have found that the pseudo pearlite is 10 Area% or more, bainite is 75 area% or less, ferrite is 60 area% or less, and (pseudo pearlite area% + bainite area% + ferrite area%) ≧ 90 area% for shortening the spheroidizing annealing time Proved effective.
本発明の鋼線材では、擬似パーライト分率を１０面積％以上とする必要がある。これは、擬似パーライト組織に含まれるセメンタイトは迅速に球状化されるため、短時間の球状化処理後の冷間加工において加工性能が高くなるからである。
擬似パーライトは、低温で変態し炭素の拡散が充分でないため、セメンタイトは粒状もしくは途中で途切れた形態を示し、フェライトとセメンタイトが層状をなし、高温で変態して生成する一般的なパーライト組織とは異なる。この擬似パーライト中のセメンタイトの形態は以下の通りである。
長径／短径の比は１〜２０の範囲で、それらの測定されたセメンタイト全体数の平均値は２．０であり、長径／短径の比が３．０以下となる比率は測定セメンタイト全体数の個数百分率９０％以上である。そして、これらのセメンタイトが、最大で１μｍ以内、平均で０．０５μｍの間隔で隣接する。こうした領域を擬似パーライト組織と定義する。
尚、この観察は、走査型電子顕微鏡で５０００倍の倍率にて行い、１００個以上のセメンタイトの長径、短径、セメンタイト間隔を測定するものである。
In the steel wire of the present invention, the pseudo pearlite fraction needs to be 10 area% or more. This is because the cementite contained in the pseudo pearlite structure is rapidly spheroidized, so that the processing performance is improved in cold working after a short spheroidizing treatment.
Pseudo pearlite is transformed at low temperature and carbon diffusion is not enough, so cementite is granular or shows a discontinuous form, ferrite and cementite are layered, and is a general pearlite structure formed by transformation at high temperature Different. The form of cementite in this pseudo pearlite is as follows.
The ratio of the major axis / minor axis is in the range of 1 to 20, the average value of the total number of measured cementites is 2.0, and the ratio of the major axis / minor axis ratio is 3.0 or less is the total measured cementite. The number percentage of the number is 90% or more. These cementites are adjacent to each other at an interval of a maximum of 1 μm and an average of 0.05 μm. Such a region is defined as a pseudo pearlite structure.
This observation is performed with a scanning electron microscope at a magnification of 5000 times to measure the major axis, minor axis, and cementite interval of 100 or more cementites.
以上説明のように、擬似パーライトには粒状のセメンタイトが多く含まれる。よって、擬似パーライトを１０面積％以上含む場合、焼鈍においてセメンタイトの球状化が促進され、短時間の球状化処理としても、その後の冷間加工において加工性能は高くなる。
本発明の鋼線材では、ベイナイトとフェライトを含んでいても良い。ベイナイト組織は、セメンタイトが均一に分散し、球状化処理後の冷間加工において加工性能が高くなる。しかしながら、ベイナイトは硬質相であるため多量に存在すると、変形抵抗が高くなってしまう。よって、ベイナイトは７５面積％以下とする。
一方、フェライトは６０面積％以下とする。フェライト分率が高くなると、冷間加工時の変形抵抗は低減されるが、球状セメンタイトの分散性が悪化して加工性能が低下する。このため、フェライト分率は６０面積％以下とする。
As described above, the pseudo pearlite contains a large amount of granular cementite. Therefore, when pseudo pearlite is contained in an area of 10 area% or more, spheroidization of cementite is promoted during annealing, and the processing performance is improved in the subsequent cold working even as a short spheroidization treatment.
The steel wire rod of the present invention may contain bainite and ferrite. In the bainite structure, cementite is uniformly dispersed, and the processing performance is improved in the cold working after the spheroidizing treatment. However, since bainite is a hard phase, if it exists in a large amount, the deformation resistance becomes high. Therefore, bainite is 75 area% or less.
On the other hand, ferrite is 60 area% or less. When the ferrite fraction is high, the deformation resistance during cold working is reduced, but the dispersibility of spherical cementite is deteriorated and the working performance is lowered. For this reason, a ferrite fraction shall be 60 area% or less.
更に、本発明の鋼線材では、（擬似パーライト面積％＋ベイナイト面積％＋フェライト面積％）≧９０面積％とする必要がある。
これは、高温で変態して生成する層状のパーライト組織が多く存在する場合、板状の形態であるセメンタイトが迅速に球状化されず、球状化処理後の冷間加工において加工性能が低くなってしまうからである。また、恒温変態が完了せず、硬質なマルテンサイトが多量に生成すると変形抵抗が高くなってしまうことから、（擬似パーライト面積％＋ベイナイト面積％＋フェライト面積％）≧９０面積％とする必要がある。
Furthermore, in the steel wire rod of the present invention, it is necessary to satisfy (pseudo pearlite area% + bainite area% + ferrite area%) ≧ 90 area%.
This is because when there is a lot of layered pearlite structure generated by transformation at high temperature, the cementite in the form of a plate is not rapidly spheroidized, and the processing performance is reduced in cold working after spheroidizing treatment. Because it ends up. Further, since the isothermal transformation is not completed and a large amount of hard martensite is generated, the deformation resistance becomes high. Therefore, it is necessary to satisfy (pseudo pearlite area% + bainite area% + ferrite area%) ≧ 90 area%. is there.
本発明の製造方法における各条件について以下に説明する。
本発明の製造方法では、熱間圧延後、７５０〜１０００℃で捲取る。ここで捲取圧延温度が、７５０℃未満ではとリング状に捲き取ることが困難となることから７５０℃を下限とする。また、１０００℃を超えると酸化スケールが増大し、本発明の鋼線材を具体的な商品に加工して利用する業者など（需要家）での歩留ロスが生じるため１０００℃を上限とすることが好ましい。
圧延材を捲取後、７５０〜１０００℃から４００〜５５０℃までを２０℃／ｓ以上の速度で冷却し、４００〜５５０℃で２０秒以上保持して恒温変態を完了させる。恒温保定温度を４００〜５５０℃としたのは、４００℃未満では変態に長時間を要し、更に冷却後の組織に大量のベイナイトやマルテンサイトが生じる可能性があるため、４００℃を下限温度とする。また、５５０℃を超えると層状パーライト組織が急増し、球状化焼鈍時間に長時間を要し、かつ加工性能の低下を招いてしまうため５５０℃を上限温度とする。保定時間は、恒温変態が終了するために２０秒以上とする。上限は特に規定するものではないが、生産性向上の観点から、１５０秒以内とすることが望ましい。
Each condition in the production method of the present invention will be described below.
In the production method of the present invention, after hot rolling, it is scraped at 750 to 1000 ° C. Here, if the winding temperature is less than 750 ° C., it is difficult to scrape in a ring shape, so 750 ° C. is set as the lower limit. In addition, when the temperature exceeds 1000 ° C, the oxide scale increases, and yield loss is caused at a supplier who uses the steel wire rod according to the present invention after processing it into a specific product. Is preferred.
After rolling the rolled material, the temperature from 750 to 1000 ° C. to 400 to 550 ° C. is cooled at a rate of 20 ° C./s or more, and held at 400 to 550 ° C. for 20 seconds or more to complete the isothermal transformation. The constant temperature holding temperature is set to 400 to 550 ° C. If the temperature is lower than 400 ° C., it takes a long time for transformation, and a large amount of bainite and martensite may be generated in the cooled structure. And If the temperature exceeds 550 ° C., the layered pearlite structure increases rapidly, requiring a long time for the spheroidizing annealing time, and lowering the processing performance, so 550 ° C. is set as the upper limit temperature. The holding time is set to 20 seconds or longer in order to complete the constant temperature transformation. The upper limit is not particularly specified, but is preferably within 150 seconds from the viewpoint of improving productivity.
本発明の鋼線材は、Ｃを０．００５〜０．６０％含むものである。Ｃに加えてその他の元素を添加する場合は、Ｓｉ：０．５０％以下、Ｍｎ：０．２０〜１．００％、Ａｌ：０．０１〜０．０６％、Ｐ：０．０２％以下、Ｓ：０．０２％以下、Ｎ：０．０１％以下に夫々規制する。これら元素の範囲限定理由は下記の通りである。
Ｃ：０．００５〜０．６０％
Ｃは、ボルト、ねじ等、本発明の鋼線材から形成する商品に求められる強度により規定される。０．００５％未満では必要な強度が得られないため下限は０．００５％とする。一方、０．６０％を超えると冷間加工性の低下、靭性の低下が生じるため、０．６０％を上限とする。
Ｓｉ：０．５０％以下
Ｓｉは、製鋼時の脱酸材として及び固溶体硬化による最終製品の強度増加目的に添加されるが、多量に添加すると強度アップが著しくなって靭性の劣化を招くため、上限を０．５０％とする。
Ｍｎ：０．２０〜１.００％
Ｍｎは、鋼材の焼入れ性を高め強度を向上させる元素として添加されるが、その効果を発揮させるためには０．２０％以上含有させる必要がある。一方、添加量が過剰になると、冷間鍛造性や靭性の低下を招くため、上限は１．００％とする。
The steel wire rod according to the present invention contains 0.005 to 0.60% of C. When other elements are added in addition to C, Si: 0.50% or less, Mn: 0.20 to 1.00%, Al: 0.01 to 0.06%, P: 0.02% or less , S: 0.02% or less, N: 0.01% or less. The reasons for limiting the ranges of these elements are as follows.
C: 0.005 to 0.60%
C is prescribed | regulated by the intensity | strength calculated | required by the goods formed from the steel wire rod of this invention, such as a volt | bolt and a screw | thread. If less than 0.005%, the required strength cannot be obtained, so the lower limit is made 0.005%. On the other hand, if it exceeds 0.60%, the cold workability and toughness are reduced, so 0.60% is made the upper limit.
Si: 0.50% or less Si is added as a deoxidizing material during steelmaking and for the purpose of increasing the strength of the final product by solid solution hardening. However, if added in a large amount, the strength is significantly increased and the toughness is deteriorated. The upper limit is 0.50%.
Mn: 0.20 to 1.00%
Mn is added as an element that enhances the hardenability of the steel material and improves the strength, but in order to exert its effect, it is necessary to contain 0.20% or more. On the other hand, if the addition amount is excessive, cold forgeability and toughness are reduced, so the upper limit is made 1.00%.
Ａｌ：０．０１％〜０．０６％
Ａｌは、Ｎを固定して冷間鍛造中の動的歪時効を抑制し、変形抵抗を低減する効果がある。この効果を得るためには、少なくとも０．０１％含有させる必要がある。しかし、過剰に含有させると靭性を低下させるため、上限は０．０６％とする。
Ｐ：０．０２％以下、Ｓ：０．０２％以下
ＰとＳは、不可避的に含有される成分である。Ｐは鋼中で粒界偏析や中心偏析を起こし靭性を劣化させるため、０．０２％以下とする必要がある。Ｓは冷間加工において有害な元素であるため、０．０２％以下とする必要がある。
Ｎ：０．０１％以下
Ｎは、冷間鍛造中に動的歪時効を起こし変形抵抗の上昇と加工性能の低下を招く。よって、Ｎは０．０１％以下とする。
Al: 0.01% to 0.06%
Al has the effect of fixing N and suppressing dynamic strain aging during cold forging and reducing deformation resistance. In order to obtain this effect, it is necessary to contain at least 0.01%. However, the upper limit is set to 0.06% because the toughness is reduced if excessively contained.
P: 0.02% or less, S: 0.02% or less
P and S are components inevitably contained. P causes grain boundary segregation and center segregation in steel and deteriorates toughness, so it is necessary to make it 0.02% or less. Since S is a harmful element in cold working, it needs to be made 0.02% or less.
N: 0.01% or less
N causes dynamic strain aging during cold forging, leading to an increase in deformation resistance and a reduction in processing performance. Therefore, N is set to 0.01% or less.
本発明の鋼線材における基本的な化学成分組成は上記の通りであり、上記の組成の他に更に、Ｃｒ：１．５０％以下、Ｍｏ：０．５０％以下、Ｎｉ：１．００％以下、Ｖ：０．５０％以下、Ｂ：０．００５％以下、Ｔｉ：０．０５％以下よりなる群から選ばれる１種以上の元素を含有すると、焼入れ性の向上や、冷間鍛造の強度向上といった利点が得られる。
Ｃｒ：１．５０％以下、Ｍｏ：０．５０％以下、Ｎｉ：１．００％以下
Ｃｒ、ＭｏおよびＮｉは、焼入れ性を高めることに有効な元素である。しかし、過剰に含有させると延性の劣化を引き起こすため、上記範囲内に抑える。
Ｖ：０．５０％以下
Ｖは、析出強化を目的として添加しても良い。しかし、多量に添加すると、延性の劣化を引き起こすため、上記範囲内に抑える。
The basic chemical composition of the steel wire rod of the present invention is as described above. In addition to the above composition, Cr: 1.50% or less, Mo: 0.50% or less, Ni: 1.00% or less V: 0.50% or less, B: 0.005% or less, Ti: containing one or more elements selected from the group consisting of 0.05% or less, improving hardenability and strength of cold forging Advantages such as improvement are obtained.
Cr: 1.50% or less, Mo: 0.50% or less, Ni: 1.00% or less Cr, Mo and Ni are effective elements for improving the hardenability. However, if it is contained excessively, ductility is deteriorated, so it is suppressed within the above range.
V: 0.50% or less
V may be added for the purpose of precipitation strengthening. However, if added in a large amount, it causes deterioration of ductility, so it is suppressed within the above range.
Ｂ：０．００５０％以下、Ｔｉ：０．０５％以下
Ｂは焼き入れ性を向上させる元素であり、必要により添加しても良い。ただし、過剰に含有させると、靭性を劣化させるため上限を０．００５％とする。Ｔｉは固溶Ｎの固定による動的時効抑制効果によって、冷間鍛造時の変形抵抗低減に有効な元素であるため、必要により添加しても良い。但し、過剰に含有させると粗大なＴｉＮが析出し、この粗大なＴｉＮを起点とする割れが生じやすくなることから、上限を０．０５％とする。
B: 0.0050% or less, Ti: 0.05% or less B is an element that improves hardenability, and may be added if necessary. However, if excessively contained, the toughness is degraded, so the upper limit is made 0.005%. Ti is an element effective in reducing deformation resistance during cold forging due to the effect of suppressing dynamic aging by fixing solute N, and may be added as necessary. However, if it is contained excessively, coarse TiN precipitates and cracks starting from this coarse TiN are likely to occur, so the upper limit is made 0.05%.
以下、本発明を実施例によって更に詳細に説明するが、下記実施例は本発明を限定する性質のものではなく、前記の趣旨または後記の趣旨に特徴して適宜設計変更することはいずれも本発明の技術的範囲に含まれるものである。 Hereinafter, the present invention will be described in more detail with reference to examples. However, the following examples are not intended to limit the present invention, and any design changes may be made as appropriate in accordance with the above-described gist or the gist described below. It is included in the technical scope of the invention.
表１に示す成分の鋼を線材圧延し、表２の冷却速度および恒温保定時間を施すことによって、表２に示す線材組織とした。
この線材をＡＣ1点直下で迅速に球状化焼鈍（ＡＣ1点直下まで１５０℃／Ｈｒで昇温し、ＡＣ1点直下で１Ｈｒ保持した後、空冷）した。なお、表１中のＣｅｑ＝Ｃ％＋（１／３）Ｓｉ％＋（１／６）Ｍｎ％である。
The steels having the components shown in Table 1 were wire-rolled and subjected to the cooling rate and constant temperature holding time shown in Table 2 to obtain the wire structure shown in Table 2.
The wire was rapidly spheroidized and annealed immediately below the AC1 point (heated to 150 ° C./Hr immediately below the AC1 point, held at 1 Hr immediately below the AC1 point, and then air-cooled). In Table 1, Ceq = C% + (1/3) Si% + (1/6) Mn%.
これら球状化焼鈍後の線材から切り出したテストピース（円筒の直径ｄと高さの比：ｈ／ｄ＝１．５）を使用して、冷間据込み性試験を実施し、割れ、変形抵抗を測定した。冷間据込み性試験は、JCFCS-1980の基準に則って実施した。変形抵抗は圧縮率７０％、歪速度＝１０Ｓ−１の条件で測定した。なお、表２中のＣｅｑ＝Ｃ％＋（１／３）Ｓｉ％＋（１／６）Ｍｎ％である。
それらの結果から、迅速球状化焼鈍後の冷間鍛造性を判定した結果を表２に示す。表１において、鋼Ａ〜Ｅは、本願発明範囲内であるが、鋼Ｆは、ＣｒとＮｉが本願範囲よりも高い試料、鋼Ｇは、Ｃｒが高い試料である。
Using a test piece cut out from the wire after spheroidizing annealing (ratio of diameter d to height of cylinder: h / d = 1.5), a cold upsetting test was carried out, cracking, deformation resistance Was measured. The cold uptake test was conducted in accordance with JCFCS-1980 standards. Deformation resistance was measured under the conditions of a compression rate of 70% and a strain rate = 10S- 1 . In Table 2, Ceq = C% + (1/3) Si% + (1/6) Mn%.
Table 2 shows the results of determining the cold forgeability after rapid spheroidizing annealing from those results. In Table 1, steels A to E are within the scope of the present invention, but steel F is a sample in which Cr and Ni are higher than the scope of the present application, and steel G is a sample in which Cr is high.
表２に示す試料Ｎｏ.２、８、１４、２０、２６は、恒温保定時間が不足して変態が完了しておらず、マルテンサイト等の硬質組織が大量に発生している。このため球状化処理後の冷間鍛造時の変形抵抗が高くなり、本発明で規定する範囲外である。
表２に示す試料Ｎｏ.５、１１は、保定温度が４００℃を下回るため、マルテンサイトが大量に発生し、同一Ｃｅｑで比較した場合、球状化処理後の冷間鍛造時の変形抵抗が高い。よって、本発明で規定する範囲外である。
表２に示す試料Ｎｏ.１７、２３、２９は、保定温度が４００℃を下回るため、ベイナイトが７５面積％を上回り、同一Ｃｅｑで比較した場合、球状化処理後の冷間鍛造時の変形抵抗が高い。よって、本発明で規定する範囲外である。
表２に示す試料Ｎｏ.６、１２、１８、２４、３０は、冷速が２０℃／ｓ以下のため、フェライトとパーライトの２相組織となり短時間では球状化が不十分である。このため、球状化処理後の冷間鍛造時の加工性能が低く、本発明で規定する範囲外である。
In Sample Nos. 2, 8, 14, 20, and 26 shown in Table 2, the constant temperature holding time is insufficient and the transformation is not completed, and a large amount of hard structure such as martensite is generated. For this reason, the deformation resistance at the time of cold forging after the spheroidizing treatment is increased, and is outside the range specified in the present invention.
Sample Nos. 5 and 11 shown in Table 2 have a retention temperature lower than 400 ° C., so a large amount of martensite is generated. When compared with the same Ceq, the deformation resistance during cold forging after spheroidization is high. . Therefore, it is outside the range defined by the present invention.
Sample Nos. 17, 23, and 29 shown in Table 2 have a holding temperature of less than 400 ° C., so that when bainite exceeds 75 area% and compared with the same Ceq, deformation resistance during cold forging after spheroidizing treatment Is expensive. Therefore, it is outside the range defined by the present invention.
Samples Nos. 6, 12, 18, 24, and 30 shown in Table 2 have a two-phase structure of ferrite and pearlite because the cold speed is 20 ° C./s or less, and spheroidization is insufficient in a short time. For this reason, the processing performance at the time of cold forging after the spheroidizing treatment is low, and is outside the range specified in the present invention.
試料Ｎｏ.３１〜３６は、Ｎｉが本発明で規定する範囲を超えて含まれるため、（擬似パーライト面積％＋ベイナイト面積％＋フェライト面積％）≧９０面積％とならない。これはマルテンサイトが多量に発生しているからである。同等Ｃｅｑで比較（Ｄ鋼）した場合、球状化処理後の冷間鍛造時の変形抵抗が高く、本発明で規定する範囲外である。
試料Ｎｏ.３７〜４１は、Ｃｒが本発明で規定する範囲を超えているために（擬似パーライト面積％＋ベイナイト面積％＋フェライト面積％）≧９０面積％とならない。これはマルテンサイトが多量に発生しているからである。同等Ｃｅｑで比較（Ｄ鋼）した場合、球状化処理後の冷間鍛造時の変形抵抗が高く、本発明で規定する範囲外である。
表２に示す試料Ｎｏ.４２は、Ｃｒが本発明で規定する範囲を超えて含まれるため、ベイナイト率が７５面積％を上回る。同等Ｃｅｑで比較（Ｃ鋼）した場合、冷間鍛造時の変形抵抗が高く、本発明で規定する範囲外である。
表２に示す上記以外の試料Ｎｏ.１、３、４、７、９，１０、１３、１５、１６、１９、２１、２２、２５、２７、２８は、本発明で規定する条件を満足する。迅速な球状化焼鈍時間後も、加工性能が高く、変形抵抗が低いという特性を有している。
これら以外の各実施例に相当する試料は本発明で規定する条件を満足する。迅速な球状化焼鈍時間後も加工性能が高く、変形抵抗が低いという特性を有している。
In Sample Nos. 31 to 36, since Ni exceeds the range defined in the present invention, (pseudo pearlite area% + bainite area% + ferrite area%) ≧ 90 area% is not satisfied. This is because a lot of martensite is generated. When compared with equivalent Ceq (steel D), the deformation resistance during cold forging after spheroidization is high, and is outside the range specified in the present invention.
In Sample Nos. 37 to 41, Cr exceeds the range specified in the present invention (pseudo pearlite area% + bainite area% + ferrite area%) ≧ 90 area%. This is because a lot of martensite is generated. When compared with equivalent Ceq (steel D), the deformation resistance during cold forging after spheroidization is high, and is outside the range specified in the present invention.
Sample No. 42 shown in Table 2 contains Cr exceeding the range specified in the present invention, and therefore the bainite ratio exceeds 75 area%. When compared with the equivalent Ceq (C steel), the deformation resistance at the time of cold forging is high, which is outside the range specified in the present invention.
Sample Nos. 1, 3, 4, 7, 9, 10, 13, 15, 16, 19, 21, 22, 25, 27, and 28 shown in Table 2 satisfy the conditions defined in the present invention. . Even after a rapid spheroidizing annealing time, it has the characteristics of high processing performance and low deformation resistance.
Samples corresponding to the examples other than these satisfy the conditions defined in the present invention. Even after a rapid spheroidizing annealing time, the processing performance is high and the deformation resistance is low.
Claims (4)
C: 0.005 to 0.6% (mass%, hereinafter the same), pseudo pearlite is 10 area% or more, bainite is 75 area% or less, ferrite is 60 area% or less, (pseudo pearlite area% + bainite area) % + Ferrite area%) ≧ 90 area% satisfying the relationship of ≧ 90 area%, in the production of a steel wire rod excellent in cold forgeability after spheroidizing treatment, after hot rolling, it is taken up at 750 to 1000 ° C. After cooling from 750 to 1000 ° C. to 400 to 550 ° C. at a rate of 20 ° C./s or more, holding at 400 to 550 ° C. for 20 seconds or more, completing the isothermal transformation, and then cooling to form a spherical shape The manufacturing method of the steel wire excellent in the cold forgeability after the spheroidization process characterized by shortening the annealing time after forming.
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| JP2005039498A JP4669300B2 (en) | 2005-02-16 | 2005-02-16 | Steel wire rod excellent in cold forgeability after spheroidizing treatment and method for producing the same |
| CNB2006800017203A CN100494450C (en) | 2005-02-16 | 2006-02-14 | Hot rolled wire material, steel wire and method for production thereof |
| PCT/JP2006/302539 WO2006088019A1 (en) | 2005-02-16 | 2006-02-14 | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
| TW95104915A TWI318645B (en) | 2005-02-16 | 2006-02-14 | Hot rolled steel wire material having superior processability for cold forgine after spheroidization, spheroidized steel wire having superior processability for cold forgine and methods for manufacturing the same |
| KR20077015015A KR101033752B1 (en) | 2005-02-16 | 2006-02-14 | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
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| Publication number | Publication date |
|---|---|
| CN100494450C (en) | 2009-06-03 |
| JP4669300B2 (en) | 2011-04-13 |
| CN101098979A (en) | 2008-01-02 |
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