JP3599551B2 - Wire with excellent drawability - Google Patents
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- JP3599551B2 JP3599551B2 JP342098A JP342098A JP3599551B2 JP 3599551 B2 JP3599551 B2 JP 3599551B2 JP 342098 A JP342098 A JP 342098A JP 342098 A JP342098 A JP 342098A JP 3599551 B2 JP3599551 B2 JP 3599551B2
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【０００１】
【発明の属する技術分野】
本発明は、伸線加工性に優れた線材に関するものであり、詳細には所定の強度が要求されるばね，ワイヤロープ，高強度ボルト等に用いられる線材で、特に生引き性に優れた線材に関するものである。
【０００２】
【従来の技術】
ばね等の様に所定の強度が要求される線材には、熱間圧延によって５．０〜２５ｍｍφの線径に加工した後、制御冷却を施すことが一般的である。制御冷却された線材は、冷間での引き抜き加工による伸線と熱処理を繰り返すことでより細い線径に加工し、所定の製品形状に成形後、焼入れ・焼戻しを施し最終製品となる。従って、最終製品を製造するにあたり、熱間圧延後の線材を伸線加工性が優れている程、製造コストを容易に低減することが可能となる。
【０００３】
高強度鋼線材の伸線加工性を改善を図る技術としては、特公平７−１１０６０号公報に、Ｍｎ偏析帯の幅を制限した高強度鋼線材が開示されているが、伸線前に鉛パテンティング処理を施すことを前提としていることから、パテンティング処理を施さなくとも伸線加工性の高い、即ち生引き性に優れた線材の開発が要望されていた。
【０００４】
尚、生引き性を改善する手段としては、特開平８−２９５９３１号に、引張試験における真応力−歪み線図を利用して主体とする組織をベイナイトにする方法が開示されているが、生引き性の改善が不十分であった。
【０００５】
【発明が解決しようとする課題】
本発明は上記事情に着目してなされたものであって、熱間加工に続く伸線加工において、伸線加工性に優れ、特に生引き性に優れた線材を提供しようとするものである。
【０００６】
【課題を解決するための手段】
上記課題を解決した本発明の線材とは、質量％で、Ｃ：０．５０〜０．８０％，Ｓｉ：０．１５〜２．５０％，Ｍｎ：０．２０〜１．０％を含有し、残部Ｆｅ及び不可避不純物からなり、圧延材のパーライトノジュールサイズが１８μｍ以下であり、伸線圧延材の中心偏析度が１．１０以下であり、かつ圧延材のパーライト組織のラメラ間隔が１０００Å以下であることを要旨とするものである。
【０００８】
更にＣｒ：２．０％以下（０％を含まない）及び／又はＶ：０．２０％以下（０％を含まない）を含有させることが推奨される。
【０００９】
【発明の実施の形態】
本発明者らは前述の課題を解決することを目的として、生引き性に及ぼすパーライトノジュールの影響に関して研究を行った。その結果、パーライトノジュールが大きくなると、ノジュール界面の面積が小さくなり圧延材の延性が低下するため伸線加工性が劣化することを見出し、本発明に想到した。図１は、高強度鋼線材のパーライトノジュールサイズと生引き時の伸線限界減面率の関係を示すグラフである。パーライトノジュールサイズが１８μｍ以下では伸線限界減面率が８５％以上と非常に優れた生引き性を示すことが分かる。
【００１０】
尚、伸線加工性には、圧延材の中心偏析や、圧延材のパーライト組織のラメラ間隔も影響を及ぼすものである。圧延材の中心偏析度が１．１以下になると偏析によるミクロ的な脆化の程度が小さくなり、伸線中に発生する内部クラックの発生が抑制されて伸線加工性が改善されるので、圧延材の中心偏析度は１．１以下とすることが推奨される。また圧延材のパーライト組織のラメラ間隔が大き過ぎると圧延材の靭性が低下し、伸線中の内部クラックが発生し易くなるので、圧延材のパーライト組織のラメラ間隔は１０００Å以下とすることが望ましい。
以下、本発明の化学成分範囲の設定理由について説明する。
【００１１】
Ｃは、強度を上げるために有効な元素であり、ばね等として十分な強度を発揮させるには少なくとも０．５％が含有させることが望ましい。但し、多過ぎると靭性が低下するので、上限は０．８％とすることが好ましい。
【００１２】
Ｓｉは、鋼の脱酸のために必要な元素であり、脱酸効果を有効に発揮させるには０．１５％以上含有させることが望ましい。但し、過剰に添加すると延性が劣化するので上限は２．０％とすることが好ましい。
【００１３】
Ｍｎは、Ｓｉと同様、脱酸元素であると共に、鋼の焼入れ性を向上させてばね等として強度・靭性を確保するためには０．２０％以上添加することが望ましい。但し、Ｍｎ量が多過ぎると、Ｍｎの偏析部が形成され、マルテンサイトやベイナイト等の過冷組織が生成して伸線加工性が劣化するので、１．０％を上限とすることが好ましい。
【００１４】
Ｃｒは、パーライト組織を微細化し、靭性の改善に効果があるので含有させることが望ましい。但し、多量に添加すると、熱処理後のフェライト中の転移密度を上昇させ、伸線加工後の線の延性を改善するので、上限は２．０％とすることが好ましい。
【００１５】
Ｖはγ粒径を微細化し、靭性値を向上させるので添加することが望ましい。但し、０．２０％以上添加すると炭化物が生成し、析出され圧延材が硬化し靭性を劣化させるので、０．２０％を上限とすることが好ましい。
【００１６】
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・後記の主旨に徴して設計変更することはいずれも本発明の技術的範囲内に含まれるものである。
【００１７】
【実施例】
実施例１
Ｃ：０．５９％，Ｓｉ：１．３７％，Ｍｎ：０．６６％，Ｃｒ：０．６９％を含有し、残部Ｆｅ及び不可避不純物からなる鋼を用いて、１５５ｍｍ角のビレットを８５０〜１０００℃に加熱し、熱間圧延にて８ｍｍφに加工し、８００〜６００℃における冷却速度を約２〜３℃／ｓｅｃにて調整冷却し、表１に示すパーライトノジュールサイズの線材を作製した。尚、パーライトノジュールサイズは、線材の横断面を光学顕微鏡にて４００倍で視野内の０．１２５ｍｍ角中にあるパーライトノジュールの大きさ（長軸の長さ）を５個測定し、平均した値である。
上記線材をダイス角度１５度で乾式伸線し、カッピー断線した際の減面率を伸線限界減面率とした。結果は表１及び図１に示す。
【００１８】
【表１】
Ｎｏ．１〜３は本発明鋼であり、伸線限界減面率が大きく生引き性に優れている。一方、パーライトノジュールサイズが本発明範囲外である比較鋼Ｎｏ．４〜７はいずれも伸線限界減面率が小さく生引き性が劣っている。
【００２０】
実施例２
表２に示す化学成分で種々の中心偏析を持つ１５５ｍｍ角のビレットを８ｍｍφに熱間圧延し、調整冷却により表２に示す種々の微細構造（ノジュールサイズ，ラメラ間隔）を有するパーライトからなる線材を製造した。尚、熱間圧延時の加熱温度は、Ｎｏ．３０が１０００℃で、これ以外は９００℃であり、また熱間圧延後の冷却速度はＮｏ．２８が７．５℃／ｓｅｃで、Ｎｏ．２９が１．０℃／ｓｅｃであり、これ以外のＮｏ．１１〜２７及びＮｏ．３０〜３１の冷却速度は２．５℃／ｓｅｃであった。
【００２１】
線材の中心偏析は、線材の中心偏析部を横断する方向でＥＰＭＡによる線分析を行い、Ｃ濃度の最大濃化部（Ｃ１ ）を測定し、図２のＣ１ ／Ｃ０ をもって偏析度とした。
【００２２】
ラメラ間隔については、断面観察で測定される値は、パーライトの切断方向が必ずしもラメラの垂直方向ではないことから実際の間隔よりも大きくなる。そこでＳＥＭにて横断面を７０００倍程度で観察し、同一のラメラ間隔を呈している２０個のパーライトコロニーのラメラ間隔を、１サンプルに対して測定し、ラメラ間隔の大きさの順に図３に示す様に並べ、外挿直線を引き縦軸との交点を当該サンプルのラメラ間隔の値とした（尚、図３の例の場合、ラメラ間隔は７５０Åである）。
上記線材をダイス角度１５度で乾式伸線し、カッピー断線した際の減面率を伸線限界減面率とした。結果は表２に示す。
【００２３】
【表２】
Ｎｏ．２０〜２７は、成分組成が本発明範囲をはずれている比較例であり、いずれも伸線減面率が小さく生引き性が劣っている。Ｎｏ．２８はラメラ間隔が大き過ぎる場合の比較例であり、Ｎｏ．２９は、パーライトノジュールサイズが大き過ぎ、Ｎｏ．３０は線材の中心偏析度が大き過ぎる場合の比較例であり、いずれも伸線限界減面率が小さく、生引き性が十分でない。
これに対して、本発明に係る要件を全て満足する本発明例Ｎｏ．１１〜１９は、伸線限界減面率が大きく、生引き性に優れている。
【００２５】
【発明の効果】
本発明は以上の様に構成されているので、熱間加工に続く伸線加工において、伸線加工性に優れ、特に生引き性に優れた線材が提供できることとなった。
【図面の簡単な説明】
【図１】高強度鋼線材のパーライトノジュールサイズと生引き時の伸線限界減面率の関係を示すグラフである。
【図２】中心偏析度の算出方法を示す説明図である。
【図３】ラメラ間隔の値の決定方法を示すグラフである。[0001]
TECHNICAL FIELD OF THE INVENTION
The present invention relates to a wire rod excellent in wire drawability, and more particularly to a wire rod used for a spring, a wire rope, a high-strength bolt, and the like, which require a predetermined strength, and in particular, a wire rod having excellent drawability. It is about.
[0002]
[Prior art]
Generally, a wire rod requiring a predetermined strength, such as a spring, is processed by hot rolling to a wire diameter of 5.0 to 25 mmφ, and then subjected to controlled cooling. The wire thus controlled and cooled is processed into a finer wire diameter by repeatedly drawing and heat-treating by cold drawing, and after being formed into a predetermined product shape, quenched and tempered to be a final product. Therefore, in manufacturing the final product, the higher the wire workability of the wire after hot rolling, the more easily the manufacturing cost can be reduced.
[0003]
As a technique for improving the drawability of a high-strength steel wire, Japanese Patent Publication No. 7-11060 discloses a high-strength steel wire in which the width of the Mn segregation zone is limited. Since it is premised that a patenting treatment is performed, there has been a demand for development of a wire rod having a high wire drawing workability, that is, excellent in the drawability, without performing the patenting treatment.
[0004]
As a means for improving the raw-drawing property, Japanese Patent Application Laid-Open No. 8-295931 discloses a method in which a main structure is made bainite using a true stress-strain diagram in a tensile test. The improvement in pullability was insufficient.
[0005]
[Problems to be solved by the invention]
The present invention has been made in view of the above circumstances, and an object of the present invention is to provide a wire excellent in wire drawing workability and particularly excellent in drawability in wire drawing after hot working.
[0006]
[Means for Solving the Problems]
The wire rod of the present invention that has solved the above-mentioned problems contains, by mass%, C: 0.50 to 0.80%, Si: 0.15 to 2.50%, and Mn: 0.20 to 1.0%. The balance consists of Fe and inevitable impurities, the pearlite nodule size of the rolled material is 18 μm or less, the center segregation degree of the drawn wire is 1.10 or less, and the lamella spacing of the pearlite structure of the rolled material is 1000 ° or less. The gist is that
[0008]
Further, it is recommended to contain Cr: 2.0% or less (excluding 0%) and / or V: 0.20% or less (excluding 0%).
[0009]
BEST MODE FOR CARRYING OUT THE INVENTION
The present inventors have conducted research on the effect of pearlite nodules on shrimpability for the purpose of solving the aforementioned problems. As a result, it has been found that when the pearlite nodule becomes large, the area of the nodule interface becomes small and the ductility of the rolled material is reduced, so that the wire drawing workability is deteriorated. FIG. 1 is a graph showing the relationship between the pearlite nodule size of a high-strength steel wire and the critical wire-drawing reduction rate during raw drawing. It can be seen that when the pearlite nodule size is 18 μm or less, the wire drawing limit area reduction rate is 85% or more, exhibiting extremely excellent raw-drawing properties.
[0010]
The drawability is affected by the center segregation of the rolled material and the lamella spacing of the pearlite structure of the rolled material. When the degree of center segregation of the rolled material is 1.1 or less, the degree of micro-brittleness due to segregation decreases, and the occurrence of internal cracks generated during drawing is suppressed, so that the wire drawing workability is improved. It is recommended that the center segregation degree of the rolled material be 1.1 or less. Further, if the lamella spacing of the pearlite structure of the rolled material is too large, the toughness of the rolled material is reduced, and internal cracks are easily generated during wire drawing. .
Hereinafter, the reason for setting the chemical component range of the present invention will be described.
[0011]
C is an element effective for increasing the strength, and is desirably contained at least 0.5% in order to exhibit sufficient strength as a spring or the like. However, if the content is too large, the toughness is reduced. Therefore, the upper limit is preferably set to 0.8%.
[0012]
Si is an element necessary for deoxidizing steel, and is desirably contained in an amount of 0.15% or more to effectively exhibit a deoxidizing effect. However, if added excessively, the ductility deteriorates, so the upper limit is preferably set to 2.0%.
[0013]
Like Mn, Mn is a deoxidizing element, and is preferably added in an amount of 0.20% or more in order to improve the hardenability of steel and secure strength and toughness as a spring or the like. However, if the amount of Mn is too large, a segregated portion of Mn is formed, and a supercooled structure such as martensite or bainite is generated to deteriorate wire drawing workability. Therefore, the upper limit is preferably 1.0%. .
[0014]
It is desirable to add Cr because it has a fine pearlite structure and is effective in improving toughness. However, when added in a large amount, the transition density in the ferrite after the heat treatment is increased and the ductility of the wire after the wire drawing is improved, so the upper limit is preferably set to 2.0%.
[0015]
V is desirably added because it refines the γ grain size and improves the toughness value. However, if added in an amount of 0.20% or more, carbides are generated, precipitated and the rolled material is hardened, and the toughness is deteriorated. Therefore, the upper limit is preferably set to 0.20%.
[0016]
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 change based on the gist of the preceding and following descriptions is not a technical limitation of the present invention. It is included in the range.
[0017]
【Example】
Example 1
Using steel containing 0.59% of C, 1.37% of Si, 0.66% of Mn, and 0.69% of Cr, the balance being Fe and unavoidable impurities, a billet of 155 mm square was 850-850 mm. It was heated to 1000 ° C., processed to 8 mmφ by hot rolling, and cooled at 800 to 600 ° C. at a cooling rate of about 2 to 3 ° C./sec to produce a pearlite nodule size wire rod shown in Table 1. The pearlite nodule size is a value obtained by measuring the size (length of major axis) of five pearlite nodules in a 0.125 mm square within the visual field at 400 times the cross section of the wire rod and averaging the results. It is.
The wire was dry-drawn at a die angle of 15 degrees, and the reduction in area at the time of cut-off at the cuppy was defined as the critical reduction in wire-drawing. The results are shown in Table 1 and FIG.
[0018]
[Table 1]
No. Nos. 1 to 3 are steels of the present invention, which have a large wire-drawing critical area reduction rate and are excellent in burrs. On the other hand, the comparative steel No. having a pearlite nodule size outside the range of the present invention was used. Each of Nos. 4 to 7 has a small wire-drawing limit area reduction rate and is inferior in the drawability.
[0020]
Example 2
A 155 mm square billet having various center segregations with the chemical components shown in Table 2 was hot-rolled to 8 mmφ, and a pearlite wire rod having various microstructures (nodule size, lamellar spacing) shown in Table 2 was obtained by controlled cooling. Manufactured. The heating temperature at the time of hot rolling is as follows. 30 was 1000 ° C., the others were 900 ° C., and the cooling rate after hot rolling was no. No. 28 was 7.5 ° C./sec. No. 29 was 1.0 ° C./sec. Nos. 11 to 27 and Nos. The cooling rate of 30 to 31 was 2.5 ° C / sec.
[0021]
The center segregation of the wire is performed by performing a line analysis by EPMA in a direction crossing the center segregation part of the wire, measuring the maximum concentrated portion (C 1 ) of C concentration, and determining the segregation degree by C 1 / C 0 in FIG. did.
[0022]
Regarding the lamella spacing, the value measured by cross-sectional observation is larger than the actual spacing because the cutting direction of the pearlite is not necessarily the vertical direction of the lamella. Then, the cross section was observed at about 7000 times by SEM, the lamella spacing of 20 pearlite colonies exhibiting the same lamella spacing was measured for one sample, and FIG. 3 shows in order of the size of the lamella spacing. The sample was arranged as shown, an extrapolated straight line was drawn, and the intersection with the vertical axis was taken as the value of the lamella interval of the sample (the lamella interval is 750 ° in the example of FIG. 3).
The wire was dry-drawn at a die angle of 15 degrees, and the reduction in area at the time of cut-off at the cuppy was defined as the critical reduction in wire-drawing. The results are shown in Table 2.
[0023]
[Table 2]
No. Nos. 20 to 27 are comparative examples in which the component composition is out of the range of the present invention, and all have low wire-drawing reduction rates and poor inferiority. No. No. 28 is a comparative example in which the lamella spacing is too large. In No. 29, the pearlite nodule size was too large.
On the other hand, the present invention example No. satisfying all the requirements according to the present invention. Nos. 11 to 19 have a large wire-drawing limit area reduction rate and are excellent in the drawability.
[0025]
【The invention's effect】
Since the present invention is configured as described above, it is possible to provide a wire excellent in wire drawing workability, and particularly excellent in raw drawability in wire drawing subsequent to hot working.
[Brief description of the drawings]
FIG. 1 is a graph showing the relationship between the pearlite nodule size of a high-strength steel wire and the critical wire-reduction rate during wire drawing.
FIG. 2 is an explanatory diagram showing a method of calculating a degree of center segregation.
FIG. 3 is a graph showing a method for determining a value of a lamella interval.
Claims (3)
Ｃ ：０．５０〜０．８０％，
Ｓｉ：０．１５〜２．５０％，
Ｍｎ：０．２０〜１．０％
を含有し、残部Ｆｅ及び不可避不純物からなり、
圧延材のパーライトノジュールサイズが１８μｍ以下であり、圧延材の中心偏析度が１．１０以下であり、かつ圧延材のパーライト組織のラメラ間隔が１０００Å以下であることを特徴とする生引き性に優れた線材。 In mass%,
C: 0.50 to 0.80%,
Si: 0.15 to 2.50%,
Mn: 0.20-1.0%
Containing the balance Fe and inevitable impurities,
The pearlite nodule size of the rolled material is 18 μm or less, the center segregation degree of the rolled material is 1.10 or less, and the lamellar spacing of the pearlite structure of the rolled material is 1000 ° or less. Wire rod.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP342098A JP3599551B2 (en) | 1998-01-09 | 1998-01-09 | Wire with excellent drawability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP342098A JP3599551B2 (en) | 1998-01-09 | 1998-01-09 | Wire with excellent drawability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11199977A JPH11199977A (en) | 1999-07-27 |
| JP3599551B2 true JP3599551B2 (en) | 2004-12-08 |
Family
ID=11556898
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP342098A Expired - Fee Related JP3599551B2 (en) | 1998-01-09 | 1998-01-09 | Wire with excellent drawability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3599551B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2824205A1 (en) * | 2012-03-07 | 2015-01-14 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Steel wire rod with excellent spring workability for high-strength spring, process for manufacturing same, and high-strength spring |
| US10385427B2 (en) | 2014-12-15 | 2019-08-20 | Nippon Steel Corporation | Wire rod |
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1998
- 1998-01-09 JP JP342098A patent/JP3599551B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2824205A1 (en) * | 2012-03-07 | 2015-01-14 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Steel wire rod with excellent spring workability for high-strength spring, process for manufacturing same, and high-strength spring |
| EP2824205A4 (en) * | 2012-03-07 | 2015-08-26 | Kobe Steel Ltd | Steel wire rod with excellent spring workability for high-strength spring, process for manufacturing same, and high-strength spring |
| US10385427B2 (en) | 2014-12-15 | 2019-08-20 | Nippon Steel Corporation | Wire rod |
| WO2022220238A1 (en) | 2021-04-15 | 2022-10-20 | 東京製綱株式会社 | Heat-treated steel material and heat treatment method for steel material |
| KR20230169306A (en) | 2021-04-15 | 2023-12-15 | 도쿄 세이꼬 가부시키가이샤 | Fresh material and manufacturing method of fresh material |
| KR20230170753A (en) | 2021-04-15 | 2023-12-19 | 도쿄 세이꼬 가부시키가이샤 | Heat treatment steel and heat treatment methods for steel materials |
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| Publication number | Publication date |
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| JPH11199977A (en) | 1999-07-27 |
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