JP3176465B2 - Manufacturing method of hypereutectoid steel wire - Google Patents
Manufacturing method of hypereutectoid steel wireInfo
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- JP3176465B2 JP3176465B2 JP01477793A JP1477793A JP3176465B2 JP 3176465 B2 JP3176465 B2 JP 3176465B2 JP 01477793 A JP01477793 A JP 01477793A JP 1477793 A JP1477793 A JP 1477793A JP 3176465 B2 JP3176465 B2 JP 3176465B2
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- steel
- cooling rate
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- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、スティールコード、ビ
ードワイヤなど細径高強度鋼線の製造に供される過共析
鋼線材の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a hypereutectoid steel wire used for producing a small diameter high strength steel wire such as a steel cord or a bead wire.
【０００２】[0002]
【従来の技術】高炭素鋼線の強度を上げる方策として、
Ｃ含有率を上げることは、安価で高い効果が得られるた
め工業的には最も望ましい方法である。しかし、過共析
領域、すなわち、通常Ｃが０．９％を越える領域では、
熱間圧延後の線材には旧オーステナイト粒界に沿って脆
い初析セメンタイトがネットワーク状に生成する。この
ため、圧延後の線材をそのまま伸線加工した場合、初析
セメンタイトに沿って粒界割れが発生するため断線が頻
発する。2. Description of the Related Art As a measure for increasing the strength of a high carbon steel wire,
Increasing the C content is the most industrially desirable method because it is inexpensive and has a high effect. However, in the hypereutectoid region, that is, the region where C usually exceeds 0.9%,
In the wire after hot rolling, brittle proeutectoid cementite is formed in a network along the old austenite grain boundaries. For this reason, if the wire rod after rolling is drawn as it is, breakage occurs frequently due to generation of grain boundary cracks along the pro-eutectoid cementite.
【０００３】従来、過共析鋼の伸線加工性を向上させる
熱処理方法が開発されている。たとえば、特公昭５６−
８８９３号公報には、熱処理により組織を粒状セメンタ
イトが分散したパーライト組織に変える方法が開示され
ている。これは、過共析鋼線をオーステナイト化し、油
焼き入れ処理してマルテンサイト組織とした後、７７０
〜９３０℃の温度域に急速加熱して粒状セメンタイトを
析出せしめ、目標加熱温度に到達後直ちに５３５〜６６
０℃の温度でパテンティング処理する方法である。この
方法は、伸線加工限界を高める方法としてはすぐれてい
るが、熱処理工程が複雑となるため線材圧延後の直接熱
処理に適用することは困難である。Conventionally, a heat treatment method has been developed to improve the drawability of hypereutectoid steel. For example,
No. 8993 discloses a method of changing the structure to a pearlite structure in which granular cementite is dispersed by heat treatment. This is because a hypereutectoid steel wire is austenitized and then oil quenched to obtain a martensite structure, and then 770
To 930 ° C. to rapidly precipitate granular cementite, and immediately after reaching the target heating temperature, 535 to 66 ° C.
This is a method of performing a patenting process at a temperature of 0 ° C. Although this method is excellent as a method for raising the drawing limit, it is difficult to apply it to direct heat treatment after wire rolling because the heat treatment process becomes complicated.
【０００４】[0004]
【発明が解決しようとする課題】このように、従来技術
では、熱間圧延後の過共析鋼線材をそのまま伸線加工に
供することは不可能であった。本発明の目的は、過共析
鋼線材の粒界初析セメンタイトの生成を完全に阻止する
ことにより、熱間圧延ままの状態の過共析鋼線材に高減
面率の伸線加工を付与することを可能ならしめる方法を
提供する。As described above, according to the prior art, it was impossible to directly use the hypereutectoid steel wire after hot rolling for wire drawing. An object of the present invention is to completely prevent the generation of grain boundary pro-eutectoid cementite in a hypereutectoid steel wire, thereby giving a high elongation wire drawing process to the hypereutectoid steel wire in a hot-rolled state. Provide a way to make it possible.
【０００５】[0005]
【課題を解決するための手段および作用】すなわち、本
発明の要旨は、 （１）質量比で Ｃ：０．９０〜１．１０％、 Ｓｉ：０．１５〜０．５０％、 Ｍｎ：０．３０〜０．６０％、 残余をＦｅおよび不可避的不純物からなる鋼を線材圧延
後、７５０〜９５０℃で巻取り、その後沸騰水中で巻取
温度から５５０℃までの温度範囲を（１）式で規定され
る範囲の冷却速度で冷却することにより初析セメンタイ
トを含まない微細パーライト組織とすることを特徴とす
る過共析鋼線材の製造方法。The gist of the present invention is as follows: (1) C: 0.90 to 1.10%, Si: 0.15 to 0.50%, Mn: 0 by mass ratio .30 to 0.60%, balance of steel consisting of Fe and inevitable impurities is rolled, then wound at 750 to 950 ° C., and then the temperature range from the winding temperature to 550 ° C. in boiling water is expressed by equation (1). A method for producing a hypereutectoid steel wire, characterized in that a fine pearlite structure not containing proeutectoid cementite is obtained by cooling at a cooling rate in the range specified in (1).
【０００６】 Ｙ≦０．１６ｌｏｇＸ＋０．８２ （１） ただし、Ｙは鋼のＣ含有率（％）、Ｘは冷却速度（℃／
sec)を示す。Y ≦ 0.16 log X + 0.82 (1) where Y is the C content (%) of steel, and X is the cooling rate (° C. /
sec).
【０００７】（２）質量比で Ｃ：０．９０〜１．１０％、 Ｓｉ：０．１５〜０．５０％、 Ｍｎ：０．３０〜０．６０％、 Ｃｒ：０．１０〜０．５０％、残余をＦｅおよび不可避的不純物からなる鋼を線材圧延
後、７５０〜９５０℃で巻取り、その後沸騰水中で巻取
温度から５５０℃までの温度範囲を上記（１）式で規定
される範囲の冷却速度で冷却することにより初析セメン
タイトを含まない微細パーライト組織とすることを特徴
とする過共析鋼線材の製造方法である。 [0007] (2) in a weight ratio C: 0.90~1.10%, Si: 0.15~0.50 %, Mn: 0.30~0.60%, Cr: 0.10~0. Wire rod rolling of steel consisting of 50%, the balance being Fe and unavoidable impurities
After that, wind at 750-950 ° C, then wind in boiling water
The temperature range from the temperature to 550 ° C is defined by the above formula (1).
Proeutectoid cement by cooling at a cooling rate
Features a fine pearlite structure that does not contain tight
This is a method for producing a hypereutectoid steel wire rod.
【０００８】以下に、本発明を詳細に説明する。本発明
者らは、過共析鋼の伸線加工性を改善すべく多くの実験
を行ない、以下に示すように、オーステナイト化温度か
らの冷却条件を選ぶことにより、初析セメンタイトの生
成を阻止できるという新たな知見を得た。すなわち、本
発明者らは、表１に示す組成の真空溶解鋼を熱間圧延し
た線材より、直径３mm、高さ１０mmの円柱状試料を製作
し、これをＡｒガス中で９５０〜１０００℃に誘導加熱
してオーステナイト化したのち、種々の冷却速度で連続
冷却した。Hereinafter, the present invention will be described in detail. The present inventors conducted many experiments to improve the drawability of hypereutectoid steel, and as shown below, prevented the formation of proeutectoid cementite by selecting cooling conditions from the austenitizing temperature. I got new knowledge that I can do it. That is, the present inventors manufactured a cylindrical sample having a diameter of 3 mm and a height of 10 mm from a wire rod obtained by hot rolling a vacuum-melted steel having a composition shown in Table 1 and then heating it to 950 to 1000 ° C. in Ar gas. After induction heating to austenitize, continuous cooling was performed at various cooling rates.
【０００９】[0009]
【表１】 [Table 1]
【００１０】冷却後の試料を研磨し、ＪＩＳ Ｇ０５５
１に規定された方法でエッチングしたのち光学顕微鏡に
より初析セメンタイトの生成状況を調べた。また、粒界
の薄いフイルム状セメンタイトの生成状況は、研磨後の
試料をピクラールでエッチングしたのち走査型電子顕微
鏡をもちいて観察した。図１に、初析セメンタイトの発
生限界とＣ含有率ならびに冷却速度の関係を示す。この
ように、初析セメンタイトの生成はＣ含有率以外に冷却
速度にも依存し、同一Ｃ含有率でも冷却速度を上げるこ
とによりその生成を防ぐことができる。図１より、初析
セメンタイトの発生しない条件を鋼のＣ含有率とオース
テナイト域からの冷却速度で表すと、次式（１）のよう
になる。[0010] The cooled sample is polished, and is subjected to JIS G055.
After etching by the method specified in No. 1, the state of formation of proeutectoid cementite was examined by an optical microscope. The state of formation of the film-like cementite having a thin grain boundary was observed using a scanning electron microscope after etching the polished sample with picral. FIG. 1 shows the relationship between the generation limit of proeutectoid cementite, the C content, and the cooling rate. As described above, the formation of proeutectoid cementite depends on the cooling rate in addition to the C content, and the formation can be prevented by increasing the cooling rate even at the same C content. From FIG. 1, the condition in which proeutectoid cementite does not occur is represented by the following equation (1) when the C content of steel and the cooling rate from the austenite region are expressed.
【００１１】 Ｙ≦０．１６ｌｏｇＸ＋０．８２ （１） ただし、Ｙは鋼のＣ含有率（％）、Ｘは冷却速度（℃／
sec)をしめす。熱間圧延後の線材を冷却するにあたって
は、（１）式を満足する条件を選べば初析セメンタイト
の発生を防止できる。また、初析セメンタイトの生成す
る温度範囲は、Ｆｅ−Ｃ系平衡状態図のＡcm点以下、Ｔ
ＴＴ線図のノーズ（Ｎｏｓｅ）温度以上と考えてよいた
め、本発明鋼では８５０℃以下５５０℃以上の温度範囲
で（１）式を満足すれば良い。Y ≦ 0.16 log X + 0.82 (1) where Y is the C content (%) of the steel, and X is the cooling rate (° C. /
sec). In cooling the wire rod after hot rolling, if conditions satisfying the expression (1) are selected, the generation of proeutectoid cementite can be prevented. The temperature range in which proeutectoid cementite is formed is below the A cm point in the Fe-C system equilibrium diagram,
Since the temperature may be considered to be equal to or higher than the nose temperature of the TT diagram, the steel of the present invention only needs to satisfy the expression (1) in a temperature range of 850 ° C. to 550 ° C.
【００１２】線材圧延後の巻取温度に関しては、巻取温
度が９５０℃を超えた場合、オーステナイト粒の粗大化
が進行し、線材の絞り値が低下し伸線初期に断線しやす
くなる。一方、巻取温度が７５０℃未満の場合、パーラ
イトの層状構造の発達が不十分となるため伸線加工限界
が低下する。以上の理由により巻取温度は７５０〜９５
０℃とする必要がある。Regarding the winding temperature after wire rolling, if the winding temperature exceeds 950 ° C., the austenite grains become coarser, the drawing value of the wire is reduced, and the wire tends to break at the beginning of drawing. On the other hand, if the winding temperature is lower than 750 ° C., the development of the layer structure of pearlite becomes insufficient, and the drawing limit is lowered. For the above reasons, the winding temperature is 750 to 95
It must be 0 ° C.
【００１３】本発明者らは、（１）式の冷却速度を満足
させるための冷媒として沸騰水が好適であることを見い
だした。沸騰水中に赤熱線材を浸漬した場合、線材表面
に薄い蒸気皮膜が形成され、この蒸気皮膜を介して熱伝
達が行われるため、マルテンサイトが発生することなく
空冷の場合より大きい冷却速度が得られる。沸騰水の温
度は、９６℃以上が望ましいが、実際操業では圧延線材
の保有熱により水温が上昇するため常に沸騰状態が保た
れる。The present inventors have found that boiling water is suitable as a refrigerant for satisfying the cooling rate of the formula (1). When the glowing wire is immersed in boiling water, a thin vapor film is formed on the surface of the wire, and heat is transferred through this vapor film, so that a higher cooling rate than in the case of air cooling can be obtained without generating martensite. . The temperature of the boiling water is desirably 96 ° C. or higher. However, in actual operation, the boiling temperature is always maintained because the water temperature rises due to the retained heat of the rolled wire.
【００１４】次に、本発明の成分限定理由について説明
する。Ｃは強度を上げるための有効かつ経済的な元素で
あり、本発明の最も重要な元素の一つである。Ｃ含有率
を上げるに伴ない、パテンティング後の強度ならびに伸
線時の加工硬化量が増大する。したがって、伸線加工に
より高強度鋼線を得るためには、Ｃ含有量は高い方が有
利であり、本発明では、０．９０％以上とする。一方、
Ｃ含有率が１．１０％を超した場合、（１）式が示すよ
うに、初析セメンタイトの発生を防止するために必要な
冷却速度は５６℃／sec を超えるため、沸騰水冷却では
実現が困難となる。したがって、Ｃ含有率の上限は１．
１０％とする。Next, the reasons for limiting the components of the present invention will be described. C is an effective and economical element for increasing the strength, and is one of the most important elements of the present invention. As the C content is increased, the strength after patenting and the amount of work hardening during drawing are increased. Therefore, in order to obtain a high-strength steel wire by drawing, it is advantageous that the C content is high, and in the present invention, the C content is set to 0.90% or more. on the other hand,
When the C content exceeds 1.10%, the cooling rate required to prevent the generation of pro-eutectoid cementite exceeds 56 ° C./sec, as shown by the equation (1). Becomes difficult. Therefore, the upper limit of the C content is 1.
10%.
【００１５】Ｓｉは脱酸剤として０．１５％以上添加す
る。一方、Ｓｉは合金元素として、フェライトに固溶し
て顕著な固溶強化作用を示す。また、フェライト中のＳ
ｉは伸線後の溶融亜鉛めっきやブルーイング時の強度低
下を低減させる効果を有するため、高強度鋼線の製造に
は不可欠な元素である。しかし、Ｓｉはベイナイトの生
成を助長し、伸線加工性を低下させるため０．５％を上
限とする。Si is added in an amount of 0.15% or more as a deoxidizing agent. On the other hand, Si, as an alloy element, forms a solid solution in ferrite and exhibits a remarkable solid solution strengthening action. In addition, S in ferrite
i is an indispensable element in the production of high-strength steel wires because it has the effect of reducing the strength reduction during hot-dip galvanizing after drawing and bluing. However, Si promotes the formation of bainite and lowers the drawability by 0.5% in order to lower the drawability.
【００１６】Ｍｎも脱酸剤として０．３％以上添加す
る。また、Ｍｎは焼入れ性向上効果が大きいため、線径
が大きい場合には、Ｍｎ含有率を上げることにより断面
内の均一性を高めることが可能であり、伸線後の鋼線の
延性向上に有効である。しかし、０．６０％を超える
と、沸騰水中での連続冷却中に中心偏析部にマルテンサ
イトが生成し、伸線加工性が劣化するため、０．６０％
を上限とする。Mn is also added as a deoxidizing agent in an amount of 0.3% or more. In addition, since Mn has a large effect of improving hardenability, when the wire diameter is large, it is possible to increase the Mn content to improve the uniformity in the cross section, and to improve the ductility of the steel wire after drawing. It is valid. However, when the content exceeds 0.60%, martensite is generated in the central segregation portion during continuous cooling in boiling water, and wire drawing workability is deteriorated.
Is the upper limit.
【００１７】Ｃｒはパーライトのラメラー間隔を低減
し、鋼線の強度と伸線加工性を向上させるため、必要に
応じて０．１０％以上添加する。０．１０％未満ではそ
の効果が十分でなく、一方、０．５０％を超えると変態
に要する時間が長くなり、沸騰水冷却中にマルテンサイ
トが生成し伸線性が著しく低下するため、０．５０％を
上限とする。Cr is added in an amount of 0.10% or more as necessary to reduce the lamellar spacing of pearlite and improve the strength and drawability of the steel wire. If it is less than 0.10%, the effect is not sufficient, while if it exceeds 0.50%, the time required for transformation becomes longer, martensite is formed during boiling water cooling, and the drawability is significantly reduced. The upper limit is 50%.
【００１８】[0018]
【実施例】以下、引張強さ１２０kgf ／mm2 以上、伸線
加工限界９０％以上を有する高強度鋼線材の製造結果に
ついて説明する。表２および３に示す化学成分の直径
５．５mmの線材を熱間圧延後沸騰水中で冷却し、そのま
ま伸線限界まで伸線した。DESCRIPTION OF THE PREFERRED EMBODIMENTS The production results of a high-strength steel wire having a tensile strength of 120 kgf / mm 2 or more and a wire drawing limit of 90% or more will be described below. A wire rod having a diameter of 5.5 mm having the chemical components shown in Tables 2 and 3 was cooled in boiling water after hot rolling, and was drawn as it was to the drawing limit.
【００１９】[0019]
【表２】 [Table 2]
【００２０】[0020]
【表３】 [Table 3]
【００２１】Ａ鋼はＣ量が０．９０％未満であるため目
標強度に未達である。一方、Ｉ鋼は高いＣ量に見合った
冷却速度が得られなかったため初析セメンタイトが生成
し、このため伸線性が大幅に劣化した。Ｂ−４およびＨ
−４鋼も冷却速度が（１）式を満足しなかったため、初
析セメンタイトが生成し伸線加工性が劣化し、早期に断
線した。Ｂ−２およびＨ−２鋼は巻取温度が９５０℃を
超えたため絞りが低下し、このため伸線限界は低い。Ｂ
−３およびＨ−３鋼は巻取温度が７５０℃未満であった
ため、絞りが比較的高いにもかかわらず伸線加工性は低
い。Ｃ鋼およびＧ鋼は中心偏析部にマルテンサイトが生
成したため絞りおよび伸線限界ともに低下した。Ｂ−５
およびＨ−５鋼は従来法で、いずれも線材圧延後の冷却
速度が（１）式を満足していないため初析セメンタイト
が生成し、このため伸線加工性が著しく低い。これに対
して、本発明法で製造された線材は、いずれも目標とす
る強度および伸線加工性を十分満足している。Steel A has not reached the target strength because the C content is less than 0.90%. On the other hand, in steel I, a proeutectoid cementite was formed because a cooling rate corresponding to a high C content was not obtained, and thus the drawability was significantly deteriorated. B-4 and H
Since the cooling rate of steel No. 4 also did not satisfy the expression (1), proeutectoid cementite was formed, the wire drawing workability was deteriorated, and the wire was broken early. For the B-2 and H-2 steels, since the winding temperature exceeded 950 ° C., the drawing was reduced, and thus the drawing limit was low. B
Since the winding temperature of -3 and H-3 steels was less than 750 ° C, the drawability was low despite the relatively high drawing. In steels C and G, martensite was generated in the center segregation part, and both the drawing and the drawing limit were lowered. B-5
For the H-5 and H-5 steels, the cooling rate after wire rolling does not satisfy the formula (1), so that proeutectoid cementite is formed, and therefore the drawability is extremely low. On the other hand, the wires produced by the method of the present invention sufficiently satisfy the target strength and drawability.
【００２２】[0022]
【発明の効果】以上説明したように、本発明法によれ
ば、従来法より強度が高く、かつ、伸線加工性に優れた
過共析鋼線材を製造することが可能となる。As described above, according to the method of the present invention, it becomes possible to produce a hypereutectoid steel wire having higher strength than the conventional method and excellent in drawability.
【図１】初析セメンタイトの発生限界とＣ含有率ならび
に冷却速度の関係を示す図である。FIG. 1 is a view showing the relationship between the generation limit of proeutectoid cementite, the C content, and the cooling rate.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平４−314829（ＪＰ，Ａ) 特開 平４−289127（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 8/06,9/52 C22C 38/00,38/04 ────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-4-314829 (JP, A) JP-A-4-289127 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C21D 8 / 06,9 / 52 C22C 38 / 00,38 / 04
Claims (2)
後、７５０〜９５０℃で巻取り、その後沸騰水中で巻取
温度から５５０℃までの温度範囲を（１）式で規定され
る範囲の冷却速度で冷却することにより初析セメンタイ
トを含まない微細パーライト組織とすることを特徴とす
る過共析鋼線材の製造方法。 Ｙ≦０．１６ｌｏｇＸ＋０．８２ （１） ただし、Ｙは鋼のＣ含有量（％）、Ｘは冷却速度（℃／
ｓｅｃ）を示す。1. A mass ratio of C: 0.90 to 1.10%, Si: 0.15 to 0.50%, Mn: 0.30 to 0.60%, the balance being Fe and unavoidable impurities After rolling the wire, the steel is rolled at 750 to 950 ° C., and then the temperature range from the winding temperature to 550 ° C. in boiling water is cooled at a cooling rate in the range defined by the formula (1) to thereby reduce proeutectoid cementite. A method for producing a hypereutectoid steel wire having a fine pearlite structure that does not contain any. Y ≦ 0.16 log X + 0.82 (1) where Y is the C content (%) of the steel, and X is the cooling rate (° C. /
sec).
後、７５０〜９５０℃で巻取り、その後沸騰水中で巻取
温度から５５０℃までの温度範囲を（１）式で規定され
る範囲の冷却速度で冷却することにより初析セメンタイ
トを含まない微細パーライト組織とすることを特徴とす
る過共析鋼線材の製造方法。 Ｙ≦０．１６ｌｏｇＸ＋０．８２ （１） ただし、Ｙは鋼のＣ含有量（％）、Ｘは冷却速度（℃／
ｓｅｃ）を示す。 2. Mass ratio of C: 0.90 to 1.10%, Si: 0.15 to 0.50%, Mn: 0.30 to 0.60%, Cr: 0.10 to 0.50 %, With the balance being Fe and unavoidable impurities, wire rod rolling
After that, wind at 750-950 ° C, then wind in boiling water
The temperature range from temperature to 550 ° C is defined by equation (1).
Cooling at a cooling rate in the range of
A fine pearlite structure that does not contain
Method for producing a hypereutectoid steel wire rod. Y ≦ 0.16 log X + 0.82 (1) where Y is the C content (%) of the steel, and X is the cooling rate (° C. /
sec).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP01477793A JP3176465B2 (en) | 1993-02-01 | 1993-02-01 | Manufacturing method of hypereutectoid steel wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP01477793A JP3176465B2 (en) | 1993-02-01 | 1993-02-01 | Manufacturing method of hypereutectoid steel wire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06228657A JPH06228657A (en) | 1994-08-16 |
| JP3176465B2 true JP3176465B2 (en) | 2001-06-18 |
Family
ID=11870490
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP01477793A Expired - Lifetime JP3176465B2 (en) | 1993-02-01 | 1993-02-01 | Manufacturing method of hypereutectoid steel wire |
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| Country | Link |
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| JP (1) | JP3176465B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0873932A (en) * | 1994-09-02 | 1996-03-19 | Metal Art:Kk | Method for heat-treating steel for machine structure |
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1993
- 1993-02-01 JP JP01477793A patent/JP3176465B2/en not_active Expired - Lifetime
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| JPH06228657A (en) | 1994-08-16 |
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