JP2001181793A - High strength directly patented wire rod and its manufacturing method - Google Patents
High strength directly patented wire rod and its manufacturing methodInfo
- Publication number
- JP2001181793A JP2001181793A JP37131299A JP37131299A JP2001181793A JP 2001181793 A JP2001181793 A JP 2001181793A JP 37131299 A JP37131299 A JP 37131299A JP 37131299 A JP37131299 A JP 37131299A JP 2001181793 A JP2001181793 A JP 2001181793A
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- Japan
- Prior art keywords
- steel
- mass
- layer
- wire according
- strength direct
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、高強度のＰＣ鋼
線、ＰＷＳ鋼線、ピアノ線、スチールコード、ホースワ
イヤ、ビードワイヤ、コントロールケーブル、釣り糸、
カットワイヤ、ソーワイヤなどに使用される高強度鋼線
を製造可能とする線材とその製造方法に関するものであ
る。The present invention relates to a high-strength PC steel wire, PWS steel wire, piano wire, steel cord, hose wire, bead wire, control cable, fishing line,
The present invention relates to a wire capable of manufacturing a high-strength steel wire used for a cut wire, a saw wire, and the like, and a method for manufacturing the same.
【０００２】[0002]
【従来の技術】一般にスチールコードなどに用いる０．
６％以上の炭素を含む高炭素鋼からなるワイヤは、熱間
圧延により直径５〜１６mmに加工された後に、調整冷却
により組織調整され線材とされる。一般に線材はコイル
状に巻き取られ搬送される。例えば、特開昭６０−２０
４８６５号公報には、Ｍｎ含有量を０．３％未満に規制
して鉛パテンティング後の過冷組織の発生を抑え、Ｃ，
Ｓｉ，Ｍｎ等の元素量を規制することによって、撚り線
時の断線が少なく高強度および高靱延性の極細線および
スチールコード用高炭素鋼線材が開示されており、ま
た、特開昭６３−２４０４６号公報には、Ｓｉ含有量を
１．００％以上とすることによって鉛パテンティング材
の引張強さを高くして伸線加工率を小さくした高靱性高
延性極細線用線材が開示されている。2. Description of the Prior Art Generally used for steel cords and the like.
A wire made of a high carbon steel containing 6% or more of carbon is worked into a wire having a diameter of 5 to 16 mm by hot rolling, and then the structure is adjusted by adjusting and cooling to obtain a wire. Generally, a wire is wound and transported in a coil shape. For example, JP-A-60-20
No. 4865 discloses that the Mn content is regulated to less than 0.3% to suppress the generation of a supercooled structure after lead patenting.
By regulating the amounts of elements such as Si and Mn, ultra-fine wires having high strength and high toughness and ductility, and high-carbon steel wires for steel cords are disclosed. Japanese Patent No. 24046 discloses a wire for high toughness and high ductility ultrafine wire in which the tensile strength of a lead patenting material is increased by setting the Si content to 1.00% or more to reduce the draw ratio. I have.
【０００３】このような高強度に用いられる線材は、伸
線工程で表面に付けられた疵により断線を引き起こしや
すい。このため、従来の線材では、輸送中やコイルの取
り扱い時に出来るだけ疵を付けない工夫がなされてい
た。しかし、このような努力にも限界があり、疵による
断線の起こらない線材が必要とされている。[0003] Such a wire used for high strength is liable to be broken due to flaws attached to the surface in the wire drawing process. For this reason, in the conventional wire rod, a device has been devised so as not to damage as much as possible during transportation or handling of the coil. However, there is a limit to such efforts, and there is a need for a wire that does not break due to flaws.
【０００４】[0004]
【発明が解決しようとする課題】本発明は上記課題を解
決するためになされたもので、熱間圧延された線材の搬
送あるいは表面処理加工過程で発生する疵に対する感受
性を低減し、疵に強い線材とその製造方法を提供する。SUMMARY OF THE INVENTION The present invention has been made in order to solve the above-mentioned problems, and has a reduced sensitivity to flaws generated in the process of transporting or surface-treating a hot-rolled wire, and is more resistant to flaws. A wire and a method for manufacturing the wire are provided.
【０００５】[0005]
【課題を解決するための手段】本発明の要旨は次のとお
りである。 （１）炭素含有量が質量％で０．７％以上を含有する高
炭素鋼で、その表層から３００μｍまでの平均炭素含有
量が全断面での平均炭素含有量の０．９７倍以下とする
ことにより、前記層が擦過マルテンサイト組織の生成し
難い層としたことを特徴とする高強度直接パテンティン
グ線材。The gist of the present invention is as follows. (1) High carbon steel having a carbon content of 0.7% or more by mass%, wherein the average carbon content from the surface layer to 300 μm is 0.97 times or less the average carbon content in the entire cross section. A high-strength direct patenting wire, characterized in that the layer is a layer in which a scratch martensite structure is hardly generated.
【０００６】（２）前記層内の平均ラメラ間隔が９５nm
以上であることを特徴とする上記（１）記載の高強度直
接パテンティング線材。 （３）前記高炭素鋼の鋼成分が、質量％で、Ｃ：０．７
〜１．２％、Ｓｉ：０．１〜１．５％、Ｍｎ：０．１〜
１．０％、残部Ｆｅおよび不可避不純物からなることを
特徴とする上記（１）または（２）記載の高強度直接パ
テンティング線材。(2) The average lamella spacing in the layer is 95 nm
The high-strength direct patenting wire according to the above (1), characterized in that: (3) The steel component of the high carbon steel is expressed by mass% and C: 0.7
-1.2%, Si: 0.1-1.5%, Mn: 0.1-
The high-strength direct patenting wire according to the above (1) or (2), comprising 1.0%, the balance being Fe and unavoidable impurities.
【０００７】（４）前記高炭素鋼の鋼成分が、更に質量
％で、Ｃｒ：０．１〜０．５％、Ｖ：０．００１〜０．
２％、Ｎｉ：０．０５〜１．０％、Ｍｏ：０．１〜０．
５％、の１種または２種以上を含有することを特徴とす
る上記（３）記載の高強度直接パテンティング線材。(4) The steel component of the high-carbon steel is further represented by mass%, Cr: 0.1 to 0.5%, V: 0.001 to 0.
2%, Ni: 0.05 to 1.0%, Mo: 0.1 to 0.
The high-strength direct patenting wire according to the above (3), characterized in that it contains 5% or more of one or more kinds.
【０００８】（５）前記高炭素鋼の鋼成分が、更に質量
％で、Ｃｕ：０．０５〜０．８％、Ｗ：０．０５〜０．
８％、Ｌａ：０．０００５〜０．０１％、Ｃｅ：０．０
００５〜０．０１％、の１種または２種以上を含有する
ことを特徴とする上記（３）または（４）記載の高強度
直接パテンティング線材。(5) The steel component of the high-carbon steel is further represented by mass%, Cu: 0.05-0.8%, W: 0.05-0.
8%, La: 0.0005 to 0.01%, Ce: 0.0
The high-strength direct patenting wire according to the above (3) or (4), comprising one or more of 005 to 0.01%.
【０００９】（６）前記高炭素鋼の鋼成分が、更に質量
％で、Ａｌ：０．００１〜０．０６％、Ｂ：０．０００
５〜０．０６％、Ｔｉ：０．００１〜０．０６％、Ｎ
ｂ：０．００１〜０．０６％、の１種または２種以上を
含有することを特徴とする上記（３）〜（５）のいずれ
かの項に記載の高強度直接パテンティング線材。(6) The steel component of the high-carbon steel is further expressed by mass%, Al: 0.001 to 0.06%, B: 0.000%
5 to 0.06%, Ti: 0.001 to 0.06%, N
b: The high-strength direct patenting wire according to any one of the above items (3) to (5), comprising one or more of 0.001 to 0.06%.
【００１０】（７）炭素含有量が質量％で０．７％以上
を含有する高炭素鋼を、線材加熱炉で１０００〜１２０
０℃で加熱後、直径４〜１６mmとする熱間圧延を行い、
７５０〜９００℃の温度で圧延を終了し、その後直ちに
４００〜５７０℃の溶融ソルトパスに浸漬してパーライ
ト変態を終了させることにより、その表層から３００μ
ｍまでの層の平均炭素含有量が全断面での平均炭素含有
量の０．９７倍以下で、前記層が擦過マルテンサイト組
織の生成し難い層としたことを特徴とする高強度直接パ
テンティング線材の製造方法。(7) A high-carbon steel having a carbon content of 0.7% by mass or more is produced in a wire heating furnace at 1000 to 120%.
After heating at 0 ° C., hot rolling to a diameter of 4 to 16 mm is performed,
The rolling is completed at a temperature of 750 to 900 ° C., and immediately thereafter, the pearlite transformation is completed by immersion in a molten salt pass at 400 to 570 ° C., so that 300 μ
m, wherein the average carbon content of the layers up to m is 0.97 times or less the average carbon content of the entire cross section, and said layer is a layer in which a scratch martensite structure is hardly generated. Wire rod manufacturing method.
【００１１】（８）前記層内の平均ラメラ間隔が９５nm
以上であることを特徴とする前記（７）記載の高強度直
接パテンティング線材の製造方法。 （９）前記熱間圧延を行い、その後、７５０〜９００℃
の温度で巻き取り、その後直ちに４００〜５７０℃の溶
融ソルトバスに浸漬することを特徴とする上記（７）ま
たは（８）記載の高強度直接パテンティング線材の製造
方法。(8) The average lamella spacing in the layer is 95 nm
(7) The method for producing a high-strength direct patenting wire according to the above (7). (9) The hot rolling is performed, and thereafter, 750 to 900 ° C.
The method for producing a high-strength direct patenting wire according to the above (7) or (8), wherein the wire is wound up at a temperature of immediately above and immediately immersed in a molten salt bath at 400 to 570 ° C.
【００１２】（１０）前記高炭素鋼の鋼成分が、質量％
で、Ｃ：０．７〜１．２％、Ｓｉ：０．１〜１．５％、
Ｍｎ：０．１〜１．０％、残部Ｆｅおよび不可避不純物
からなることを特徴とする上記（７）〜（９）のいずれ
かの項に記載の高強度直接パテンティング線材の製造方
法。(10) The steel component of the high carbon steel is
And C: 0.7 to 1.2%, Si: 0.1 to 1.5%,
The method for producing a high-strength direct patenting wire according to any one of the above items (7) to (9), comprising Mn: 0.1 to 1.0%, the balance being Fe and unavoidable impurities.
【００１３】（１１）前記高炭素鋼の鋼成分が、更に質
量％で、Ｃｒ：０．１〜０．５％、Ｖ：０．００１〜
０．２％、Ｎｉ：０．０５〜１．０％、Ｍｏ：０．１〜
０．５％、の１種または２種以上を含有することを特徴
とする上記（１０）記載の高強度直接パテンティング線
材の製造方法。(11) The steel component of the high-carbon steel further includes, by mass%, Cr: 0.1 to 0.5%, V: 0.001 to
0.2%, Ni: 0.05 to 1.0%, Mo: 0.1 to
(10) The method for producing a high-strength direct patenting wire according to the above (10), which comprises one or more of 0.5%.
【００１４】（１２）前記高炭素鋼の鋼成分が、更に質
量％で、Ｃｕ：０．０５〜０．８％、Ｗ：０．０５〜
０．８％、Ｌａ：０．０００５〜０．０１％、Ｃｅ：
０．０００５〜０．０１％、の１種または２種以上を含
有することを特徴とする上記（１０）または（１１）記
載の高強度直接パテンティング線材の製造方法。(12) The steel component of the high-carbon steel further includes, by mass%, Cu: 0.05 to 0.8% and W: 0.05 to
0.8%, La: 0.0005 to 0.01%, Ce:
The method for producing a high-strength direct patenting wire according to the above (10) or (11), comprising one or more of 0.0005 to 0.01%.
【００１５】（１３）前記高炭素鋼の鋼成分が、更に質
量％で、Ａｌ：０．００１〜０．０６％、Ｂ：０．００
０５〜０．０６％、Ｔｉ：０．００１〜０．０６％、Ｎ
ｂ：０．００１〜０．０６％、の１種または２種以上を
含有することを特徴とする上記（１０）〜（１２）のい
ずれかの項に記載の高強度直接パテンティング線材の製
造方法。(13) The steel component of the high-carbon steel is further represented by mass%, Al: 0.001 to 0.06%, B: 0.00
05-0.06%, Ti: 0.001-0.06%, N
b: production of a high-strength direct patenting wire according to any one of the above (10) to (12), wherein one or more of 0.001 to 0.06% is contained. Method.
【００１６】[0016]
【発明の実施の形態】まず、鋼成分の限定理由について
説明する。成分は全て質量％である。Ｃは強化に有効な
元素であり高強度の鋼線を得るためにはＣ量を０．７％
以上とすることが必要であるが、高すぎると初析セメン
タイトが析出しやすいため、延性が低下し、かつ伸線性
が劣化するのでその上限は１．２％とする。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS First, reasons for limiting steel components will be described. All components are% by weight. C is an effective element for strengthening. To obtain a high-strength steel wire, the amount of C must be 0.7%.
It is necessary to make the above, but if it is too high, the proeutectoid cementite is likely to precipitate, so that the ductility is lowered and the drawability is deteriorated. Therefore, the upper limit is set to 1.2%.
【００１７】Ｓｉは鋼の脱酸のために必要な元素であ
り、従ってその含有量があまりに少ないとき、脱酸効果
が不十分になるので０．１％以上添加する。また、Ｓｉ
は熱処理後に形成されるパーライト中のフェライト相に
固溶しパテンティング後の強度を上げるが、反面、熱処
理性を阻害するので１．５％以下とする。Ｍｎは鋼の焼
き入れ性を確保するために０．１％以上のＭｎを添加す
ることが望ましい。しかし、多量のＭｎの添加も溶融亜
鉛めっきの際の延性の回復を遅らすので１．０％以下と
する。Si is an element necessary for the deoxidation of steel. Therefore, when its content is too small, the deoxidizing effect becomes insufficient, so that 0.1% or more is added. In addition, Si
Is dissolved in the ferrite phase in the pearlite formed after heat treatment to increase the strength after patenting, but on the other hand, it impairs the heat treatment property, so that the content is 1.5% or less. As for Mn, it is desirable to add 0.1% or more Mn in order to secure the hardenability of steel. However, the addition of a large amount of Mn also delays the recovery of ductility during hot-dip galvanizing, so it is set to 1.0% or less.
【００１８】Ｃｒはパテンティング後の強度ならびに伸
線加工後の強度を向上するために添加する。従って、Ｃ
ｒの添加量はその効果が期待できる０．１％以上とし、
パテンティング時の変態遅延による熱処理性が悪化する
ことの無い０．５％以下とする。Ｖもパテンティング後
の強度ならびに伸線加工後の強度を向上するために添加
する。添加する場合は、その効果の表れる０．００１％
以上とし、添加し過ぎると変態が著しく遅れ、生産性に
影響を及ぼすので０．２％以下とする。Cr is added to improve the strength after patenting and the strength after wire drawing. Therefore, C
The added amount of r should be 0.1% or more where the effect can be expected,
The content is set to 0.5% or less so that the heat treatment property is not deteriorated due to the transformation delay during the patenting. V is also added to improve the strength after patenting and the strength after wire drawing. When added, 0.001% to show the effect
When the amount is too large, the transformation is significantly delayed, and the productivity is affected.
【００１９】Ｎｉもパテンティング後の強度ならびに伸
線加工後の強度を向上するために添加する。添加する場
合は、その効果の表れる０．０５％以上とし、添加し過
ぎると変態が著しく遅れ、生産性に影響を及ぼすので
１．０％以下とする。Ｍｏもパテンティング後の強度な
らびに伸線加工後の強度を向上するために添加する。添
加する場合は、その効果の表れる０．１％以上とし、添
加し過ぎるとパーライト変態を著しく遅らせ生産性を低
下させるので影響の無い０．５％以下とする。Ni is also added to improve the strength after patenting and the strength after wire drawing. When added, the content is set to 0.05% or more at which the effect is exhibited. When added too much, the transformation is significantly delayed and the productivity is affected. Mo is also added to improve the strength after patenting and the strength after wire drawing. When added, the content is set to 0.1% or more where the effect is exhibited, and when added too much, the pearlite transformation is remarkably delayed to lower the productivity, so that the content is set to 0.5% or less which has no effect.
【００２０】Ｃｕは腐食疲労特性を向上するために添加
する。添加する場合は、その効果の表れる０．１％以上
とし、添加し過ぎるとパーライト変態を著しく遅らせ生
産性を低下させる影響の無い０．８％以下とする。Ｗは
腐食疲労特性を向上するために添加する。添加する場合
は、その効果の表れる０．０５％以上とし、添加し過ぎ
るとパーライト変態を著しく遅らせ生産性を低下させる
影響の無い０．８％以下とする。また、これらの元素は
複合添加するとより効果を発揮する。Cu is added to improve corrosion fatigue characteristics. When added, the content is set to 0.1% or more at which the effect is exhibited, and when added too much, the content is set to 0.8% or less, at which the pearlite transformation is significantly delayed and there is no effect of lowering the productivity. W is added to improve corrosion fatigue characteristics. When added, the content is set to 0.05% or more at which the effect is exhibited, and when added too much, the content is set to 0.8% or less, which does not significantly delay the pearlite transformation and does not lower the productivity. Further, these elements exhibit more effects when added in combination.
【００２１】その他、Ｌａ，Ｃｅを微量添加（０．００
０５％〜０．０１％）することにより腐食疲労特性を向
上することができる。Ａｌはパーライトブロックサイズ
を微細にするために添加する。添加する場合は、その効
果の表れる０．００１％以上添加する。添加量が０．０
６％を超えるとＡｌ2 Ｏ3 などの硬質の介在物が増え伸
線加工性を低下させるので上限を０．０６％とする。In addition, a small amount of La and Ce is added (0.00
(05% to 0.01%) can improve corrosion fatigue properties. Al is added to make the pearlite block size fine. When it is added, it is added in an amount of 0.001% or more that shows the effect. 0.0
If it exceeds 6%, hard inclusions such as Al 2 O 3 increase and the wire drawing workability deteriorates, so the upper limit is made 0.06%.
【００２２】Ｂはパーライトブロックサイズを微細にす
るために添加する。添加する場合は、その効果の表れる
０．０００５％以上添加する。添加元素が多すぎると恒
温変態が遅延し、硬質なミクロマルテンサイトが発生し
やすくなるため０．０６％以下とする。Ｔｉはパーライ
トブロックサイズを微細にするため添加する。添加する
場合は、その効果の表れる０．００１％以上添加する。
添加元素が多すぎると恒温変態が遅延し、硬質なミクロ
マルテンサイトが発生しやすくなるため０．０６％以下
とする。B is added to reduce the pearlite block size. When adding, 0.0005% or more which shows the effect is added. If the amount of the added element is too large, the isothermal transformation is delayed and hard micro martensite is easily generated, so the content is set to 0.06% or less. Ti is added to make the pearlite block size fine. When it is added, it is added in an amount of 0.001% or more that shows the effect.
If the amount of the added element is too large, the isothermal transformation is delayed and hard micro martensite is easily generated, so the content is set to 0.06% or less.
【００２３】Ｎｂはパーライトブロックサイズを微細に
するため添加する。添加する場合は、その効果の表れる
０．００１％以上添加する。添加元素が多すぎると恒温
変態が遅延し、硬質なミクロマルテンサイトが発生しや
すくなるため０．０６％以下とする。Ｐは偏析すること
による脆化組織を生成しやすく、Ｓは介在物を形成しや
すい元素なので悪影響の少なくなる０．０２％以下にそ
れぞれするのが望ましい。Nb is added to make the pearlite block size fine. When it is added, it is added in an amount of 0.001% or more that shows the effect. If the amount of the added element is too large, the isothermal transformation is delayed and hard micro martensite is easily generated, so the content is set to 0.06% or less. P easily forms an embrittlement structure due to segregation, and S is an element that easily forms inclusions. Therefore, it is preferable that P is set to 0.02% or less, at which adverse effects are reduced.
【００２４】次にこれらの本発明の製造方法について説
明する。前述の鋼成分に調整された鋼は、溶製された後
にブルームあるいはビレットに連続鋳造される。この鋳
造時の鋳型内のモールド近傍に純鉄を添加する事によ
り、表層から３００μｍの炭素濃度を平均の炭素濃度の
０．９７倍以下とする。０．９７倍超の場合では、一般
的な製造工程である巻き取り温度８５０℃以上で巻き取
った後、４００℃〜５３０℃の温度で溶融ソルトに浸漬
してパーライト組織とした場合、表層から３００μｍの
範囲のビッカース硬度がＨｖ３９０以下、あるいは平均
のラメラ間隔が９５nm以上とすることが出来ない。従っ
て表層から３００μｍの炭素量が断面全体平均濃度の
０．９７倍以下である必要がある。線材加熱炉では、１
０００℃から１２００℃の間に加熱する。加熱温度が１
０００℃以下の場合、圧延温度が低くなり圧延が困難と
なる。また、１２００℃以上に加熱すると一般的な燃焼
炉内では脱炭層が大きくなるので１２００℃以下とす
る。加熱後、一般的な線径４〜１６mmに圧延する。その
後、巻き取り温度を９０℃以下に調整し必要に応じて巻
き取る。巻き取り温度が９００℃超になるとスケール厚
みが大きく成りすぎるので９００℃以下とする。Next, the production method of the present invention will be described. The steel adjusted to the above-mentioned steel composition is continuously cast into a bloom or a billet after being melted. By adding pure iron to the vicinity of the mold in the casting mold, the carbon concentration of 300 μm from the surface layer is reduced to 0.97 times or less of the average carbon concentration. In the case of more than 0.97 times, after winding at a winding temperature of 850 ° C. or higher, which is a general manufacturing process, when immersing in a molten salt at a temperature of 400 ° C. to 530 ° C. to form a pearlite structure, The Vickers hardness in the range of 300 μm cannot be Hv390 or less, or the average lamella spacing cannot be 95 nm or more. Therefore, the carbon content of 300 μm from the surface layer needs to be 0.97 times or less of the average concentration of the entire cross section. In the wire heating furnace, 1
Heat between 000 ° C and 1200 ° C. Heating temperature is 1
If the temperature is lower than 000 ° C., the rolling temperature becomes low and the rolling becomes difficult. Further, when heating to 1200 ° C. or more, the decarburized layer becomes large in a general combustion furnace, so that the temperature is set to 1200 ° C. or less. After heating, it is rolled to a general wire diameter of 4 to 16 mm. Thereafter, the winding temperature is adjusted to 90 ° C. or lower, and winding is performed as necessary. If the winding temperature exceeds 900 ° C., the scale thickness becomes too large.
【００２５】その後、直ちに４００℃〜５７０℃の溶融
ソルトに浸漬しパーライト変態を終了させる。溶融塩温
度が４００℃以下となると組織が微細に成りすぎ表層の
ビッカース硬度がＨｖ３９０以下、３００μｍの平均の
ラメラ間隔が９５nm以上とすることが困難となる。また
５７０℃以上とすると操業が困難となるので５７０℃以
下とする。Then, it is immediately immersed in a molten salt at 400 to 570 ° C. to complete the pearlite transformation. When the molten salt temperature is 400 ° C. or less, the structure becomes too fine, and it is difficult to make the surface Vickers hardness Hv 390 or less and the average lamella spacing of 300 μm to 95 nm or more. If the temperature is higher than 570 ° C., the operation becomes difficult.
【００２６】次に線材に疵が入る場合、断線に至る原因
について述べる。線材に入る疵の深さは、大きいもので
１００μｍ程度である。このとき断線に最も影響を与え
るのは、疵が入る際に発生する熱により表層に形成され
る硬質なマルテンサイトの存在である。断線を引き起こ
すマルテンサイトの発生を無害化するためには、表層か
ら３００μｍのビッカース硬度をＨｖ３９０以下、ある
いは表層から３００μｍの平均のラメラ間隔を９５nm以
下に調整する必要がある。これらの事により、疵が入る
際に形成されるマルテンサイトは、発生しなくなるか無
害な程度に薄くなる。Next, a description will be given of the cause of breakage when the wire rod has a flaw. The depth of the flaw entering the wire is as large as about 100 μm. At this time, what has the greatest influence on the disconnection is the presence of hard martensite formed on the surface layer by heat generated when a flaw is formed. In order to render the generation of martensite causing disconnection harmless, it is necessary to adjust the Vickers hardness of 300 μm from the surface layer to Hv 390 or less, or the average lamella spacing of 300 μm from the surface layer to 95 nm or less. As a result, the martensite formed when a flaw is formed is not generated or becomes harmlessly thin.
【００２７】[0027]
【実施例】表１に試作に用いた本発明鋼および比較鋼の
化学成分を示す。本発明鋼ならびに比較鋼を転炉で溶製
したのち連続鋳造により５００mm×３００mmのブルーム
とした。その後、熱間圧延で１２２mm角のビレットとし
た。その後、１１００〜１２００℃で加熱した後、熱間
圧延で直径５．５mmから１３mmの線材とした。EXAMPLES Table 1 shows the chemical composition of the steel of the present invention and the comparative steel used in the trial production. The steel of the present invention and the comparative steel were melted in a converter and then continuously cast into blooms of 500 mm × 300 mm. Thereafter, a billet of 122 mm square was formed by hot rolling. Then, after heating at 1100 to 1200 ° C, a wire rod having a diameter of 5.5 mm to 13 mm was formed by hot rolling.
【００２８】表２に線材の表層から３００μｍの炭素濃
度を線材全断面積の平均の炭素量で割った炭素量比なら
びに熱間圧延終了後の温度をはじめとする製造条件を示
した。得られた線材の表層の硬度ならびに表層のラメラ
間隔を同表２に示した。本発明鋼１〜１５は、本発明に
従って鋼の化学成分とミクロ組織が調整されている。一
方、比較鋼１６，１７は、鋼の成分と圧延方法は本発明
鋼と同じであるが、炭素量比が本発明鋼に比べ高い場合
である。Table 2 shows the production conditions including the carbon content ratio obtained by dividing the carbon concentration of 300 μm from the surface layer of the wire by the average carbon content of the entire cross-sectional area of the wire, and the temperature after completion of hot rolling. Table 2 shows the hardness of the surface layer and the lamella spacing of the surface layer of the obtained wire. In the present invention steels 1 to 15, the chemical composition and the microstructure of the steel are adjusted according to the present invention. On the other hand, comparative steels 16 and 17 have the same steel composition and rolling method as the steel of the present invention, but have a higher carbon content ratio than the steel of the present invention.
【００２９】これらの線材を用いて、人工的に疵を付
け、疵の下に形成されたマルテンサイトの厚み測定し
た。また、これらの線材の２ｔのコイルをフォークリフ
トのフックが線材と擦れあうようにして３０回運搬を繰
り返し、伸過程における断線回数を調べた。これらの結
果を表２に示した。本発明にしたがって製造された本発
明鋼１〜１５はマルテンサイトの厚みが薄く、断線回数
の少ない良好な結果を示す。一方、比較鋼１６〜１７
は、マルテンサイトの厚みがあつく、断線回数が本発明
鋼より高い。Using these wires, flaws were artificially formed and the thickness of martensite formed under the flaws was measured. In addition, a 2t coil of these wires was repeatedly transported 30 times with the hook of the forklift rubbing against the wires, and the number of disconnections in the elongation process was examined. Table 2 shows the results. The steels 1 to 15 of the present invention produced according to the present invention have good martensite thickness and show good results with a small number of disconnections. On the other hand, comparative steels 16-17
Has a larger martensite thickness and the number of disconnections is higher than that of the steel of the present invention.
【００３０】[0030]
【表１】 [Table 1]
【００３１】[0031]
【表２】 [Table 2]
【００３２】[0032]
【発明の効果】本発明を用いることで、疵による断線の
少ない高強度の線材を容易に得ることができる。According to the present invention, it is possible to easily obtain a high-strength wire with less breakage due to flaws.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｃ 38/54 Ｃ２２Ｃ 38/54 Ｆターム(参考） 4K032 AA01 AA02 AA06 AA07 AA11 AA14 AA16 AA19 AA22 AA23 AA27 AA29 AA31 AA32 AA35 AA36 AA37 AA40 BA02 CA02 CB02 CC03 CC04 CE02 4K043 AA02 AB01 AB02 AB05 AB06 AB10 AB13 AB15 AB18 AB21 AB22 AB25 AB26 AB27 AB28 AB29 AB30 AB31 AB33 BA01 BA03 BA04 BA05 CA06 CB02 DA01 EA03 EA04 FA03 FA11──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) C22C 38/54 C22C 38/54 F term (Reference) 4K032 AA01 AA02 AA06 AA07 AA11 AA14 AA16 AA19 AA22 AA23 AA27 AA29 AA31 AA32 AA35 AA36 AA37 AA40 BA02 CA02 CB02 CC03 CC04 CE02 4K043 AA02 AB01 AB02 AB05 AB06 AB10 AB13 AB15 AB18 AB21 AB22 AB25 AB26 AB27 AB28 AB29 AB30 AB31 AB33 BA01 BA03 BA04 BA05 CA06 CB02 DA01 EA03 EA04 FA03 FA11
Claims (13)
有する高炭素鋼で、その表層から３００μｍまでの層の
平均炭素含有量が全断面での平均炭素含有量の０．９７
倍以下とすることにより、前記層が擦過マルテンサイト
組織の生成し難い層としたことを特徴とする高強度直接
パテンティング線材。1. A high-carbon steel having a carbon content of 0.7% or more by mass%, wherein the average carbon content of the layer from the surface layer to 300 μm is 0.97 of the average carbon content in the entire cross section.
A high-strength direct patenting wire rod characterized in that the layer is less than twice as large as the above layer so that a scratch martensite structure is hardly generated.
であることを特徴とする請求項１記載の高強度直接パテ
ンティング線材。2. The high-strength direct patenting wire according to claim 1, wherein the average lamella spacing in the layer is 95 nm or more.
請求項１乃至２記載の高強度直接パテンティング線材。3. The steel component of the high carbon steel is, in mass%, C: 0.7 to 1.2%, Si: 0.1 to 1.5%, Mn: 0.1 to 1.0%. 3. The high-strength direct patenting wire according to claim 1, comprising a balance of Fe and unavoidable impurities.
で、 Ｃｒ：０．１〜０．５％、 Ｖ：０．００１〜０．２％、 Ｎｉ：０．０５〜１．０％、 Ｍｏ：０．１〜０．５％、 の１種または２種以上を含有することを特徴とする請求
項３記載の高強度直接パテンティング線材。4. The steel composition of the high carbon steel further comprises a mass%
And one of Cr: 0.1 to 0.5%, V: 0.001 to 0.2%, Ni: 0.05 to 1.0%, Mo: 0.1 to 0.5%, or The high-strength direct patenting wire according to claim 3, comprising two or more kinds.
で、 Ｃｕ：０．０５〜０．８％、 Ｗ：０．０５〜０．８％、 Ｌａ：０．０００５〜０．０１％、 Ｃｅ：０．０００５〜０．０１％、 の１種または２種以上を含有することを特徴とする請求
項３乃至４記載の高強度直接パテンティング線材。5. The steel composition of the high carbon steel further comprises a mass%
And one of Cu: 0.05 to 0.8%, W: 0.05 to 0.8%, La: 0.0005 to 0.01%, Ce: 0.0005 to 0.01%, or The high-strength direct patenting wire according to claim 3, comprising two or more types.
で、 Ａｌ：０．００１〜０．０６％、 Ｂ：０．０００５〜０．０６％、 Ｔｉ：０．００１〜０．０６％、 Ｎｂ：０．００１〜０．０６％、 の１種または２種以上を含有することを特徴とする請求
項３乃至５記載の高強度直接パテンティング線材。6. The steel composition of the high carbon steel further comprises a mass%
And one of the following: Al: 0.001 to 0.06%, B: 0.0005 to 0.06%, Ti: 0.001 to 0.06%, Nb: 0.001 to 0.06%, or The high-strength direct patenting wire according to any one of claims 3 to 5, comprising two or more types.
有する高炭素鋼を、線材加熱炉で１０００〜１２００℃
で加熱後、直径４〜１６mmとする熱間圧延を行い、７５
０〜９００℃の温度で圧延を終了し、その後直ちに４０
０〜５７０℃の溶融ソルトバスに浸漬してパーライト変
態を終了させることにより、その表層から３００μｍま
での層の平均炭素含有量が全断面での平均炭素含有量の
０．９７倍以下で、前記層が擦過マルテンサイト組織の
生成し難い層としたことを特徴とする高強度直接パテン
ティング線材の製造方法。7. A high-carbon steel having a carbon content of 0.7% by mass or more in a wire heating furnace at 1000 to 1200 ° C.
After hot-rolling, hot rolling to a diameter of 4 to 16 mm
Rolling is completed at a temperature of 0 to 900 ° C.
By immersing in a molten salt bath at 0 to 570 ° C. to terminate the pearlite transformation, the average carbon content of the layer from the surface layer to 300 μm is 0.97 times or less of the average carbon content in the entire cross section. A method for producing a high-strength direct patenting wire, characterized in that the layer is a layer in which an abrasion martensite structure is hardly generated.
ることを特徴とする請求項７記載の高強度直接パテンテ
ィング線材の製造方法。8. The method for producing a high-strength direct patenting wire according to claim 7, wherein the lamella interval in the layer is 95 nm or more.
９００℃の温度で巻き取り、その後直ちに４００〜５７
０℃の溶融ソルトバスに浸漬することを特徴とする請求
項７または８記載の高強度直接パテンティング線材の製
造方法。9. The hot rolling is performed, and thereafter, 750 to
Wound at a temperature of 900 ° C, and immediately thereafter 400-57
The method for producing a high-strength direct patenting wire according to claim 7 or 8, wherein the method is immersed in a molten salt bath at 0 ° C.
請求項７〜９のいずれかの項に記載の高強度直接パテン
ティング線材の製造方法。10. The steel component of the high carbon steel is, in mass%, C: 0.7 to 1.2%, Si: 0.1 to 1.5%, Mn: 0.1 to 1.0%. The method for producing a high-strength direct patenting wire according to any one of claims 7 to 9, comprising a balance of Fe and unavoidable impurities.
で、 Ｃｒ：０．１〜０．５％、 Ｖ：０．００１〜０．２％、 Ｎｉ：０．０５〜１．０％、 Ｍｏ：０．１〜０．５％、 の１種または２種以上を含有することを特徴とする請求
項１０記載の高強度直接パテンティング線材の製造方
法。11. The steel composition of the high carbon steel further comprises a mass%
And one of Cr: 0.1 to 0.5%, V: 0.001 to 0.2%, Ni: 0.05 to 1.0%, Mo: 0.1 to 0.5%, or The method for producing a high-strength direct patenting wire according to claim 10, comprising two or more kinds.
で、 Ｃｕ：０．０５〜０．８％、 Ｗ：０．０５〜０．８％、 Ｌａ：０．０００５〜０．０１％、 Ｃｅ：０．０００５〜０．０１％、 の１種または２種以上を含有することを特徴とする請求
項１０または１１記載の高強度直接パテンティング線材
の製造方法。12. The steel composition of the high carbon steel further comprises a mass%
And one of Cu: 0.05 to 0.8%, W: 0.05 to 0.8%, La: 0.0005 to 0.01%, Ce: 0.0005 to 0.01%, or The method for producing a high-strength direct patenting wire according to claim 10, comprising two or more kinds.
で、 Ａｌ：０．００１〜０．０６％、 Ｂ：０．０００５〜０．０６％、 Ｔｉ：０．００１〜０．０６％、 Ｎｂ：０．００１〜０．０６％、 の１種または２種以上を含有することを特徴とする請求
項１０〜１２のいずれかの項に記載の高強度直接パテン
ティング線材の製造方法。13. The steel composition of the high carbon steel further comprises a mass%
And one of the following: Al: 0.001 to 0.06%, B: 0.0005 to 0.06%, Ti: 0.001 to 0.06%, Nb: 0.001 to 0.06%, or The method for producing a high-strength direct patenting wire according to any one of claims 10 to 12, comprising two or more kinds.
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP37131299A JP4392093B2 (en) | 1999-12-27 | 1999-12-27 | High-strength direct patenting wire and method for producing the same |
| MYPI20006128A MY128660A (en) | 1999-12-22 | 2000-12-22 | High strength direct patenting wire rod and method of producing the same |
| PCT/JP2000/009167 WO2001046485A1 (en) | 1999-12-22 | 2000-12-22 | Direct patenting high strength wire rod and method for producing the same |
| KR10-2001-7010640A KR100430068B1 (en) | 1999-12-22 | 2000-12-22 | Direct patenting high strength wire rod and method for producing the same |
| CN00804128A CN1117171C (en) | 1999-12-22 | 2000-12-22 | Direct patenting high strength wire rod and method for producing same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP37131299A JP4392093B2 (en) | 1999-12-27 | 1999-12-27 | High-strength direct patenting wire and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2001181793A true JP2001181793A (en) | 2001-07-03 |
| JP4392093B2 JP4392093B2 (en) | 2009-12-24 |
Family
ID=18498497
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP37131299A Expired - Fee Related JP4392093B2 (en) | 1999-12-22 | 1999-12-27 | High-strength direct patenting wire and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4392093B2 (en) |
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1999
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| WO2015163407A1 (en) * | 2014-04-24 | 2015-10-29 | 新日鐵住金株式会社 | Wire material for high strength steel cord |
| KR20160137604A (en) | 2014-04-24 | 2016-11-30 | 신닛테츠스미킨 카부시키카이샤 | Wire material for high strength steel cord |
| KR20160138164A (en) | 2014-04-24 | 2016-12-02 | 신닛테츠스미킨 카부시키카이샤 | Filament for high strength steel cord |
| JPWO2015163407A1 (en) * | 2014-04-24 | 2017-04-20 | 新日鐵住金株式会社 | High strength steel cord wire |
| JPWO2015163409A1 (en) * | 2014-04-24 | 2017-04-20 | 新日鐵住金株式会社 | Filament for high strength steel cord |
| EP3135786A4 (en) * | 2014-04-24 | 2017-10-04 | Nippon Steel & Sumitomo Metal Corporation | Wire material for high strength steel cord |
| KR101869633B1 (en) * | 2014-04-24 | 2018-06-20 | 신닛테츠스미킨 카부시키카이샤 | Wire material for high strength steel cord |
| US10156001B2 (en) | 2014-04-24 | 2018-12-18 | Nippon Steel & Sumitomo Metal Corporation | Filament for high strength steel cord |
| US10435765B2 (en) | 2014-04-24 | 2019-10-08 | Nippon Steel Corporation | Wire rod for high strength steel cord |
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| JP4392093B2 (en) | 2009-12-24 |
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