JPH06312210A - Steel wire for steel cord excellent in fatigue strength and its manufacture - Google Patents
Steel wire for steel cord excellent in fatigue strength and its manufactureInfo
- Publication number
- JPH06312210A JPH06312210A JP10270993A JP10270993A JPH06312210A JP H06312210 A JPH06312210 A JP H06312210A JP 10270993 A JP10270993 A JP 10270993A JP 10270993 A JP10270993 A JP 10270993A JP H06312210 A JPH06312210 A JP H06312210A
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- steel
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- less
- plating
- fatigue strength
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- 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)
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明はタイヤ、ベルトコードな
どのゴムおよび有機材料の補強用に使用されているスチ
ールコードなどの高強度で高延性の極細鋼線に関するも
のである。これらの鋼線は、長尺ゴムベルト、スチール
タイヤ用コード、ホースワイヤなどに使用される。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength, high-ductility ultrafine steel wire such as a steel cord used for reinforcing rubber and organic materials such as tires and belt cords. These steel wires are used for long rubber belts, steel tire cords, hose wires and the like.
【０００２】[0002]
【従来の技術】一般にスチールコードなど伸線された高
炭素鋼極細線は、通常必要に応じて熱間圧延した後に調
整冷却した直径４．０〜５．５mmの線材を一次伸線加工
後、最終パテンティング処理を行ない、その後ブラスメ
ッキ処理を経て最終湿式伸線加工により製造されてい
る。このような極細鋼線の多くは、２本撚り、５本撚り
などの撚り線加工を施した状態でスチールコードとして
使用されている。これらのスチールコードにおいては １）より高強度であること ２）高速伸線性が優れていること、 ３）疲労特性が優れていること、 ４）高速撚り線性が優れること、 等の特性を具備しなければならない。2. Description of the Related Art In general, drawn high carbon steel ultrafine wire such as steel cord is usually hot-rolled as necessary, and then adjusted and cooled, and a wire having a diameter of 4.0 to 5.5 mm is subjected to primary wire drawing. The final patenting process is performed, then the brass plating process is performed, and the final wet wire drawing process is performed. Most of such ultra-fine steel wires are used as steel cords in a state in which a twisted wire process such as two-strand and five-strand is applied. These steel cords have characteristics such as 1) higher strength, 2) superior high-speed drawability, 3) superior fatigue properties, 4) superior high-speed twistability, and the like. There must be.
【０００３】このため、従来から要望に応じた高品質の
鋼材が開発されている。例えば、特開昭６０−２０４８
６５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，Ｓ
ｉ，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。Therefore, high-quality steel materials have been developed in response to demands. For example, JP-A-60-2048
No. 65 discloses that the Mn content is regulated to less than 0.3% to suppress the generation of a supercooled structure after lead patenting, and
By controlling the amount of elements such as i and Mn, there has been disclosed a high-strength wire and a high-carbon steel wire material for steel cord, which has less breakage when twisted and has high strength and high ductility.
JP-A-63-24046 discloses that the Si content is 1.
A high toughness and high ductility wire rod for ultrafine wires in which the tensile strength of the lead patenting material is increased and the wire drawing work ratio is reduced by setting the content to be at least 00% is disclosed.
【０００４】また、一方でこれらの特性に悪影響を与え
るものの一つとして硬質の酸化物系非金属介在物があげ
られる。一般的に酸化物系介在物の中でもＡｌ2 Ｏ3 ，
ＳｉＯ2 ，ＣａＯ，ＴｉＯ2 ，ＭｇＯ等の単組成の介在
物は硬度も高く非延性である。従って伸線性に優れた高
炭素鋼線材製造のためには、溶鋼の清浄性を高めるとと
もに、酸化物系介在物を低融点化し軟質化する必要があ
る。On the other hand, a hard oxide type non-metallic inclusion is one of those which adversely affect these characteristics. Generally, among oxide-based inclusions, Al 2 O 3 ,
Inclusions having a single composition such as SiO 2 , CaO, TiO 2 , and MgO have high hardness and are non-ductile. Therefore, in order to produce a high carbon steel wire rod having excellent wire drawability, it is necessary to enhance the cleanliness of molten steel and to lower the melting point and soften the oxide inclusions.
【０００５】この様に鋼の清浄度を上げ、非延性介在物
の軟質化を図る方法として、特公昭５７−２２９６９号
公報に示される伸線性の良好な高炭素鋼線材用鋼の製造
法及び特開昭５５−２４９６１号公報に示される極細線
の製造方法が示されているが、これらの技術の基本思想
は、Ａｌ2 Ｏ3 −ＳｉＯ2 −ＭｎＯの三元系の酸化物系
非金属介在物の組成制御によるものである。As a method for improving the cleanliness of steel and softening non-ductile inclusions as described above, a method for producing a steel for high carbon steel wire rod having good drawability, which is disclosed in JP-B-57-22969, and Japanese Unexamined Patent Publication (Kokai) No. 55-24961 discloses a method for producing an ultrafine wire. The basic idea of these techniques is that Al 2 O 3 —SiO 2 —MnO ternary oxide nonmetal. This is because the composition of the inclusions is controlled.
【０００６】一方、特開昭５０−７１５０７号公報で
は、非金属介在物をＡｌ2 Ｏ3 ，ＳｉＯ2 ，ＭｎＯの三
元状態図におけるスペーサータイト領域にすることによ
って製品の伸線性を改善することが提案され、又特開昭
５０−８１９０７号公報では溶鋼中に添加するＡｌ量を
規制することによって有害な介在物を減少せしめて、伸
線性を改善する方法が開示されている。On the other hand, in Japanese Unexamined Patent Publication (Kokai) No. 50-71507, the wire drawability of a product is improved by making a non-metallic inclusion a spacer tight region in the ternary phase diagram of Al 2 O 3 , SiO 2 and MnO. Japanese Patent Application Laid-Open No. 50-81907 discloses a method in which harmful inclusions are reduced and the wire drawability is improved by controlling the amount of Al added to molten steel.
【０００７】又、特公昭５７−３５２４３号公報におい
ては、非延性介在物指数２０以下のスチールコード製造
に関し、Ａｌ完全規制の下で取鍋溶鋼内にキャリアーガ
ス（不活性ガス）と共にＣａＯ含有フラックスを吹込
み、予備脱酸した後、Ｃａ，Ｍｇ，ＲＥＭの一種または
二種以上を含む合金を吹込み介在物を軟質化する方法が
提案されている。Further, in Japanese Patent Publication No. 57-35243, regarding the production of steel cords having a non-ductile inclusion index of 20 or less, a CaO-containing flux together with a carrier gas (inert gas) in a ladle molten steel is fully regulated under Al. A method has been proposed in which the inclusions are blown and then pre-deoxidized, and then an alloy containing one or more of Ca, Mg and REM is blown to soften the inclusions.
【０００８】しかしながら、軽量化、長寿命化の観点か
ら一層、高強度でかつ疲労特性の優れた材料が求められ
るようになっている。However, from the viewpoint of weight reduction and long life, a material having higher strength and excellent fatigue characteristics has been demanded.
【０００９】[0009]
【発明が解決しようとする課題】本発明は、従来の鋼線
では達成し得なかった高強度でかつ高延性かつ高疲労強
度の鋼線の製造方法を提供することを目的とする。SUMMARY OF THE INVENTION It is an object of the present invention to provide a method for producing a steel wire having high strength, high ductility and high fatigue strength which cannot be achieved by the conventional steel wire.
【００１０】[0010]
【課題を解決するための手段】本発明は前記課題を解決
するためになされたもので、その要旨は、 （１）重量％で Ｃ ：０．９〜１．１０％ Ｓｉ：０．４％以下 Ｍｎ：０．５％以下 Ｐ ：０．０２０％以下 Ｓ ：０．０２０％以下 Ａｌ：０．００３％以下 に加え以下の元素のいづれかあるいは両方を添加し Ｃｒ：０．１０〜０．３０％ Ｎｉ：０．１０〜１．００％ 残部鉄及び不可避的不純物からよりなる鋼で、鋳片の介
在物組成がＭｎＯ＋ＣａＯ，ＳｉＯ2 ，Ａｌ2 Ｏ3 の四
元系で見た場合に、図１のイ、ロ、ハ、ニ、ホ、ヘ、
ト、チ、リ、ヌで囲まれる領域Ｉとなる介在物が８０％
以上で、パーライト組織で、ブラスめっき、Ｃｕめっ
き、Ｎｉめっきのいづれかを施し、引張強さが、３５０
０MPa 以上、（−１５９０×ｌｏｇＤ＋３３３０）MPa
以下で、円相当直径が０．１５〜０．４mmφであること
を特徴とする疲労強度の優れたスチールコード用鋼線。The present invention has been made to solve the above problems, and the gist thereof is as follows: (1) C: 0.9 to 1.10% Si: 0.4% by weight Below Mn: 0.5% or less P: 0.020% or less S: 0.020% or less Al: 0.003% or less In addition to one or both of the following elements Cr: 0.10 to 0.30 % Ni: 0.10 to 1.00% Steel consisting of balance iron and unavoidable impurities, the composition of inclusions in the slab is MnO + CaO, SiO 2 , Al 2 O 3 When viewed in the quaternary system, the figure 1 a, b, ha, d, h, h,
80% of the inclusions are the region I surrounded by g
As described above, the pearlite structure was subjected to brass plating, Cu plating, or Ni plating, and the tensile strength was 350.
0 MPa or more, (-1590 x logD + 3330) MPa
Below, a steel wire for steel cords having excellent fatigue strength, characterized in that the equivalent circle diameter is 0.15 to 0.4 mmφ.
【００１１】但し、 Ｄ：円相当直径（mm）However, D: Diameter equivalent to circle (mm)
【００１２】（２）鋼成分が、重量％で、更に、Ｃｕ：
０．１０〜０．８０％を含む（１）記載の疲労強度の優
れたスチールコード用鋼線。(2) The steel composition is wt% and further Cu:
The steel wire for steel cord having excellent fatigue strength according to (1), which contains 0.10 to 0.80%.
【００１３】（３）重量％で Ｃ ：０．９〜１．１０％ Ｓｉ：０．４％以下 Ｍｎ：０．５％以下 Ｐ ：０．０２０％以下 Ｓ ：０．０２０％以下 Ａｌ：０．００３％以下 に加え以下の元素のいづれかあるいは両方を添加し Ｃｒ：０．１０〜０．３０％ Ｎｉ：０．１０〜１．００％ 残部鉄及び不可避的不純物からよりなる鋼で、鋳片の介
在物組成がＭｎＯ＋ＣａＯ，ＳｉＯ2 ，Ａｌ2 Ｏ3 の四
元系で見た場合に、図１のイ、ロ、ハ、ニ、ホ、ヘ、
ト、チ、リ、ヌで囲まれる領域Ｉとなる介在物が８０％
以上に調整したビレットを熱間圧延によって４．０〜
７．０mmφの線材とし、調整冷却により初析セメンタイ
トの存在しない組織とし、伸線加工により１．１から
２．７mmφのワイヤとし、パテンティング処理により引
張強さを｛（５３０＋９８０×Ｃwt％）±５０｝MPa に
調整し、ブラスめっき、Ｃｕめっき、Ｎｉめっきのいづ
れかを行い、真歪で（−１．４３×ｌｏｇＤ＋２．４
９）以上、（−１．４３×ｌｏｇＤ＋３．０９）以下の
加工を行い円相当直径が０．１５〜０．４mmφのワイヤ
とすることを特徴とする（１）記載の疲労強度の優れた
スチールコード用鋼線の製造方法。(3) C: 0.9 to 1.10% Si: 0.4% or less Mn: 0.5% or less P: 0.020% or less S: 0.020% or less Al: 0 In addition to 0.003% or less, one or both of the following elements are added: Cr: 0.10 to 0.30% Ni: 0.10 to 1.00% Steel consisting of balance iron and unavoidable impurities. When the inclusion composition of MnO + CaO, SiO 2 , Al 2 O 3 is seen in the quaternary system of FIG. 1, a, b, c, d, h, f,
80% of the inclusions are the region I surrounded by g
The billet adjusted as described above is subjected to 4.0 to 4.0 by hot rolling.
The wire rod has a diameter of 7.0 mm, and the structure has no pro-eutectoid cementite by cooling, and the wire has a diameter of 1.1 to 2.7 mm φ. 50} MPa, and either brass plating, Cu plating, or Ni plating is performed, and the true strain is (-1.43 x logD + 2.4).
A steel having excellent fatigue strength according to (1), characterized in that a wire having a circle-equivalent diameter of 0.15 to 0.4 mmφ is obtained by processing not less than 9) and not more than (−1.43 × logD + 3.09). Manufacturing method of steel wire for cord.
【００１４】但し、 Ｄ：円相当直径（mm）However, D: Diameter equivalent to circle (mm)
【００１５】（４）出発鋼成分が重量％で、更に、Ｃ
ｕ：０．１０〜０．８０％を含む鋼である（３）記載の
疲労強度の優れたスチールコード用鋼線の製造方法。(4) The starting steel composition is wt%, and further C
u: The steel wire for steel cord having excellent fatigue strength according to (3), which is a steel containing 0.10 to 0.80%.
【００１６】（５）調整冷却後、中間パテンティングを
加えながら伸線加工により１．１から２．７mmφのワイ
ヤとすることを特徴とする（３）または（４）記載の疲
労強度の優れたスチールコード用鋼線の製造方法。(5) An excellent fatigue strength as described in (3) or (4), which is characterized in that a wire of 1.1 to 2.7 mmφ is formed by wire drawing while applying intermediate patenting after conditioning cooling. Manufacturing method of steel wire for steel cord.
【００１７】（６）めっき後の伸線加工において、その
アプローチ角が１０°±２°であるダイスによって伸線
加工することを特徴とする（３）、（４）または（５）
記載の疲労強度の優れたスチールコード用鋼線の製造方
法。(6) In the wire drawing process after plating, the wire drawing process is performed with a die having an approach angle of 10 ° ± 2 ° (3), (4) or (5).
A method for producing a steel wire for a steel cord having excellent fatigue strength as described above.
【００１８】[0018]
【作用】以下本発明を詳細に説明する。なお、以下に示
す％は重量％である。本発明の鋼組成の限定理由は下記
の通りである。通常のパテンティング処理においては、
Ｃが０．８％近傍の共析成分においても、旧オーステナ
イト粒界に沿って微量の初析フェライトが析出するこ
と、また、この初析フェライトが伸線後の延性低下の原
因となることを本発明者らは発見した。Ｃは経済的かつ
有効な強化元素であるが、この初析フェライトの析出量
低下にも有効な元素である。従って、引張強さ３６００
MPa 以上の極細線とし延性を高めるためにはＣは０．９
０％以上とすることが必要であるが、高すぎると延性が
低下し伸線性が劣化するのでその上限は１．１０％とす
る。The present invention will be described in detail below. In addition,% shown below is weight%. The reasons for limiting the steel composition of the present invention are as follows. In normal patenting process,
Even in the eutectoid component where C is around 0.8%, a small amount of proeutectoid ferrite is precipitated along the former austenite grain boundary, and this proeutectoid ferrite causes a decrease in ductility after wire drawing. The present inventors have discovered. Although C is an economical and effective strengthening element, it is also an effective element for reducing the precipitation amount of this proeutectoid ferrite. Therefore, the tensile strength is 3600
C is 0.9 in order to increase the ductility by making ultra fine wires of MPa or more.
It is necessary to set the content to 0% or more, but if it is too high, the ductility decreases and wire drawability deteriorates, so the upper limit is made 1.10%.
【００１９】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。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、反面フェライトの延性を低下させ伸線
後の極細線の延性を低下させるため０．４％以下とす
る。Si is an element necessary for deoxidizing the steel, so when the content is too low, the deoxidizing effect becomes insufficient. Further, Si dissolves in the ferrite phase in pearlite formed after heat treatment to increase the strength after patenting, but on the other hand, it reduces the ductility of ferrite and reduces the ductility of ultrafine wires after drawing, so 0.4% Below.
【００２０】Ｍｎは鋼の焼き入れ性を確保するために小
量のＭｎを添加することが望ましい。しかし、多量のＭ
ｎの添加は偏析を引き起こしパテンティングの際にベイ
ナイト、マルテンサイトという過冷組織が発生しその後
の伸線性を害するため０．５％以下とする。本発明のよ
うな過共析鋼の場合、パテンティング後の組織において
セメンタイトのネットワークが発生しやすくセメンタイ
トの厚みのあるものが析出しやすい。この鋼において高
強度高延性を実現するためには、パーライトを微細に
し、かつ先に述べたようなセメンタイトネットワークや
厚いセメンタイトを無くす必要がある。Ｃｒはこのよう
なセメンタイトの異常部の出現を抑制しさらに、パーラ
イトを微細にする効果を持っている。しかし、多量の添
加は熱処理後のフェライト中の転移密度を上昇させるた
め、引き抜き加工後の極細線の延性を著しく害すること
になる。従って、Ｃｒの添加量はその効果が期待できる
０．１０％以上としフェライト中の転移密度を増加させ
延性を害することの無い０．３０％以下とする。For Mn, it is desirable to add a small amount of Mn in order to secure the hardenability of steel. However, a large amount of M
The addition of n causes segregation and causes a supercooled structure such as bainite and martensite during patenting, which impairs the wire drawability thereafter, so the content is set to 0.5% or less. In the case of the hyper-eutectoid steel as in the present invention, a cementite network is likely to occur in the microstructure after patenting, and a cementite having a thickness is likely to precipitate. In order to realize high strength and high ductility in this steel, it is necessary to make pearlite fine and to eliminate the cementite network and thick cementite as described above. Cr has the effect of suppressing the appearance of such abnormal portions of cementite and further refining pearlite. However, addition of a large amount increases the dislocation density in the ferrite after heat treatment, and therefore significantly impairs the ductility of the ultrafine wire after drawing. Therefore, the addition amount of Cr is set to 0.10% or more, which is expected to be effective, and 0.30% or less, which does not impair ductility by increasing the transition density in ferrite.
【００２１】ＮｉもＣｒと同じ効果があるため、必要に
よりその効果を発揮する０．１％以上添加する。Ｎｉも
添加量が多くなり過ぎるとフェライト相の延性を低下さ
せるので上限を１．０％とする。Ｃｕは線材の腐食疲労
特性を向上させる元素であるので、ワイヤ被覆ゴムの種
類などによっては、必要によりその効果を発揮する０．
１％以上添加することが望ましい。Ｃｕも添加量が多く
なり過ぎるとフェライト相の延性を低下させるので上限
を０．８％とする。Since Ni also has the same effect as Cr, if necessary, 0.1% or more is added to exhibit the effect. If Ni is added too much, the ductility of the ferrite phase deteriorates, so the upper limit is made 1.0%. Since Cu is an element that improves the corrosion fatigue property of the wire rod, it exhibits an effect as necessary depending on the type of wire-coated rubber.
It is desirable to add 1% or more. If Cu is added too much, the ductility of the ferrite phase will be reduced, so the upper limit is made 0.8%.
【００２２】従来の極細鋼線と同様に、延性を確保する
ためＳの含有量を０．０２０％以下とし、ＰもＳと同様
に線材の延性を害するのでその含有量を０．０２０％以
下とするのが望ましい。極細線の延性を低下させる原因
としてＡｌ2 Ｏ3 ，Ａｌ2 Ｏ3 −ＭｇＯ等のＡｌ2 Ｏ3
を主成分とする非延性介在物の存在がある。従って、本
発明においては非延性介在物による延性低下を避けるた
めに、鋼中のＡｌ含有量を０．００３％以下にする。Like the conventional ultra-fine steel wire, the content of S is 0.020% or less in order to secure the ductility, and P also impairs the ductility of the wire like S, so the content is 0.020% or less. Is desirable. For Al 2 O 3 cause of reducing the ductility of the extra fine wire, Al 2 O 3 or the like -MgO of Al 2 O 3
There are non-ductile inclusions containing as a main component. Therefore, in the present invention, the Al content in the steel is set to 0.003% or less in order to avoid a decrease in ductility due to non-ductile inclusions.
【００２３】次に、本発明の介在物組成の限定理由に関
して説明する。鋼線中の非金属介在物は、介在物融点が
低い方が加工時の介在物の伸びが大きく線材圧延加工時
の断線防止に有効な事は従来から知られている。しか
し、伸線加工を行ったままの状態で使用するスチールコ
ードなどにおいて介在物の及ぼす疲労特性への影響は明
確ではなかった。Next, the reason for limiting the composition of the inclusions of the present invention will be described. It is conventionally known that the lower the melting point of the inclusions of the non-metallic inclusions in the steel wire, the greater the elongation of the inclusions during processing and the more effective the prevention of disconnection during the wire rod rolling. However, the effect of inclusions on the fatigue properties of steel cords used in the as-drawn state was not clear.
【００２４】本発明者らが研究を進めた結果、疲労特性
を大きく低下させる原因として伸線加工中に形成される
非変形介在物近傍のクラックの存在がある。従って、伸
線ワイヤの疲労特性を向上させることを考えた場合、鋳
片中に含まれる介在物を変形しやすいものにする必要が
ある。図２に示すように、鋳片の介在物組成を、ＭｎＯ
＋ＣａＯ，ＳｉＯ2 ，Ａｌ2Ｏ3 四元系で見た融点１５
００℃以下の組成にすると、鋳片からビレットに分塊圧
延後、および伸線加工過程において伸びた介在物の割合
が急増する。このように鋳片中の介在物組成を調整する
ことで、伸線加工ワイヤの延性および疲労特性が向上す
る。そこで、延性のある介在物を増加させるために鋳
片、線材の介在物組成を図１のイ、ロ、ハ、ニ、ホ、
ヘ、ト、チ、リ、ヌで囲まれる領域Ｉに制御することが
有効である。As a result of the research conducted by the present inventors, there is a crack in the vicinity of a non-deformable inclusion formed during wire drawing as a cause of greatly reducing fatigue properties. Therefore, in consideration of improving the fatigue property of the wire drawing wire, it is necessary to make the inclusions contained in the slab easily deformable. As shown in FIG. 2, the inclusion composition of the cast slab was set to MnO.
+ CaO, SiO 2 , Al 2 O 3 Quaternary system melting point 15
When the composition is set to 00 ° C. or less, the proportion of inclusions stretched after slabbing from a slab to a billet and in the wire drawing process rapidly increases. By adjusting the composition of inclusions in the slab in this way, the ductility and fatigue characteristics of the wire-drawn wire are improved. Therefore, in order to increase the number of inclusions having ductility, the composition of inclusions in the cast slab and the wire is set to a, b, c, d, h in FIG.
It is effective to control the region I surrounded by F, G, C, L, and N.
【００２５】図１の領域Ｉに隣接し、かつ融点が１５０
０℃以下の領域があるが、この領域では初晶としてムラ
イト（ＭＵＬＬＩＴＥ）、コランダム（ＣＲＯＵＮＤＵ
Ｍ）、ＣａＡｌ12Ｏ19，ＣａＡｌ4 Ｏ7 の伸線時に断線
の原因となる硬質な高融点相が晶出するので介在物組成
としては望ましくない。本発明者らが研究を進めた結
果、図３に示すように、介在物組成が図１の領域Ｉに存
在する割合が増えるに従って疲労特性は向上する。ま
た、領域Ｉに存在する割合が８０％近傍で疲労特性の向
上がほぼ飽和する。従って、図１の領域Ｉには計数され
る介在物の８０％以上が存在する必要がある。Adjacent to region I of FIG. 1 and having a melting point of 150.
There is a region below 0 ℃, but in this region, the primary crystals are mullite and corundum.
M), CaAl 12 O 19 and CaAl 4 O 7 crystallize a hard high melting point phase that causes wire breakage during wire drawing, which is not desirable as an inclusion composition. As a result of the research conducted by the present inventors, as shown in FIG. 3, the fatigue characteristics improve as the proportion of inclusion composition present in the region I of FIG. 1 increases. Further, the improvement of the fatigue characteristics is almost saturated when the ratio of existence in the region I is around 80%. Therefore, it is necessary that 80% or more of the counted inclusions exist in the region I of FIG.
【００２６】以下、製造方法の限定理由について述べ
る。先の鋼組成と含有する介在物が前記範囲内にある鋼
を熱間圧延により、４．０mmφ以上７．０mmφ以下の線
材とする。この時の線径は円相当直径で、実際の断面形
状は、円、楕円、三角などの多角形のいづれでも良い。
４．０mmφ未満の線径とする場合には生産性が著しく低
下する。また、７．０mmφを越えた場合には、調整冷却
において充分な冷却速度が得られないため、７．０mmφ
以下とする。The reasons for limiting the manufacturing method will be described below. A steel having the above steel composition and inclusions contained in the above range is hot-rolled to obtain a wire rod having a diameter of 4.0 mmφ or more and 7.0 mmφ or less. The wire diameter at this time is a circle equivalent diameter, and the actual cross-sectional shape may be any of polygonal shapes such as a circle, an ellipse, and a triangle.
If the wire diameter is less than 4.0 mmφ, the productivity will be significantly reduced. Also, if it exceeds 7.0 mmφ, it is not possible to obtain a sufficient cooling rate in the adjustment cooling, so 7.0 mmφ
Below.
【００２７】また線材圧延後の調整冷却において、初析
セメンタイトが出現すると伸線性が著しく低下するた
め、熱間圧延後の調整冷却の際の線材中心部の冷却速度
をｖとすると ｌｏｇｖ≧０．２０６６×Ｃwt．％＋０．０９９７６ を満足する冷却速度で冷却することで、実質、初析セメ
ンタイトの出現しない組織とする必要がある。Further, in the controlled cooling after the wire rod rolling, the appearance of pro-eutectoid cementite significantly reduces the wire drawability. Therefore, if the cooling rate of the central portion of the wire rod during the controlled cooling after hot rolling is v, logv ≧ 0. 2066 x Cwt. It is necessary to form a structure in which pro-eutectoid cementite does not substantially appear by cooling at a cooling rate satisfying% + 0.09976.
【００２８】これらの熱間圧延線材を伸線加工により線
径を１．１から２．７mmφのワイヤとする。線径を１．
０mmφ以下にすると伸線ワイヤ中にクラックが入るた
め、その後の加工に悪影響を与えるため１．１mmφ以上
とする。また、２．７mmφ以上のワイヤとすると最終製
品線径を０．４以下とする場合に伸線加工後のワイヤ延
性面で良好な結果を得ることができないので最終パテン
ティング処理前の線径を２．７mmφ以下とする。この
時、伸線加工は引き抜き加工でもローラーダイスのどち
らを用いても良い。These hot-rolled wire rods are drawn to obtain wires having a wire diameter of 1.1 to 2.7 mmφ. Wire diameter is 1.
If it is set to 0 mmφ or less, cracks will occur in the wire drawing wire, which will adversely affect the subsequent processing. Also, if the wire diameter is 2.7 mm or more, it is not possible to obtain good results in terms of wire ductility after wire drawing when the final product wire diameter is 0.4 or less. 2.7mmφ or less. At this time, the drawing process may be either a drawing process or a roller die.
【００２９】パテンティング処理により、引張強さが
（５３０＋９８０×Ｃwt．％）MPa に調整された時、真
ひずみで３．４以上４．２以下の加工を施した場合の強
度延性バランスが最も優れている。｛（５３０＋９８０
×Ｃwt．％）−５０｝MPa 以下となった場合、伸線加工
後の引張強さを充分に得ることができない。｛（５３０
＋９８０×Ｃwt．％）＋５０｝MPa 以上となった場合に
は、強度は高いがパーライト組織中にベイナイト組織が
多く出現しているので、伸線加工中の加工硬化率が低下
し、同一減面率での到達強度が低下し、延性も低下す
る。従って、パテンティング処理における引張強さを
｛（５３０＋９８０×Ｃwt．％）±５０｝MPaに調整す
る必要がある。When the tensile strength is adjusted to (530 + 980 × Cwt.%) MPa by the patenting treatment, the best balance of strength and ductility is obtained when the true strain is processed to 3.4 or more and 4.2 or less. ing. {(530 + 980
X Cwt. %) −50} MPa or less, sufficient tensile strength after wire drawing cannot be obtained. {(530
+ 980 × Cwt. %) + 50} MPa or more, the strength is high, but a large amount of bainite structure appears in the pearlite structure, so the work hardening rate during wire drawing decreases and the same area reduction rate is reached. The strength is reduced and the ductility is also reduced. Therefore, it is necessary to adjust the tensile strength in the patenting process to {(530 + 980 × Cwt.%) ± 50} MPa.
【００３０】これらのワイヤは、乾式伸線、湿式伸線の
いづれかあるいは組み合わせで製造されているが、伸線
の過程においてダイスの磨耗を出来るだけ起こしにくく
するため表面にめっきを施すことが望ましい。これらの
めっきはブラスメッキ、Ｃｕめっき、Ｎｉめっきなどが
経済的に望ましいがこれ以外のめっきでも良い。湿式伸
線加工において真歪みで（−１．４３×ｌｏｇＤ＋３．
０９）以上の加工では、強度が上がり過ぎるため疲労特
性が低下する。また、（−１．４３×ｌｏｇＤ＋２．４
９）以下の加工では、３５００MPa 以上の強度を得るこ
とができない。These wires are manufactured by either dry drawing or wet drawing, or a combination thereof, and it is desirable that the surface of the wires be plated in order to minimize abrasion of the die during the drawing process. Brass plating, Cu plating, Ni plating and the like are economically desirable as these platings, but other platings may be used. True strain (-1.43 x logD + 3.
In the processing of 09) or more, since the strength is too high, the fatigue property is deteriorated. In addition, (-1.43 x logD + 2.4
9) In the following processing, it is impossible to obtain a strength of 3500 MPa or more.
【００３１】引張強さが（−１５９０×ｌｏｇＤ＋３３
３０）を越えるとワイヤが脆化してその後の加工が困難
となるので、引張強さを（−１５９０×ｌｏｇＤ＋３３
３０）以下に調整する必要がある。以上の製造工程にお
いて使用する引き抜きダイスに、アプローチ角が１０°
±２°である引き抜き用ダイスを使用することで、従来
の１４°±２°のダイスに比べ、内部に圧縮残留応力を
働かせて伸線加工をすることが可能となり、いっそう優
れた超極細線を製造することが可能となる。The tensile strength is (-1590 × logD + 33).
If it exceeds 30), the wire becomes brittle and subsequent processing becomes difficult, so the tensile strength is (-1590 x logD + 33).
30) The following needs to be adjusted. The drawing die used in the above manufacturing process has an approach angle of 10 °.
By using a drawing die of ± 2 °, it is possible to perform compressive residual stress inside and perform wire drawing, as compared with the conventional 14 ° ± 2 ° dice, making it even more excellent ultrafine wire. Can be manufactured.
【００３２】この製造工程により円相当直径が０．１５
〜０．４mmφのワイヤを製造することで、多くの場合に
この後に行われる撚り線加工において、撚り線の際に捻
りに耐えられるだけの延性を備えさせることができるた
め、素線においても、撚り線においても疲労特性の優れ
たスチールコードを製造することが可能となる。With this manufacturing process, the equivalent circle diameter is 0.15.
By producing a wire of ~ 0.4 mmφ, in many cases, in the twisted wire processing that is performed after this, it is possible to provide ductility that can withstand twisting when twisted, so even in the case of strands, It is possible to manufacture a steel cord having excellent fatigue properties even with a stranded wire.
【００３３】[0033]
【実施例】以下に本発明に基づいてスチールコードを試
作した場合について説明する。転炉出鋼後、二次精錬処
理を行い表１に示した溶鋼組成に成分調整した後に、連
続鋳造法により鋳造を行い、３００×５００mmの鋳片を
製造した。EXAMPLES A case where a steel cord is trial-produced based on the present invention will be described below. After tapping the converter, secondary refining treatment was performed to adjust the composition to the molten steel composition shown in Table 1, and then casting was performed by the continuous casting method to produce a slab of 300 × 500 mm.
【００３４】[0034]
【表１】 [Table 1]
【００３５】さらにこの鋳片を分塊圧延してビレットを
製造し、４．０〜７．０mmφに熱間圧延した後に調整冷
却を行い線材を製造した。調整冷却はステルモア冷却に
て行った。この線材を伸線加工と中間パテンティング処
理により１．２〜２．０mmφのワイヤとした（表２およ
び表３）。Further, this slab was slab-rolled to produce a billet, which was hot-rolled to 4.0-7.0 mmφ and then adjusted and cooled to produce a wire. Conditioned cooling was performed by Stelmore cooling. This wire rod was drawn into a wire having a diameter of 1.2 to 2.0 mm by a drawing process and an intermediate patenting process (Tables 2 and 3).
【００３６】[0036]
【表２】 [Table 2]
【００３７】[0037]
【表３】 [Table 3]
【００３８】この後、最終パテンティング処理を行うこ
とで組織と引張強さを調整し、めっきを行ってから最終
湿式伸線を行った。それぞれの鋼線の製造における、パ
テンティング処理時のワイヤ径、パテンティング処理後
の引張強さ、伸線加工後の最終ワイヤ径は表２および表
３に示される通りである。これらのワイヤ特性を引張試
験、捻回試験、疲労試験により評価した。After that, a final patenting treatment was performed to adjust the structure and tensile strength, plating was performed, and then final wet drawing was performed. In the production of each steel wire, the wire diameter during patenting treatment, the tensile strength after patenting treatment, and the final wire diameter after wire drawing are shown in Tables 2 and 3. These wire properties were evaluated by a tensile test, a twist test, and a fatigue test.
【００３９】表４中の疲労特性は、ハンター疲労試験に
おいて疲労強度を測定し、疲労強度が引張強さの０．３
３以上の場合を◎で表し、０．３以上の場合を○として
表し、０．３未満の場合を×で表した。The fatigue properties in Table 4 are measured by measuring the fatigue strength in the Hunter fatigue test, and the fatigue strength is 0.3 of the tensile strength.
The case of 3 or more was represented by ⊚, the case of 0.3 or more was represented by ◯, and the case of less than 0.3 was represented by x.
【００４０】[0040]
【表４】 [Table 4]
【００４１】また、ハンター疲労試験における疲労強度
は１０6 以下の繰り返しで破壊しない強度を疲労強度と
した（図４）。表中の鋼１〜１１は本発明鋼であり、鋼
１２〜１６は比較鋼である。本発明鋼中、鋼１０と鋼１
１は伸線加工において使用するダイスアプローチ角を１
０°と１４°で比較した水準である。比較鋼１２は鋼組
成が本発明範囲外で製造方法は同じ場合である。比較鋼
１３は鋼成分が本発明範囲であるが、鋳片中の介在物的
中率が本発明鋼より低く、これ以外のワイヤの製造方法
は本発明方法と同じ場合である。比較鋼１４は鋼組成と
介在物組成が同じで熱間圧延後の調整冷却において初析
セメンタイトの出現した場合である。比較鋼１５は鋼組
成および介在物組成が本発明と同じで、最終パテンティ
ング材の引張り強さが本発明法より高くなった場合であ
る。比較鋼１６は鋼組成および介在物組成が本発明と同
じで、最終パテンティング処理後の伸線減面率が本発明
より大きい場合である。The fatigue strength in the hunter fatigue test was defined as the strength that does not break by repeating 10 6 or less (FIG. 4). Steels 1 to 11 in the table are steels of the present invention, and steels 12 to 16 are comparative steels. Among the steels of the present invention, Steel 10 and Steel 1
1 is the die approach angle used in wire drawing
This is the level compared with 0 ° and 14 °. Comparative steel 12 has a steel composition outside the scope of the present invention and the same manufacturing method. Although the steel composition of the comparative steel 13 is within the range of the present invention, the inclusion content ratio in the cast piece is lower than that of the steel of the present invention, and the other wire manufacturing methods are the same as those of the present invention. Comparative Steel 14 has the same steel composition and inclusion composition, and is a case where proeutectoid cementite appears in controlled cooling after hot rolling. Comparative Steel 15 has the same steel composition and inclusion composition as the present invention, and the final patenting material has a higher tensile strength than the method of the present invention. Comparative Steel 16 has the same steel composition and inclusion composition as that of the present invention, and the drawing area reduction rate after the final patenting treatment is larger than that of the present invention.
【００４２】表４より、本発明鋼を用いて製造したワイ
ヤの場合にはいずれも３５００MPa以上の強度と優れた
疲労寿命を持ち合せることが分る。一方、比較鋼１２に
おいてはＣが０．９０％未満であるため鋼成分が本発明
鋼と異なるため３５００MPa 以上の強度が得られていな
い。比較鋼１３においては、３５００MPa 以上の強度が
得られているが鋳片中の介在物組成が本発明鋼と異なる
ため、疲労特性において良好な結果が得られていない。From Table 4, it can be seen that each of the wires produced using the steel of the present invention has a strength of 3500 MPa or more and an excellent fatigue life. On the other hand, in Comparative Steel 12, since C is less than 0.90% and the steel composition is different from that of the steel of the present invention, strength of 3500 MPa or more cannot be obtained. In Comparative Steel 13, a strength of 3500 MPa or more was obtained, but since the composition of inclusions in the cast was different from that of the steel of the present invention, good results were not obtained in terms of fatigue properties.
【００４３】比較鋼１４においては、熱間圧延後に初析
セメンタイトが出現したため、途中で断線が多発し、最
終ワイヤまでの製造が出来なかった。比較鋼１５におい
ては、最終パテンティング処理における引張強さが高す
ぎるため、最終ワイヤでの疲労特性が劣化して良好な結
果が得られていない。比較鋼１６に於いては、最終湿式
伸線の際の減面率が高すぎるため、最終ワイヤでの疲労
特性が劣化して良好な結果が得られていない。In Comparative Steel 14, since pro-eutectoid cementite appeared after hot rolling, many wire breakages occurred on the way and it was not possible to manufacture the final wire. In Comparative Steel 15, since the tensile strength in the final patenting treatment was too high, the fatigue characteristics of the final wire deteriorated and good results were not obtained. In Comparative Steel 16, since the area reduction rate at the final wet drawing is too high, the fatigue property of the final wire deteriorates and a good result cannot be obtained.
【００４４】[0044]
【発明の効果】本発明を用いて０．１５〜０．４mmφの
スチールコードを製造した場合、３５００MPa 以上の引
張強さと優れた疲労特性スチールコードを製造すること
が可能となる。Industrial Applicability When a steel cord having a diameter of 0.15 to 0.4 mm is manufactured by using the present invention, it becomes possible to manufacture a steel cord having a tensile strength of 3500 MPa or more and excellent fatigue characteristics.
【図１】本発明における介在物適性組成範囲を示す図で
ある。FIG. 1 is a diagram showing a suitable composition range of inclusions in the present invention.
【図２】鋼中介在物融点とビレットでの非延性介在物量
との関係を示す図である。FIG. 2 is a diagram showing the relationship between the melting point of inclusions in steel and the amount of non-ductile inclusions in the billet.
【図３】介在物適性率と疲労強度の関係を示す図であ
る。FIG. 3 is a diagram showing a relationship between inclusion suitability and fatigue strength.
【図４】疲労限の決定方法を示す図である。FIG. 4 is a diagram showing a method of determining a fatigue limit.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.5 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 38/16 Ｃ２３Ｃ 30/00 Ｂ (72)発明者 芹川 修道 千葉県君津市君津１番地 新日本製鐵株式 会社君津製鐵所内─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 5 Identification number Reference number in the agency FI Technical indication C22C 38/16 C23C 30/00 B (72) Inventor Shudo Serikawa 1 Kimitsu, Kimitsu-shi, Chiba New Japan Kimitsu Steel Works, Ltd.
Claims (6)
在物組成がＭｎＯ＋ＣａＯ，ＳｉＯ2 ，Ａｌ2 Ｏ3 の四
元系で見た場合に、図１のイ、ロ、ハ、ニ、ホ、ヘ、
ト、チ、リ、ヌで囲まれる領域Ｉとなる介在物が８０％
以上で、パーライト組織で、ブラスめっき、Ｃｕめっ
き、Ｎｉめっきのいづれかを施し、引張強さが、３５０
０MPa 以上、（−１５９０×ｌｏｇＤ＋３３３０）MPa
以下で、円相当直径が０．１５〜０．４mmφであること
を特徴とする疲労強度の優れたスチールコード用鋼線。
但し、 Ｄ：円相当直径（mm）1. By weight%, C: 0.9 to 1.10% Si: 0.4% or less Mn: 0.5% or less P: 0.020% or less S: 0.020% or less Al: 0. In addition to 003% or less, one or both of the following elements are added: Cr: 0.10 to 0.30% Ni: 0.10 to 1.00% Steel consisting of balance iron and unavoidable impurities. When the inclusion composition is viewed as a quaternary system of MnO + CaO, SiO 2 , and Al 2 O 3 , it is shown in FIG.
80% of the inclusions are the region I surrounded by g
As described above, the pearlite structure was subjected to brass plating, Cu plating, or Ni plating, and the tensile strength was 350.
0 MPa or more, (-1590 x logD + 3330) MPa
Below, a steel wire for steel cords having excellent fatigue strength, characterized in that the equivalent circle diameter is 0.15 to 0.4 mmφ.
However, D: Diameter equivalent to circle (mm)
１０〜０．８０％を含む請求項１記載の疲労強度の優れ
たスチールコード用鋼線。2. A steel composition, in% by weight, further comprising Cu: 0.
The steel wire for steel cord having excellent fatigue strength according to claim 1, containing 10 to 0.80%.
在物組成がＭｎＯ＋ＣａＯ，ＳｉＯ2 ，Ａｌ2 Ｏ3 の四
元系で見た場合に、図１のイ、ロ、ハ、ニ、ホ、ヘ、
ト、チ、リ、ヌで囲まれる領域Ｉとなる介在物が８０％
以上に調整したビレットを熱間圧延によって４．０〜
７．０mmφの線材とし、調整冷却により初析セメンタイ
トの存在しない組織とし、伸線加工により１．１から
２．７mmφのワイヤとし、パテンティング処理により引
張強さを｛（５３０＋９８０×Ｃwt％）±５０｝MPa に
調整し、ブラスめっき、Ｃｕめっき、Ｎｉめっきのいづ
れかを行い、真歪で（−１．４３×ｌｏｇＤ＋２．４
９）以上、（−１．４３×ｌｏｇＤ＋３．０９）以下の
加工を行い円相当直径が０．１５〜０．４mmφのワイヤ
とすることを特徴とする請求項１記載の疲労強度の優れ
たスチールコード用鋼線の製造方法。但し、 Ｄ：円相当直径（mm）3. C: 0.9 to 1.10% Si: 0.4% or less Mn: 0.5% or less P: 0.020% or less S: 0.020% or less Al: 0. In addition to 003% or less, one or both of the following elements are added: Cr: 0.10 to 0.30% Ni: 0.10 to 1.00% Steel consisting of balance iron and unavoidable impurities. When the inclusion composition is viewed as a quaternary system of MnO + CaO, SiO 2 , and Al 2 O 3 , it is shown in FIG.
80% of the inclusions are the region I surrounded by g
The billet adjusted as described above is subjected to 4.0 to 4.0 by hot rolling.
The wire rod has a diameter of 7.0 mmφ, and the structure has no pro-eutectoid cementite by adjusting cooling, and the wire has a wire size of 1.1 to 2.7 mmφ, and the tensile strength is {(530 + 980 × Cwt%) ± 50} MPa, and either brass plating, Cu plating, or Ni plating is performed, and the true strain is (-1.43 x logD + 2.4).
The steel having excellent fatigue strength according to claim 1, characterized in that a wire having a circle equivalent diameter of 0.15 to 0.4 mmφ is processed by processing 9) or more and (−1.43 × logD + 3.09) or less. Manufacturing method of steel wire for cord. However, D: Diameter equivalent to circle (mm)
０．１０〜０．８０％を含む鋼である請求項３記載の疲
労強度の優れたスチールコード用鋼線の製造方法。4. The starting steel composition is wt% and further Cu:
The method for producing a steel wire for steel cord having excellent fatigue strength according to claim 3, which is steel containing 0.10 to 0.80%.
がら伸線加工により１．１から２．７mmφのワイヤとす
ることを特徴とする請求項３または４記載の疲労強度の
優れたスチールコード用鋼線の製造方法。5. A steel cord with excellent fatigue strength according to claim 3 or 4, characterized in that after the controlled cooling, a wire of 1.1 to 2.7 mmφ is formed by wire drawing while applying intermediate patenting. Steel wire manufacturing method.
ーチ角が１０°±２°であるダイスによって伸線加工す
ることを特徴とする請求項３，４または５記載の疲労強
度の優れたスチールコード用鋼線の製造方法。6. Steel with excellent fatigue strength according to claim 3, 4 or 5, characterized in that, in the wire drawing after plating, the wire is drawn with a die having an approach angle of 10 ° ± 2 °. Manufacturing method of steel wire for cord.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10270993A JP2888727B2 (en) | 1993-04-28 | 1993-04-28 | Steel wire for steel cord having excellent fatigue strength and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10270993A JP2888727B2 (en) | 1993-04-28 | 1993-04-28 | Steel wire for steel cord having excellent fatigue strength and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06312210A true JPH06312210A (en) | 1994-11-08 |
| JP2888727B2 JP2888727B2 (en) | 1999-05-10 |
Family
ID=14334803
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10270993A Expired - Fee Related JP2888727B2 (en) | 1993-04-28 | 1993-04-28 | Steel wire for steel cord having excellent fatigue strength and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2888727B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008032829A1 (en) * | 2006-09-14 | 2008-03-20 | Bridgestone Corporation | High strength high carbon steel wire and method for manufacture thereof |
| JP2011219836A (en) * | 2010-04-13 | 2011-11-04 | Nippon Steel Corp | Extra fine plated steel wire having excellent adhesiveness to rubber |
| JP2012107353A (en) * | 2010-11-16 | 2012-06-07 | Toyo Tire & Rubber Co Ltd | Rubber reinforcement steel cord and pneumatic radial tire |
| WO2023162615A1 (en) * | 2022-02-22 | 2023-08-31 | 住友電気工業株式会社 | Steel wire |
-
1993
- 1993-04-28 JP JP10270993A patent/JP2888727B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008032829A1 (en) * | 2006-09-14 | 2008-03-20 | Bridgestone Corporation | High strength high carbon steel wire and method for manufacture thereof |
| JP2008069409A (en) * | 2006-09-14 | 2008-03-27 | Bridgestone Corp | High strength high carbon steel wire and producing method therefor |
| US8899087B2 (en) | 2006-09-14 | 2014-12-02 | Bridgestone Corporation | High strength, high carbon steel wire and method of producing the same |
| JP2011219836A (en) * | 2010-04-13 | 2011-11-04 | Nippon Steel Corp | Extra fine plated steel wire having excellent adhesiveness to rubber |
| JP2012107353A (en) * | 2010-11-16 | 2012-06-07 | Toyo Tire & Rubber Co Ltd | Rubber reinforcement steel cord and pneumatic radial tire |
| WO2023162615A1 (en) * | 2022-02-22 | 2023-08-31 | 住友電気工業株式会社 | Steel wire |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2888727B2 (en) | 1999-05-10 |
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