JP2008261028A - High-carbon steel wire rod having excellent wire drawability - Google Patents
High-carbon steel wire rod having excellent wire drawability Download PDFInfo
- Publication number
- JP2008261028A JP2008261028A JP2007105731A JP2007105731A JP2008261028A JP 2008261028 A JP2008261028 A JP 2008261028A JP 2007105731 A JP2007105731 A JP 2007105731A JP 2007105731 A JP2007105731 A JP 2007105731A JP 2008261028 A JP2008261028 A JP 2008261028A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- carbon steel
- steel wire
- pearlite
- hydrogen
- 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.)
- Granted
Links
Images
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
本発明は、例えば、タイヤ補強用スチールコード、スチールベルトコード、ソーワイヤ等に使用される、伸線加工性の優れた高炭素鋼線材に関するものである。 The present invention relates to a high carbon steel wire material having excellent wire drawing workability, which is used for, for example, a steel cord for reinforcing tires, a steel belt cord, a saw wire and the like.
従来、自動車用タイヤ、産業用各種ベルト類などの補強用に使用されているスチールコードや、スチールベルトコード、ソーワイヤなどの極細鋼線は、高炭素鋼の熱間圧延線材に中間伸線と中間パテンティング処理を繰り返し行って所定の線径にした後、最終パテンティング処理を行い、所定の線径まで湿式伸線加工することにより製造される。このような製造工程のうち、中間パテンティング処理については、製造コスト削減の観点から、省略が検討されている。 Conventionally, steel cords used to reinforce automobile tires, various industrial belts, etc., ultra-fine steel wires such as steel belt cords and saw wires, are hot-rolled high-carbon steel wires with intermediate wire and intermediate wires. After the patenting process is repeated to obtain a predetermined wire diameter, the final patenting process is performed, and wet drawing is performed to a predetermined wire diameter. Among such manufacturing processes, the omission of the intermediate patenting process has been studied from the viewpoint of reducing manufacturing costs.
一方、極細鋼線は、軽量化等の観点から高強度化の要求が一段と高まっている。しかしながら、極細鋼線の強度が増加するほど、断線頻度が増加し、生産性が著しく低下するため、中間パテンティング処理を省略して高強度の極細鋼線を製造する際には、伸線加工工程や撚り線工程における断線率の増加が問題になる。したがって、熱間圧延線材から最終パテンティング線径まで伸線加工が可能な伸線加工性の優れた高炭素鋼線材の要求が強まっている。 On the other hand, the demand for increasing the strength of ultrafine steel wires is further increased from the viewpoint of weight reduction and the like. However, as the strength of the ultrafine steel wire increases, the frequency of wire breakage increases and the productivity decreases significantly. Therefore, when producing a high strength ultrafine steel wire without intermediate patenting, An increase in the disconnection rate in the process and the stranded wire process becomes a problem. Accordingly, there is an increasing demand for a high carbon steel wire rod having excellent wire drawing workability that can be drawn from a hot rolled wire rod to a final patenting wire diameter.
このような伸線加工性に優れた鋼線として、析出物、介在物を制御する技術が提案されている（例えば、特許文献１〜３を参照）。また、断面における硬度差を抑制した素材を、ダイスのアプローチ角度および減面率を制御して、伸線加工する技術が提案されている（例えば、特許文献４を参照）。 Techniques for controlling precipitates and inclusions have been proposed as steel wires having excellent wire drawing workability (see, for example, Patent Documents 1 to 3). In addition, a technique has been proposed in which a material in which the hardness difference in the cross section is suppressed is drawn by controlling the approach angle and area reduction rate of the die (see, for example, Patent Document 4).
さらに、中間パテンティング処理を省略する技術として、平均線径が５．０ｍｍ未満の熱間圧延線材における引張強さの最小値及び引張強さのばらつきの規制、破断絞りの最小値などを規制する技術が提案されている（例えば、特許文献５を参照）。また、オーステナイト結晶粒度制御や、パーライトコロニーサイズ制御、初析フェライト、初析セメンタイトの形状制御等により、中間パテンティング処理の省略が可能な圧延線材の線径が４．５ｍｍ以下の伸線加工性の優れた熱間圧延線材が提案されている（例えば、特許文献６を参照）。 Further, as a technique for omitting the intermediate patenting process, the minimum value of the tensile strength and the variation of the tensile strength in the hot rolled wire rod having an average wire diameter of less than 5.0 mm, the minimum value of the squeeze drawing, and the like are regulated. Techniques have been proposed (see, for example, Patent Document 5). In addition, the wire diameter of rolled wire rods with a wire diameter of 4.5 mm or less, which can omit intermediate patenting treatment, is possible by controlling the grain size of austenite, control of pearlite colony size, shape control of proeutectoid ferrite and proeutectoid cementite Has been proposed (see, for example, Patent Document 6).
しかしながら、中間パテンティングを省略した場合の熱間圧延線材の伸線加工性と、最終伸線及び撚り線工程における高強度極細鋼線の断線との関係や断線原因の詳細は、よく分かっていない。したがって、その対策技術も十分に確立されていないのが実態であり、中間パテンティング処理を省略した際の断線率の低下技術には限界があった。
本発明は、上記の実状に鑑みてなされたものであって、最終線径が０．０５〜０．４ｍｍである高強度極細鋼線の製造において、中間パテンティングの省略を可能にし、伸線加工工程及び撚り線工程の断線率の低下を実現することが可能な、伸線加工性の優れた高炭素鋼圧延線材を提供することを目的とするものである。 The present invention has been made in view of the above situation, and in the production of a high-strength ultrafine steel wire having a final wire diameter of 0.05 to 0.4 mm, it is possible to omit intermediate patenting, and wire drawing. An object of the present invention is to provide a high carbon steel rolled wire rod having excellent wire drawing workability that can realize a reduction in the disconnection rate in the processing step and the stranded wire step.
本発明は、熱間圧延線材の非拡散性水素量、パーライト分率及びラメラー間隔を制御することにより、熱間圧延線材の伸線加工性が向上し、高強度極細鋼線の製造工程における断線頻度を抑制することができるという知見に基づくものであり、その要旨は以下のとおりである。 By controlling the amount of non-diffusible hydrogen, the pearlite fraction, and the lamellar spacing of the hot-rolled wire, the present invention improves the hot-drawn wire drawing workability, and breaks in the manufacturing process of high-strength ultrafine steel wire This is based on the knowledge that the frequency can be suppressed, and the gist thereof is as follows.
（１） 質量％で、Ｃ：０．８０〜１．２０％、Ｓｉ：０．０１〜１．５０％、Ｍｎ：０．０５〜１．００％を含有し、残部がＦｅ及び不可避的不純物からなり、パーライトの面積分率が９５％以上であり、ラメラー間隔が０．０８〜０．３５μｍであり、非拡散性水素量が０．５ｐｐｍ以下であることを特徴とする伸線加工性の優れた高炭素鋼線材。
（２） 更に、質量％で、Ｃｒ：０．０１〜１．００％、Ｎｂ：０．００１〜０．２００％、Ｖ：０．０１〜０．５０％の少なくとも１種又は２種以上を含有することを特徴とする上記（１）に記載の伸線加工性の優れた高炭素鋼線材。
（３） 更に、質量％で、Ｎｉ：０．０１〜２．００％、Ｃｏ：０．０１〜１．００％の一方又は双方を含有することを特徴とする上記（１）又は（２）に記載の伸線加工性の優れた高炭素鋼線材。
（４） 更に、質量％で、Ｍｏ：０．０１〜０．５０％、Ｂ：０．０００１〜０．００７０％の一方又は双方を含有することを特徴とする上記（１）〜（３）の何れか一項に記載の伸線加工性の優れた高炭素鋼線材。
(1) By mass%, C: 0.80 to 1.20%, Si: 0.01 to 1.50%, Mn: 0.05 to 1.00%, the balance being Fe and inevitable impurities The pearlite has an area fraction of 95% or more, a lamellar spacing of 0.08 to 0.35 μm, and a non-diffusible hydrogen content of 0.5 ppm or less. Excellent high carbon steel wire.
(2) Furthermore, at least 1 type or 2 types or more of Cr: 0.01-1.00%, Nb: 0.001-0.200%, V: 0.01-0.50% by the mass%. The high carbon steel wire material having excellent wire drawing workability as described in (1) above.
(3) The above (1) or (2), further comprising one or both of Ni: 0.01 to 2.00% and Co: 0.01 to 1.00% by mass% A high carbon steel wire rod excellent in wire drawing workability described in 1.
(4) The above (1) to (3), characterized by further containing one or both of Mo: 0.01 to 0.50% and B: 0.0001 to 0.0070% by mass%. A high carbon steel wire rod excellent in wire drawing workability according to any one of the above.
以上のように、本発明の伸線加工性の優れた高炭素鋼線材では、熱間圧延線材のラメラー間隔、パーライト分率及び非拡散性水素量を制御することによって、高強度の極細鋼線を製造する際の断線回数を低減させることができ、中間パテンティング処理の省略が可能になるなど、産業上の貢献が極めて顕著である。 As described above, in the high carbon steel wire rod excellent in wire drawing workability of the present invention, by controlling the lamellar spacing, pearlite fraction and non-diffusible hydrogen content of the hot rolled wire rod, The contribution to the industry is extremely remarkable, such as the number of disconnections in the manufacturing process can be reduced and the intermediate patenting process can be omitted.
以下、本発明の伸線加工性の優れた高炭素鋼線材について詳細に説明する。
本発明者らは、中間パテンティング処理を省略した場合の熱間圧延線材の伸線加工性に及ぼす組織因子等の影響、熱間圧延線材の組織因子と最終伸線工程や撚り線工程における断線頻度との関係等を詳細に解析した。その結果、最終伸線工程、撚り線工程における断線は、介在物以外に熱間圧延線材中に存在する非拡散性水素が著しく影響することを見出した。さらに、熱間圧延線材の伸線性加工性は、パーライト組織におけるセメンタイト間の間隔であるラメラー間隔及びパーライト組織分率が影響することを明確にした。
Hereinafter, the high carbon steel wire wire excellent in the wire drawing workability of the present invention will be described in detail.
The present inventors, the influence of the structure factor on the wire drawing workability of the hot rolled wire when the intermediate patenting process is omitted, the structure factor of the hot rolled wire and the disconnection in the final wire drawing process and the stranded wire process The relationship with frequency was analyzed in detail. As a result, it was found that the non-diffusible hydrogen present in the hot-rolled wire rod significantly affects the disconnection in the final wire drawing process and the stranded wire process in addition to the inclusions. Furthermore, it has been clarified that the drawability of the hot-rolled wire is affected by the lamellar spacing, which is the spacing between cementites in the pearlite structure, and the pearlite structure fraction.
本発明で目的とする中間パテンティング処理を省略し、なお且つ最終伸線及び撚り線工程での断線を防止する上で最も重要となる非拡散性水素の限定理由を以下に説明する。
図１は、熱間圧延線材中の非拡散性水素量と、中間パテンティング処理を省略した最終伸線及び撚り線工程での断線回数との関係を測定した解析結果の一例である。
図１に測定結果から、非拡散性水素量が低下するほど、断線回数が低下することがわかる。ここで、非拡散性水素量が０．５ｐｐｍ以下で特に断線回数が低下することから、本発明では、非拡散性水素量の上限を０．５ｐｐｍ以下に限定した。また、断線率を安定的に低下する上で、更に好ましい条件は０．３ｐｐｍ以下である。
The reason why the non-diffusible hydrogen is most important in omitting the intermediate patenting treatment intended in the present invention and preventing disconnection in the final wire drawing and stranded wire processes will be described below.
FIG. 1 is an example of an analysis result obtained by measuring the relationship between the amount of non-diffusible hydrogen in a hot-rolled wire and the number of wire breaks in a final wire drawing and stranded wire process in which intermediate patenting is omitted.
From the measurement results in FIG. 1, it can be seen that the number of disconnections decreases as the amount of non-diffusible hydrogen decreases. Here, since the number of disconnections particularly decreases when the amount of non-diffusible hydrogen is 0.5 ppm or less, the upper limit of the amount of non-diffusible hydrogen is limited to 0.5 ppm or less in the present invention. Further, in order to stably reduce the disconnection rate, a more preferable condition is 0.3 ppm or less.
本発明の限界拡散性水素量は、熱間圧延線材を１００ｍｍに切断し、線材表層のスケールをエメリー紙で除去した後、ガスクロマトグラフを用いた昇温水素分析装置で測定する。より具体的には、以下の(ｉ)〜(iii)に示す通りである。
（ｉ） 線材を室温から８００℃まで１００℃／ｈｒの昇温速度で加熱し、線材から放出される水素量を測定する。
（ii） 上記（ｉ）で昇温した線材を昇温水素分析装置内で室温まで冷却し、再び室温から８００℃まで１００℃／ｈｒの昇温速度で加熱し、放出される水素量、すなわち「バックグラウンドの水素量」を測定する。
（iii） 上記（ｉ）の水素量から上記（ii）の水素量を引いた値を線材中に含まれる「非拡散性水素量」として求める。
The critical diffusible hydrogen content of the present invention is measured with a temperature rising hydrogen analyzer using a gas chromatograph after cutting the hot-rolled wire to 100 mm and removing the scale of the wire surface layer with emery paper. More specifically, it is as shown in the following (i) to (iii).
(I) The wire is heated from room temperature to 800 ° C. at a rate of 100 ° C./hr, and the amount of hydrogen released from the wire is measured.
(Ii) The wire heated up in the above (i) is cooled to room temperature in a temperature rising hydrogen analyzer, heated again from room temperature to 800 ° C. at a temperature rising rate of 100 ° C./hr, and the amount of released hydrogen, Measure the “background hydrogen content”.
(Iii) A value obtained by subtracting the hydrogen amount of (ii) from the hydrogen amount of (i) above is determined as the “non-diffusible hydrogen amount” contained in the wire.
上記(ｉ)〜(iii)の手順に従った測定結果の一例として、高炭素鋼線材における非拡散性水素の水素放出速度曲線を図２に示す。なお、図２中に示す非拡散性水素量（△）は、上記（ｉ）の実測値（○）から上記(ii)のバックグラウンドの水素量（□）を引いた値であり、４００〜６５０℃で放出される水素量である。 As an example of the measurement results according to the procedures (i) to (iii) above, a hydrogen release rate curve of non-diffusible hydrogen in a high carbon steel wire is shown in FIG. Note that the non-diffusible hydrogen amount (Δ) shown in FIG. 2 is a value obtained by subtracting the background hydrogen amount (□) of (ii) from the actually measured value (◯) of (i) above. This is the amount of hydrogen released at 650 ° C.
鋼材中の水素には、大きく分類すると拡散性水素と非拡散性水素との２種類がある。このうち、拡散性水素は、室温付近で鋼材中を拡散できる水素であり、転位、粒界、空孔にトラップされた原子状の水素であると理解されている。また、拡散性水素が遅れ破壊などの水素脆化を引き起こす水素であると考えられている。一方、非拡散性水素は、室温付近では拡散できない水素であり、遅れ破壊などの水素脆化には関与しない水素であると考えられている。 Hydrogen in steel is roughly classified into two types, diffusible hydrogen and non-diffusible hydrogen. Of these, diffusible hydrogen is hydrogen that can diffuse in steel near room temperature, and is understood to be atomic hydrogen trapped in dislocations, grain boundaries, and vacancies. In addition, diffusible hydrogen is considered to be hydrogen that causes hydrogen embrittlement such as delayed fracture. On the other hand, non-diffusible hydrogen is hydrogen that cannot diffuse near room temperature, and is considered to be hydrogen that does not participate in hydrogen embrittlement such as delayed fracture.
非拡散性水素の鋼中での存在状態は明確になっていないものの、本発明者らは非拡散性水素がＭｎＳ、Ａｌ２Ｏ３などの介在物にトラップされた水素であり、介在物／地鉄界面の空隙に分子状の水素として存在していることをほぼ明確にした。伸線加工の工程で介在物／地鉄界面も変形されるため、新たな面（新生面）が現れる。さらに、本発明者らは、新生面には分子状水素を原子状水素にしやすくする触媒作用があることを明確にした。したがって、線材中に分子状の非拡散性水素が多量に存在すると、伸線加工の工程で、分子状の非拡散性水素の一部が原子状の拡散性水素に変化するため、断線を引き起こすと考えられる。 Although the existence state of non-diffusible hydrogen in the steel is not clear, the present inventors are non-diffusible hydrogen trapped in inclusions such as MnS and Al 2 O 3 , and the inclusion / It was almost clarified that it exists as molecular hydrogen in the voids at the iron-iron interface. Since the inclusion / base metal interface is also deformed in the wire drawing process, a new surface (new surface) appears. Furthermore, the present inventors clarified that the nascent surface has a catalytic action that facilitates the conversion of molecular hydrogen into atomic hydrogen. Therefore, if a large amount of molecular non-diffusible hydrogen is present in the wire, a part of the molecular non-diffusible hydrogen changes to atomic diffusible hydrogen during the wire drawing process, causing disconnection. it is conceivable that.
高炭素鋼圧延線材の非拡散性水素量は、以下の（Ａ）〜（Ｆ）に示す方法のうち、２つ以上の方法によって低減することができる。
（Ａ） 製鋼時の溶鋼中の水素量を脱ガス処理によって２．０ｐｐｍ以下に低減する。より好ましくは、１．５ｐｐｍ以下に制御する。
（Ｂ） ＭｎＳ、Ａｌ２Ｏ３など硫化物、酸化物及びこれらの複合の介在物サイズの低減及び介在物数を低減する。特に好ましい条件は介在物サイズの低減であり、最大厚みを２０μｍ以下にする。介在物サイズの低減及び介在物数を低減するためには、Ｓが０．０１％以下、Ａｌが０．００５％以下、Ｏが０．００２５％以下にすることが好ましい条件である。
（Ｃ） 連続鋳造時の凝固後の冷却速度を低下させる。特に、８００〜４００℃の平均冷却速度を３００℃／時間未満とするのが好ましい条件である。
（Ｄ） 熱間線材圧延の際のビレット加熱温度を高温にし、更に加熱保定時間を長くする。好ましい条件は、加熱温度が１１００℃以上、保定時間が３０分以上である。
（Ｅ） 熱間圧延後の線材の冷却速度を低下させる。特に、パーライト変態後の冷却速度、具体的には５００〜１００℃の平均冷却速度を１０℃／秒以下とする。
（Ｆ） 熱間圧延後の線材を３００〜６００℃の温度範囲に加熱する。
The amount of non-diffusible hydrogen in the high carbon steel rolled wire can be reduced by two or more methods among the methods shown in the following (A) to (F).
(A) The amount of hydrogen in the molten steel during steelmaking is reduced to 2.0 ppm or less by degassing. More preferably, it is controlled to 1.5 ppm or less.
(B) Reduction of the inclusion size and the number of inclusions of sulfides, oxides such as MnS and Al 2 O 3 and their composites. A particularly preferable condition is to reduce the inclusion size, and the maximum thickness is set to 20 μm or less. In order to reduce the inclusion size and the number of inclusions, it is preferable that S is 0.01% or less, Al is 0.005% or less, and O is 0.0025% or less.
(C) The cooling rate after solidification during continuous casting is reduced. In particular, an average cooling rate of 800 to 400 ° C. is preferably less than 300 ° C./hour.
(D) The billet heating temperature during hot wire rolling is increased, and the heating and holding time is further increased. Preferred conditions are a heating temperature of 1100 ° C. or higher and a holding time of 30 minutes or longer.
(E) Decrease the cooling rate of the wire after hot rolling. In particular, the cooling rate after pearlite transformation, specifically, the average cooling rate of 500 to 100 ° C. is set to 10 ° C./second or less.
(F) The wire after hot rolling is heated to a temperature range of 300 to 600 ° C.
なお、線材の非拡散性水素量を低減させるためには、上記（Ａ）〜（Ｆ）の中から２つ以上の方法を用いることが重要であるが、具体的な選択は個々の設備能力、生産性などの観点に立って、決定されるべきものである。 In order to reduce the amount of non-diffusible hydrogen in the wire, it is important to use two or more methods from the above (A) to (F). It should be determined from the standpoint of productivity.
次に、熱間圧延線材の組織形態の制御による伸線加工性の向上について説明する。
熱間圧延線材の組織は、強度と伸線加工性を両立させるため、パーライト組織であることが好ましい。これは、粒界フェライトやベイナイトが存在すると伸線加工性が劣化し、最終伸線工程及び撚り線工程での断線が発生しやすくなるためである。したがって、本発明の熱間圧延線材は、パーライト組織の分率を９５％以上に限定する。更に好ましい条件は、９８％以上である。
Next, improvement of wire drawing workability by controlling the structure of the hot rolled wire will be described.
The structure of the hot rolled wire rod is preferably a pearlite structure in order to achieve both strength and wire drawing workability. This is because the presence of grain boundary ferrite or bainite deteriorates the wire drawing workability, and breaks easily in the final wire drawing process and the stranded wire process. Therefore, the hot rolled wire rod of the present invention limits the fraction of the pearlite structure to 95% or more. Further preferable conditions are 98% or more.
さらに、熱間圧延線材のパーライトのラメラー間隔を０．３５μｍ以下にすることにより、圧延線材の伸線工程で内部欠陥の発生を抑制することができる。伸線工程で発生した内部欠陥は、最終パテンティング処理後の最終伸線工程及び撚り線工程での断線の原因になる。したがって、パーライトのラメラー間隔の上限値を０．３５μｍに限定することが必要である。一方、パーライトのラメラー間隔を０．０８μｍ未満にすると、熱間圧延線材の強度が高くなり、伸線加工性が劣化するため、その下限値を０．０８μｍに限定した。 Furthermore, by setting the pearlite lamellar spacing of the hot-rolled wire rod to 0.35 μm or less, it is possible to suppress the occurrence of internal defects in the drawing step of the rolled wire rod. Internal defects generated in the wire drawing process cause disconnection in the final wire drawing process and the stranded wire process after the final patenting process. Therefore, it is necessary to limit the upper limit of the pearlite lamellar spacing to 0.35 μm. On the other hand, when the lamellar spacing of pearlite is less than 0.08 μm, the strength of the hot-rolled wire becomes high and the wire drawing workability deteriorates, so the lower limit is limited to 0.08 μm.
熱間圧延線材のパーライト分率、パーライトのラメラー間隔は、特に、熱間圧延後の冷却速度及び化学成分によって変化する。後述する本発明の化学成分の範囲内であれば、熱間圧延後の８００〜５００℃の平均冷却速度を５〜２５℃／ｓとすることによって、パーライト分率９５％以上、ラメラー間隔０．０８〜０．３５μｍに制御することが可能となる。なお、平均冷却速度が５℃未満では、ラメラー間隔が０．３５μｍを超えやすく、また、パーライト分率が９５％を下回る可能性が高くなる。一方、平均冷却速度が２５℃／ｓを超えると、ラメラー間隔が０．０８未満になりやすく、更に、ベイナイトなどの過冷組織が発生しパーライト分率が９５％を下回る頻度が増加する。以上のことから、熱間圧延線材の８００〜５００℃の平均冷却速度は、５〜２５℃／ｓとすることが好ましい。 The pearlite fraction of the hot-rolled wire and the lamellar spacing of the pearlite vary depending on the cooling rate and chemical composition after hot rolling. Within the range of the chemical components of the present invention described later, the average cooling rate at 800 to 500 ° C. after hot rolling is 5 to 25 ° C./s, so that the pearlite fraction is 95% or more and the lamellar spacing is 0. It becomes possible to control to 08 to 0.35 μm. If the average cooling rate is less than 5 ° C., the lamellar interval tends to exceed 0.35 μm, and the pearlite fraction is likely to be less than 95%. On the other hand, when the average cooling rate exceeds 25 ° C./s, the lamellar interval tends to be less than 0.08, and further, a supercooled structure such as bainite is generated, and the frequency of the pearlite fraction falling below 95% increases. From the above, the average cooling rate of 800 to 500 ° C. of the hot-rolled wire is preferably 5 to 25 ° C./s.
パーライト分率は、走査型電子顕微鏡で倍率が２０００〜５０００で２０視野以上を写真撮影し、画像処理によってパーライト組織の面積分率を測定し、その平均値を求めた値である。また、パーライトのラメラー間隔の測定は、走査型電子顕微鏡を用いて、倍率が５０００〜１００００で２０視野以上を写真撮影し、その平均値を求めて行えばよい。 The pearlite fraction is a value obtained by taking an image of 20 or more fields of view with a scanning electron microscope at a magnification of 2000 to 5000, measuring the area fraction of the pearlite structure by image processing, and obtaining the average value. Further, the measurement of the pearlite lamellar spacing may be performed by taking 20 or more fields of view at a magnification of 5000 to 10,000 using a scanning electron microscope, and obtaining the average value.
次に、本発明による高炭素鋼線材の成分を限定した理由について説明する。
（Ｃ：０．８０〜１．２０％）
Ｃは、最終パテンティング処理後の引張強さの増加及び伸線加工硬化率を高める効果があり、より少ない伸線加工歪で極細鋼線の引張強さを高めることができる。しかしながら、Ｃが０．８０％未満では本発明の目的とする高強度の極細鋼線を製造することが困難となり、一方、Ｃが１．２０％を超えるとパテンティング処理時に初析セメンタイトがオーステナイト粒界に析出して伸線加工性が劣化し、伸線加工工程又は撚り線加工工程で断線が頻発してしまう。このため、Ｃを０．８０〜１．２０％の範囲に限定した。
Next, the reason why the components of the high carbon steel wire according to the present invention are limited will be described.
(C: 0.80 to 1.20%)
C has the effect of increasing the tensile strength after the final patenting treatment and increasing the wire drawing work hardening rate, and can increase the tensile strength of the ultra fine steel wire with less wire drawing strain. However, if C is less than 0.80%, it is difficult to produce the high strength ultrafine steel wire of the present invention. On the other hand, if C exceeds 1.20%, proeutectoid cementite is austenite during patenting. It precipitates at the grain boundary and wire drawing workability deteriorates, and disconnection frequently occurs in the wire drawing process or the stranded wire process. For this reason, C was limited to the range of 0.80 to 1.20%.
（Ｓｉ：０．０１〜１．５０％）
Ｓｉは、パーライト中のフェライトを強化させるためと鋼の脱酸のために有効な元素である。しかしながら、Ｓｉが０．０１％未満では上記の効果が期待できず、一方、Ｓｉが１．５％を超えると伸線加工性に対して有害な硬質のＳｉＯ２系介在物が発生しやすくなる。このため、Ｓｉを０．０１〜１．５０％の範囲に制限した。
(Si: 0.01-1.50%)
Si is an effective element for strengthening ferrite in pearlite and for deoxidizing steel. However, if the Si content is less than 0.01%, the above effect cannot be expected. On the other hand, if the Si content exceeds 1.5%, hard SiO 2 inclusions harmful to the wire drawing workability are likely to occur. . For this reason, Si was limited to the range of 0.01 to 1.50%.
（Ｍｎ：０．０５〜１．００％）
Ｍｎは、脱酸、脱硫のために必要であるばかりでなく、鋼の焼入性を向上させパテンティング処理後の引張強さを高めるために有効な元素である。しかしながら、Ｍｎが０．０５％未満では上記の効果が得られず、一方、Ｍｎが１．００％を超えると上記の効果が飽和し、更にパテンティング処理時のパーライト変態を完了させるための処理時間が長くなりすぎて生産性が低下してしまう。このため、Ｍｎを０．０５〜１．００％の範囲に限定した。
(Mn: 0.05-1.00%)
Mn is an element effective not only for deoxidation and desulfurization but also for improving the hardenability of the steel and increasing the tensile strength after the patenting treatment. However, if Mn is less than 0.05%, the above effect cannot be obtained. On the other hand, if Mn exceeds 1.00%, the above effect is saturated, and further, a treatment for completing the pearlite transformation during the patenting process. The time will be too long and productivity will decrease. For this reason, Mn was limited to 0.05 to 1.00%.
本発明による高炭素鋼線材においては、上記の元素に加えて、ラメラー間隔を微細化させるための元素として、Ｃｒ、Ｎｂ、Ｖの少なくとも１種又は２種以上を添加してもよい。また、伸線加工性を高めるための元素として、Ｎｉ、Ｃｏの一方又は双方を添加してもよい。さらに、焼入れ性を高めるための元素として、Ｍｏ、Ｂの一方又は双方を添加してもよい。以下、これらの成分を限定した理由について説明する。 In the high carbon steel wire according to the present invention, in addition to the above elements, at least one of Cr, Nb and V may be added as an element for refining the lamellar spacing. Moreover, you may add one or both of Ni and Co as an element for improving wire drawing workability. Furthermore, you may add one or both of Mo and B as an element for improving hardenability. Hereinafter, the reason for limiting these components will be described.
（Ｃｒ：０．０１〜１．００％）
Ｃｒは、パーライトのラメラー間隔を微細化し、最終パテンティング処理後の引張強さを高めるとともに、特に伸線加工硬化率を向上させる有効な元素である。しかしながら、Ｃｒが０．０１％未満では効果が小さく、一方、Ｃｒが１．００％を超えるとパテンティング処理時のパーライト変態終了時間が長くなり生産性が低下してしまう。このため、Ｃｒは０．０１〜１．００％の範囲とすることが好ましい。
(Cr: 0.01-1.00%)
Cr is an effective element that refines the lamellar spacing of pearlite, increases the tensile strength after the final patenting treatment, and improves the wire drawing work hardening rate. However, if the Cr content is less than 0.01%, the effect is small. On the other hand, if the Cr content exceeds 1.00%, the pearlite transformation end time during the patenting process becomes long and the productivity is lowered. For this reason, it is preferable to make Cr into the range of 0.01 to 1.00%.
（Ｎｂ：０．００１〜０．２００％）
Ｎｂは、パーライトのラメラー間隔を微細化し、パテンティング処理後の引張強さを高める効果があり、更に最終パテンティング処理時のオーステナイト粒の細粒化効果を有する。しかしながら、Ｎｂが０．００１％未満ではその効果が小さく、一方、Ｎｂが０．２００％を超えて添加されてもその効果が飽和してしまう。このため、Ｎｂは０．００１〜０．２００％の範囲とすることが好ましい。
(Nb: 0.001 to 0.200%)
Nb has the effect of reducing the lamellar spacing of pearlite and increasing the tensile strength after the patenting treatment, and further has the effect of refining austenite grains during the final patenting treatment. However, if Nb is less than 0.001%, the effect is small. On the other hand, even if Nb exceeds 0.200%, the effect is saturated. For this reason, it is preferable to make Nb into the range of 0.001 to 0.200%.
（Ｖ：０．０１〜０．５０％）
Ｖは、パーライトのラメラー間隔を微細化し、パテンティング処理後の引張強さを高める効果がある。しかしながら、この効果はＶが０．０１％未満ではその効果が小さく、一方、Ｖが０．５０％を超えるとその効果が飽和してしまう。このため、Ｖは０．０１〜０．５０％の範囲とすることが好ましい。
(V: 0.01 to 0.50%)
V has the effect of reducing the lamellar spacing of pearlite and increasing the tensile strength after patenting. However, this effect is small when V is less than 0.01%, whereas the effect is saturated when V exceeds 0.50%. For this reason, it is preferable to make V into the range of 0.01 to 0.50%.
（Ｎｉ：０．０１〜２．００％）
Ｎｉは、パテンティング処理時に変態生成するパーライトを伸線加工性の良好なものにする作用を有する。しかしながら、Ｎｉが０．０１％未満ではその効果が小さく、一方、Ｎｉが２．００％を超えても添加量に見合うだけの効果が発揮できない。このため、Ｎｉは０．０１〜２．００％の範囲とすることが好ましい。
(Ni: 0.01-2.00%)
Ni has an effect of making pearlite generated by transformation during the patenting process have good wire drawing workability. However, if Ni is less than 0.01%, the effect is small. On the other hand, even if Ni exceeds 2.00%, the effect corresponding to the added amount cannot be exhibited. For this reason, it is preferable to make Ni into the range of 0.01 to 2.00%.
（Ｃｏ：０．０１〜１．００％）
Ｃｏは、熱間圧延線材及び最終パテンティング処理後の鋼線の伸線加工性を高める作用がある。しかしながら、Ｃｏが０．０１％未満ではその効果が小さく、一方、Ｃｏが１．００％を超えても添加量に見合う効果が発揮できない。このため、Ｃｏは０．０１〜１．００％の範囲とすることが好ましい。
(Co: 0.01-1.00%)
Co has the effect of enhancing the wire drawing workability of the hot-rolled wire and the steel wire after the final patenting treatment. However, if Co is less than 0.01%, the effect is small. On the other hand, even if Co exceeds 1.00%, an effect commensurate with the amount of addition cannot be exhibited. For this reason, it is preferable to make Co into the range of 0.01 to 1.00%.
（Ｍｏ：０．０１〜０．５０％）
Ｍｏは、焼入性向上効果により、パテンティング処理時の強度を増加させる効果がある。しかしながら、Ｍｏが０．０１％未満ではその効果が小さく、一方、Ｍｏが０．５０％を超えても熱間圧延後の組織に伸線加工性を劣化させるベイナイト発生しやすくなる。このため、Ｍｏは０．０１〜０．５０％の範囲とすることが好ましい。
(Mo: 0.01 to 0.50%)
Mo has the effect of increasing the strength during the patenting process due to the effect of improving hardenability. However, if the Mo content is less than 0.01%, the effect is small. On the other hand, even if the Mo content exceeds 0.50%, bainite is easily generated in the microstructure after hot rolling. For this reason, it is preferable to make Mo into the range of 0.01 to 0.50%.
（Ｂ：０．０００１〜０．００７０％）
Ｂは、焼入性の向上効果によりパテンティング処理後の強度を向上させるために添加する。しかしながら、Ｂが０．０００１％未満ではその効果が小さく、一方、Ｂが０．００７０％を超えもその効果が飽和してしまう。このため、Ｂは０．０００１〜０．００７０％の範囲とすることが好ましい。
(B: 0.0001 to 0.0070%)
B is added in order to improve the strength after the patenting treatment due to the effect of improving hardenability. However, when B is less than 0.0001%, the effect is small. On the other hand, when B exceeds 0.0070%, the effect is saturated. For this reason, it is preferable to make B into the range of 0.0001 to 0.0070%.
なお、その他の元素については、特に限定しないが、Ｐ：０．０１％以下、Ｓ：０．０１％以下、Ｎ：０．００７％以下が好ましい範囲である。また、Ａｌは０．００５％を超えると鋼中の介在物の中で最も硬質なＡｌ２Ｏ３系介在物が生成しやすくなり、伸線加工又は撚り線加工の際の断線原因となる。このため、Ａｌは０．００５％以下が好ましい範囲である。 In addition, although it does not specifically limit about another element, P: 0.01% or less, S: 0.01% or less, N: 0.007% or less are a preferable range. On the other hand, if Al exceeds 0.005%, the hardest Al 2 O 3 inclusions among the inclusions in the steel are likely to be generated, which causes wire breakage during wire drawing or stranded wire processing. For this reason, 0.005% or less of Al is a preferable range.
以下、実施例により本発明の効果を更に具体的に説明する。なお、本発明は、以下の実施例に限定されるものではなく、その要旨を変更しない範囲で適宜変更して実施することができる。 Hereinafter, the effects of the present invention will be described more specifically with reference to examples. In addition, this invention is not limited to a following example, In the range which does not change the summary, it can change suitably and can implement.
表１に供試材の化学組成を示す。なお、表１の空欄は、成分元素を意図的に添加していないことを意味する。これらの供試材を熱間圧延し、線径５．５ｍｍの鋼線を得た。なお、熱間圧延後の、８００℃から５００℃までの平均冷却速度を変化させた。得られた鋼線に、中間パテンティング処理を省略し、線径１．６ｍｍまで一次伸線加工（乾式伸線）を施した。その後、最終パテンティング処理、ブラスめっき処理を行い、引き続き伸線速度が９００ｍ／分の条件で線径０．２ｍｍまで湿式伸線加工を行った。その後、線径０．２ｍｍの極細鋼線の撚り線加工を行った。 Table 1 shows the chemical composition of the test materials. In addition, the blank of Table 1 means that the component element is not added intentionally. These test materials were hot-rolled to obtain steel wires having a wire diameter of 5.5 mm. In addition, the average cooling rate from 800 degreeC to 500 degreeC after hot rolling was changed. The obtained steel wire was subjected to primary wire drawing (dry wire drawing) up to a wire diameter of 1.6 mm, omitting the intermediate patenting treatment. Thereafter, final patenting treatment and brass plating treatment were performed, and then wet wire drawing was performed to a wire diameter of 0.2 mm under the condition that the wire drawing speed was 900 m / min. Then, the strand wire process of the ultra fine steel wire with a wire diameter of 0.2 mm was performed.
表２には、各高炭素鋼線材の製造条件、上述した非拡散性水素量の制御方法（Ａ）〜（Ｆ）、熱間圧延後の冷却速度、高炭素鋼線材のラメラー間隔、パーライト組織分率、非拡散性水素量、湿式伸線加工と撚り線加工時の断線回数を示す。なお、断線回数の単位［回／１００トン］は、１００トンの鋼線材を湿式伸線加工、撚り線加工した際の断線回数を意味する。 Table 2 shows the production conditions for each high carbon steel wire, the control method (A) to (F) for the amount of non-diffusible hydrogen described above, the cooling rate after hot rolling, the lamellar spacing of the high carbon steel wire, and the pearlite structure. The fraction, the amount of non-diffusible hydrogen, the number of wire breaks during wet wire drawing and stranded wire processing are shown. The unit of the number of times of disconnection [times / 100 tons] means the number of times of disconnection when 100 tons of steel wire material is wet-drawn or stranded.
表２中の試験Ｎｏ.１〜１７が本発明例であり、試験Ｎｏ.１８〜２６が比較例である。 同表に見られるように、本発明例は、何れも高炭素鋼線材のラメラー間隔、パーライト分率、非拡散性水素量が適切に制御されているために、極細鋼線の伸線加工及び撚り線工程での断線回数が低下していることがわかる。 Test Nos. 1 to 17 in Table 2 are examples of the present invention, and Test Nos. 18 to 26 are comparative examples. As can be seen from the table, all examples of the present invention are appropriately controlled for lamellar spacing, pearlite fraction, non-diffusible hydrogen content of high carbon steel wire, It turns out that the frequency | count of disconnection in a strand wire process is falling.
これに対して、比較例であるＮｏ.１８，２６は、線材の化学成分が不適切な例である。すなわち、Ｎｏ.１８は、Ｃ含有量が高すぎるために、熱間圧延時の冷却過程で初析セメンタイトが析出し、断線回数が増加した例である。Ｎｏ.２６は、Ｍｏ含有量が高すぎるために、熱間圧延線材においてベイナイト組織が発生し、パーライト分率が低下し、伸線加工性が低下して、断線回数が増加した例である。 On the other hand, No. 18 and 26 which are comparative examples are examples in which the chemical composition of the wire is inappropriate. That is, No. 18 is an example in which, because the C content is too high, pro-eutectoid cementite was precipitated in the cooling process during hot rolling, and the number of disconnections increased. No. 26 is an example in which, since the Mo content is too high, a bainite structure is generated in the hot-rolled wire, the pearlite fraction is lowered, the wire drawing workability is lowered, and the number of wire breaks is increased.
また、比較例のＮｏ.１９，２０，２４は、熱間圧延後の冷却速度が５℃／ｓよりも遅いか、２５℃／ｓよりも速いものであり、パーライト組織のラメラー間隔、パーライト分率が不適切な例である。Ｎｏ.１９は、ラメラー間隔が粗大化し、Ｎｏ.２０，２４は、ラメラー間隔が細かく、パーライト分率も低く、更にＮｏ.２４は非拡散性水素量も不適切なために、何れも断線回数が改善効果を得られなかった例である。 In Comparative Examples No. 19, 20, and 24, the cooling rate after hot rolling is slower than 5 ° C./s or faster than 25 ° C./s. This is an example of an inappropriate rate. No. 19 has a coarse lamellar spacing, No. 20 and 24 have a narrow lamellar spacing and a low pearlite fraction, and No. 24 has an inappropriate amount of non-diffusible hydrogen. Is an example in which the improvement effect was not obtained.
さらに、比較例のＮｏ.２１，２２，２３，２５は、何れもラメラー間隔、パーライト組織分率は適正であるものの、上述の非拡散性水素量の制御方法のうち、Ｂ又はＤのみを実施したものであり、非拡散性水素量が多いために、断線回数が高かった例である。 Furthermore, although No. 21, 22, 23, and 25 of the comparative examples are all suitable for lamellar spacing and pearlite structure fraction, only B or D is implemented among the above non-diffusible hydrogen amount control methods. This is an example in which the number of disconnections is high due to a large amount of non-diffusible hydrogen.
Claims (4)
Ｃ：０．８０〜１．２０％、
Ｓｉ：０．０１〜１．５０％、
Ｍｎ：０．０５〜１．００％
を含有し、残部がＦｅ及び不可避的不純物からなり、パーライトの面積分率が９５％以上であり、ラメラー間隔が０．０８〜０．３５μｍであり、非拡散性水素量が０．５ｐｐｍ以下であることを特徴とする伸線加工性の優れた高炭素鋼線材。 % By mass
C: 0.80 to 1.20%,
Si: 0.01 to 1.50%,
Mn: 0.05-1.00%
The balance consists of Fe and inevitable impurities, the area fraction of pearlite is 95% or more, the lamellar spacing is 0.08 to 0.35 μm, and the amount of non-diffusible hydrogen is 0.5 ppm or less A high-carbon steel wire rod with excellent wire-drawing workability characterized by being.
Ｃｒ：０．０１〜１．００％、
Ｎｂ：０．００１〜０．２００％、
Ｖ：０．０１〜０．５０％
の少なくとも１種又は２種以上を含有することを特徴とする請求項１に記載の伸線加工性の優れた高炭素鋼線材。 Furthermore, in mass%,
Cr: 0.01 to 1.00%,
Nb: 0.001 to 0.200%,
V: 0.01 to 0.50%
The high carbon steel wire rod excellent in wire drawing workability according to claim 1, comprising at least one kind or two kinds or more.
Ｎｉ：０．０１〜２．００％、
Ｃｏ：０．０１〜１．００％
の一方又は双方を含有することを特徴とする請求項１又は２に記載の伸線加工性の優れた高炭素鋼線材。 Furthermore, in mass%,
Ni: 0.01 to 2.00%,
Co: 0.01-1.00%
One or both of these are contained, The high carbon steel wire wire excellent in the wire drawing workability of Claim 1 or 2 characterized by the above-mentioned.
Ｍｏ：０．０１〜０．５０％、
Ｂ：０．０００１〜０．００７０％
の一方又は双方を含有することを特徴とする請求項１〜３の何れか一項に記載の伸線加工性の優れた高炭素鋼線材。 Furthermore, in mass%,
Mo: 0.01 to 0.50%,
B: 0.0001 to 0.0070%
One or both of these are contained, The high carbon steel wire rod excellent in the wire drawing workability as described in any one of Claims 1-3 characterized by the above-mentioned.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007105731A JP5157230B2 (en) | 2007-04-13 | 2007-04-13 | High carbon steel wire rod with excellent wire drawing workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007105731A JP5157230B2 (en) | 2007-04-13 | 2007-04-13 | High carbon steel wire rod with excellent wire drawing workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2008261028A true JP2008261028A (en) | 2008-10-30 |
| JP5157230B2 JP5157230B2 (en) | 2013-03-06 |
Family
ID=39983723
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2007105731A Active JP5157230B2 (en) | 2007-04-13 | 2007-04-13 | High carbon steel wire rod with excellent wire drawing workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP5157230B2 (en) |
Cited By (21)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2009119359A1 (en) * | 2008-03-25 | 2009-10-01 | 新日本製鐵株式会社 | Wire rod and high-strength steel wire excellent in ductility, and processes for production of both |
| KR101053328B1 (en) * | 2008-12-04 | 2011-08-01 | 주식회사 포스코 | Method for manufacturing cast steel of high carbon steel wire for drawing with excellent internal quality and cast steel manufactured by the method |
| WO2011125447A1 (en) * | 2010-04-01 | 2011-10-13 | 株式会社神戸製鋼所 | High-carbon steel wire with excellent suitability for wiredrawing and fatigue property after wiredrawing |
| JP2012172247A (en) * | 2011-02-24 | 2012-09-10 | Nippon Steel Corp | Steel for high strength spring, excellent in hydrogen embrittlement resistance |
| WO2014157142A1 (en) * | 2013-03-25 | 2014-10-02 | 株式会社神戸製鋼所 | Steel wire rod for high-strength spring having excellent drawability into wire and excellent post-drawing bendability, process for manufacturing same, high-strength spring, and production process therefor |
| KR101461714B1 (en) | 2012-08-21 | 2014-11-14 | 주식회사 포스코 | Steel wire rod and steel wire having excellent drawability and method for manufacturing thereof |
| KR101482358B1 (en) | 2012-12-27 | 2015-01-13 | 주식회사 포스코 | High carbon steel wire rod for high strength and method for manufacturing thereof |
| KR101518584B1 (en) | 2013-09-16 | 2015-05-07 | 주식회사 포스코 | Steel wire rod with superior drawability and metheod for manufacturing thereof |
| JP2015143391A (en) * | 2013-12-27 | 2015-08-06 | 株式会社神戸製鋼所 | Rolled steel material for high-strength spring and wire for high-strength spring using the same |
| WO2016024635A1 (en) * | 2014-08-15 | 2016-02-18 | 新日鐵住金株式会社 | Steel wire for wire drawing |
| JP2016106177A (en) * | 2015-11-27 | 2016-06-16 | 新日鐵住金株式会社 | Hot-dip galvanized steel wire excellent in torsion property |
| JP2017101296A (en) * | 2015-12-02 | 2017-06-08 | 株式会社神戸製鋼所 | Hot rolled wire excellent in hydrogen blistering resistance |
| JP2017106097A (en) * | 2015-12-11 | 2017-06-15 | ポスコＰｏｓｃｏ | High carbon steel wire material excellent in strength and corrosion resistance, high carbon steel wire and manufacturing method therefor |
| JP2017187441A (en) * | 2016-04-08 | 2017-10-12 | Ｊｆｅスチール株式会社 | Method for evaluating delayed fracture of metal material |
| CN108004470A (en) * | 2017-12-08 | 2018-05-08 | 江苏省沙钢钢铁研究院有限公司 | Low-manganese high-carbon steel wire rod for high-strength steel strand and preparation method thereof |
| CN109735773A (en) * | 2018-12-28 | 2019-05-10 | 首钢集团有限公司 | A kind of high-carbon steel pearlite lamella interval controlling method |
| EP3366802A4 (en) * | 2015-10-23 | 2019-05-15 | Nippon Steel & Sumitomo Metal Corporation | Steel wire for wire drawing |
| EP3561100A4 (en) * | 2016-12-20 | 2020-07-29 | Nippon Steel Corporation | Wire rod |
| US20220025691A1 (en) * | 2019-02-26 | 2022-01-27 | Nv Bekaert Sa | Actuator for opening and closing a door or a tailgate of a car |
| WO2022047714A1 (en) * | 2020-09-03 | 2022-03-10 | Nv Bekaert Sa | A steel cord for rubber reinforcement |
| CN114635084A (en) * | 2022-03-04 | 2022-06-17 | 包头钢铁（集团）有限责任公司 | Method for reducing segregation index of high-carbon hard line steel |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06185513A (en) * | 1992-12-21 | 1994-07-05 | Nippon Steel Corp | High strength bolt excellent in delay destruction resistance characteristic and manufacture thereof |
| JPH08337844A (en) * | 1995-06-10 | 1996-12-24 | Sumitomo Electric Ind Ltd | Steel wire rod, steel wire and production thereof |
-
2007
- 2007-04-13 JP JP2007105731A patent/JP5157230B2/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06185513A (en) * | 1992-12-21 | 1994-07-05 | Nippon Steel Corp | High strength bolt excellent in delay destruction resistance characteristic and manufacture thereof |
| JPH08337844A (en) * | 1995-06-10 | 1996-12-24 | Sumitomo Electric Ind Ltd | Steel wire rod, steel wire and production thereof |
Cited By (34)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US9689053B2 (en) | 2008-03-25 | 2017-06-27 | Nippon Steel & Sumitomo Metal Corporation | Steel rod and high strength steel wire having superior ductility and methods of production of same |
| WO2009119359A1 (en) * | 2008-03-25 | 2009-10-01 | 新日本製鐵株式会社 | Wire rod and high-strength steel wire excellent in ductility, and processes for production of both |
| US9212410B2 (en) | 2008-03-25 | 2015-12-15 | Nippon Steel & Sumitomo Metal Corporation | Steel rod and high strength steel wire having superior ductility and methods of production of same |
| KR101053328B1 (en) * | 2008-12-04 | 2011-08-01 | 주식회사 포스코 | Method for manufacturing cast steel of high carbon steel wire for drawing with excellent internal quality and cast steel manufactured by the method |
| US9121080B2 (en) | 2010-04-01 | 2015-09-01 | Kobe Steel, Ltd. | High-carbon steel wire excellent in wire drawability and fatigue property after wiredrawing |
| WO2011125447A1 (en) * | 2010-04-01 | 2011-10-13 | 株式会社神戸製鋼所 | High-carbon steel wire with excellent suitability for wiredrawing and fatigue property after wiredrawing |
| JP2011225990A (en) * | 2010-04-01 | 2011-11-10 | Kobe Steel Ltd | High-carbon steel wire rod with excellent suitability for wiredrawing and fatigue property after wiredrawing |
| RU2507292C1 (en) * | 2010-04-01 | 2014-02-20 | Кабусики Кайся Кобе Сейко Се | Wire from high-carbon steel with excellent properties of ability to drawing and fatigue characteristics after drawing |
| KR101470720B1 (en) * | 2010-04-01 | 2014-12-08 | 가부시키가이샤 고베 세이코쇼 | High-carbon steel wire with excellent suitability for wiredrawing and fatigue property after wiredrawing |
| JP2012172247A (en) * | 2011-02-24 | 2012-09-10 | Nippon Steel Corp | Steel for high strength spring, excellent in hydrogen embrittlement resistance |
| KR101461714B1 (en) | 2012-08-21 | 2014-11-14 | 주식회사 포스코 | Steel wire rod and steel wire having excellent drawability and method for manufacturing thereof |
| KR101482358B1 (en) | 2012-12-27 | 2015-01-13 | 주식회사 포스코 | High carbon steel wire rod for high strength and method for manufacturing thereof |
| JP2014208900A (en) * | 2013-03-25 | 2014-11-06 | 株式会社神戸製鋼所 | Steel wire for high-strength spring which is excellent in wire drawability and bendability after wire drawing, method of producing the wire, high-strength spring, and method producing the spring |
| WO2014157142A1 (en) * | 2013-03-25 | 2014-10-02 | 株式会社神戸製鋼所 | Steel wire rod for high-strength spring having excellent drawability into wire and excellent post-drawing bendability, process for manufacturing same, high-strength spring, and production process therefor |
| KR101518584B1 (en) | 2013-09-16 | 2015-05-07 | 주식회사 포스코 | Steel wire rod with superior drawability and metheod for manufacturing thereof |
| JP2015143391A (en) * | 2013-12-27 | 2015-08-06 | 株式会社神戸製鋼所 | Rolled steel material for high-strength spring and wire for high-strength spring using the same |
| WO2016024635A1 (en) * | 2014-08-15 | 2016-02-18 | 新日鐵住金株式会社 | Steel wire for wire drawing |
| CN106661694A (en) * | 2014-08-15 | 2017-05-10 | 新日铁住金株式会社 | Steel wire for wire drawing |
| US10329646B2 (en) | 2014-08-15 | 2019-06-25 | Nippon Steel & Sumitomo Metal Corporation | Steel wire for drawing |
| JPWO2016024635A1 (en) * | 2014-08-15 | 2017-06-22 | 新日鐵住金株式会社 | Steel wire for wire drawing |
| EP3366802A4 (en) * | 2015-10-23 | 2019-05-15 | Nippon Steel & Sumitomo Metal Corporation | Steel wire for wire drawing |
| US10597748B2 (en) | 2015-10-23 | 2020-03-24 | Nippon Steel Corporation | Steel wire rod for wire drawing |
| JP2016106177A (en) * | 2015-11-27 | 2016-06-16 | 新日鐵住金株式会社 | Hot-dip galvanized steel wire excellent in torsion property |
| JP2017101296A (en) * | 2015-12-02 | 2017-06-08 | 株式会社神戸製鋼所 | Hot rolled wire excellent in hydrogen blistering resistance |
| JP2017106097A (en) * | 2015-12-11 | 2017-06-15 | ポスコＰｏｓｃｏ | High carbon steel wire material excellent in strength and corrosion resistance, high carbon steel wire and manufacturing method therefor |
| JP2017187441A (en) * | 2016-04-08 | 2017-10-12 | Ｊｆｅスチール株式会社 | Method for evaluating delayed fracture of metal material |
| EP3561100A4 (en) * | 2016-12-20 | 2020-07-29 | Nippon Steel Corporation | Wire rod |
| CN108004470A (en) * | 2017-12-08 | 2018-05-08 | 江苏省沙钢钢铁研究院有限公司 | Low-manganese high-carbon steel wire rod for high-strength steel strand and preparation method thereof |
| CN109735773A (en) * | 2018-12-28 | 2019-05-10 | 首钢集团有限公司 | A kind of high-carbon steel pearlite lamella interval controlling method |
| US20220025691A1 (en) * | 2019-02-26 | 2022-01-27 | Nv Bekaert Sa | Actuator for opening and closing a door or a tailgate of a car |
| US12065867B2 (en) * | 2019-02-26 | 2024-08-20 | Nv Bekaert Sa | Actuator for opening and closing a door or a tailgate of a car |
| WO2022047714A1 (en) * | 2020-09-03 | 2022-03-10 | Nv Bekaert Sa | A steel cord for rubber reinforcement |
| WO2022048822A1 (en) * | 2020-09-03 | 2022-03-10 | Nv Bekaert Sa | A steel cord for rubber reinforcement |
| CN114635084A (en) * | 2022-03-04 | 2022-06-17 | 包头钢铁（集团）有限责任公司 | Method for reducing segregation index of high-carbon hard line steel |
Also Published As
| Publication number | Publication date |
|---|---|
| JP5157230B2 (en) | 2013-03-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5157230B2 (en) | High carbon steel wire rod with excellent wire drawing workability | |
| JP5162875B2 (en) | High strength wire rod excellent in wire drawing characteristics and method for producing the same | |
| JP3440937B2 (en) | Method of manufacturing steel wire and steel for steel wire | |
| JP5114684B2 (en) | Wire material excellent in ductility, high-strength steel wire, and production method thereof | |
| JP5233281B2 (en) | High strength steel wire with excellent ductility and method for producing the same | |
| CN108138285B (en) | Steel wire for wire drawing | |
| WO2011055746A1 (en) | High-carbon steel wire material with excellent processability | |
| JP2005206853A (en) | High carbon steel wire rod having excellent wire drawability, and production method therefor | |
| CN107406950B (en) | High-carbon steel wire rod and steel wire having excellent drawability | |
| JP2003082437A (en) | High strength steel wire having excellent strain age embrittlement resistance and longitudinal crack resistance, and production method therefor | |
| WO2016002413A1 (en) | Wire material for steel wire, and steel wire | |
| JP2007131945A (en) | High strength steel wire having excellent ductility and its production method | |
| WO2018117157A1 (en) | Wire rod | |
| JP5503515B2 (en) | High carbon steel wire rod excellent in dry drawing and method for producing the same | |
| JP4980172B2 (en) | Manufacturing method of high-strength ultrafine steel wire with excellent balance of strength and ductility | |
| JP4646850B2 (en) | High carbon steel wire rod with excellent resistance to breakage of copper | |
| JP5945196B2 (en) | High strength steel wire | |
| JP2001181789A (en) | Small-diameter hot rolled high carbon steel wire rod excellent in wire drawability | |
| JPH11269607A (en) | Wire drawing type high strength steel wire rod and its production | |
| JP4555711B2 (en) | High-strength ultrafine steel wire with excellent ductility | |
| JP6922726B2 (en) | Hot rolled wire | |
| JP3267833B2 (en) | High-strength extra-fine steel wire with excellent fatigue properties and method for producing the same | |
| JP2005163082A (en) | High carbon steel wire rod having excellent longitudinal crack resistance | |
| JP3428502B2 (en) | Steel wire, extra fine steel wire and twisted steel wire | |
| JP2002212676A (en) | Steel wire for wire saw and production method therefor |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20090915 |
|
| RD04 | Notification of resignation of power of attorney |
Free format text: JAPANESE INTERMEDIATE CODE: A7424 Effective date: 20110909 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20111026 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20120221 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20120406 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20121113 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20121126 |
|
| R151 | Written notification of patent or utility model registration |
Ref document number: 5157230 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R151 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20151221 Year of fee payment: 3 |
|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |