JP3709600B2 - Carbon steel wire rod with excellent drawability - Google Patents
Carbon steel wire rod with excellent drawability Download PDFInfo
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Description
【０００１】
【発明の属する技術分野】
本発明は高強度，強靭性，高疲労強度を有し、ベルトコード，タイヤコード，ピアノ線，釣り糸，ゴルフシャフト補強用ワイヤ等の極細鋼線に用いられる炭素鋼線材であって、特に伸線性に優れた炭素鋼線材に関するものである。
【０００２】
【従来の技術】
各種製品の補強材として用いられる極細鋼線の製造方法は、所定の成分組成に調整した鋼を線径約４〜５．５ｍｍφに熱間圧延して得られる鋼線材に対して、１次伸線加工，パテンティング処理，２次伸線加工を行い、必要に応じて再度パテンティング処理およびブラスメッキ処理を行い、最後に、湿式伸線加工を施して極細鋼線とする方法が一般的に採用されている。例えばタイヤコードは上記極細鋼線を撚り合わせて製造されるが、伸線および撚線工程時において断線が発生するという問題があった。素材として極細鋼線に起因する断線原因の一つに、線材中に存在する非延性介在物が挙げられる。しかも、この非延性介在物が存在するとダイス寿命の低下を招いたり、タイヤコードの疲労破断の原因ともなることが指摘されている。
【０００３】
従来はこの問題を解決するために、延性を有する介在物となる様に組成を調整することを目的として、介在物の組成とその組合わせを規定した炭素鋼線材（例えば特開昭６２−１３０２５８号等）が提案されている。
【０００４】
しかしながら、これまでに提案されている技術によれば、例えば１トン当りの炭素鋼を用いて極細線材に伸線すると、どうしても断線が発生することが指摘されており、必ずしも断線を防止できる技術は開示されていなかった。
【０００５】
【発明が解決しようとする課題】
本発明は上記の事情に着目してなされたものであって、伸線性に優れ、断線の発生に対する信頼性の高い炭素鋼線材の提供を目的とするものである。
【０００６】
【課題を解決するための手段】
上記課題を解決した本発明の炭素鋼線材とは、Ｃ ：０．３〜１．０％、Ｓｉ：０．１〜０．５％、Ｍｎ：０．１〜０．７％、残部Ｆｅおよび不可避的不純物からなる炭素鋼線材であって、Ａｌ，Ｃａ，Ｍｇ，Ｔｉ，Ｚｒの鋼中固溶量が、Ａｌ：０．１ppm 以上３．０ppm 未満、Ｃａ：０．０１ppm 以上０．５ppm 以下、Ｍｇ：０．１５ppm 以上３．０ppm 未満、Ｔｉ：５．０ppm 未満（０ppm を含む）、Ｚｒ：０．５ppm 未満（０ppm を含む）であることを要旨とするものであり、さらにＣｒ：０．１〜０．６％を含有させれば、強度向上に有効であり、またＣｕ：０．１〜１．０％を含有させれば、スケール剥離性を向上させることができる。
尚、前記鋼中固溶量は、２次イオン質量分析装置（以下、ＳＩＭＳという）を用いることにより精度良く分析することが可能である。
【０００７】
【発明の実施の形態】
本発明者らは、鋼中における微量元素の固溶量と断線指数には、非常に高い相関があることを突き止めた。これまでは、介在物組成に範囲を設けることにより高い延性を有する介在物となる様に配慮されていたが、どうしても結晶質な介在物を有することから、伸線時の断線を防止できなかった。本発明によれば、鋼中固溶量を制御することによって、伸線および撚線時の断線を大幅に改善することが可能である。
【０００８】
また従来の技術における微量元素の定量分析は、供試材を酸により溶解して、例えばＩＣＰ発光分光分析により測定されることが一般的であり、上記微量成分の含有量は、介在物の構成成分と鋼中の固溶成分との合計値であった。図１は、従来の一般的な分析方法である酸溶解とＩＣＰ発光分光分析の組み合わせによるＡｌ含有量の分析値と、ＳＩＭＳにより分析した鋼中Ａｌ固溶量の値を比較して示すグラフである。両分析値の差は、介在物の成分量に相当する。
【０００９】
本発明者らは鋭意研究を重ねた結果、従来の方法で分析された成分値では、確実な断線の制御は困難であり、Ａｌ，Ｃａ，Ｍｇ，Ｔｉ，Ｚｒという微量元素の鋼中固溶量を制御してはじめて確実な断線防止が可能となることを見出し、本発明に想到したものである。従って本発明では、各微量元素の鋼中固溶量を以下の様に限定することが重要である。尚、図２〜図６における鋼中のＡｌ，Ｃａ，Ｍｇ，Ｔｉ，Ｚｒの固溶量と、図７，８におけるＣｒ，Ｃｕの含有量は、後述する実施例で測定した分析値を断線指数との関係で整理したグラフである。
【００１０】
Ａｌ：０．１ ppm 以上３．０ ppm 未満
鋼中に固溶するＡｌ量と断線指数との関係を示す図２の結果から明らかな様に、鋼中のＡｌ固溶量が０．１ppm 未満または３．０ppm 以上の場合には断線指数が高くなった。Ａｌ固溶量が０．１ppm 未満の場合には介在物としてＣａＯ−ＳｉＯ2 およびＭｎＯ−ＳｉＯ2 系の結晶が存在し、また３．０ppm 以上の場合にはＡｌ2 Ｏ3 含有量が４０％以上の非延性な介在物が存在しており、これらの非延性介在物により断線指数が高くなったものと考えられる。
従って、鋼中のＡｌ固溶量は、０．１ppm 以上３．０ppm 未満に規定した。
【００１１】
Ｃａ：０．０１ ppm 以上０．５ ppm 以下
図３より明らかな様に、鋼中のＣａ固溶量が０．０１ppm 未満であるか、或いは０．５ppm を超える場合には断線指数が高くなった。鋼中Ｃａ固溶量が０．０１ppm 未満の場合には、ＭｎＯ−ＳｉＯ2 −Ａｌ2 Ｏ3 系介在物を主体として、介在物組成がばらついており、非延性介在物が多く発生していた。鋼中Ｃａ固溶量が０．５ppm を超える場合には２ＣａＯ・ＳｉＯ2 や２ＣａＯ・ＳｉＯ2 ・Ａｌ2 Ｏ3 等の結晶質な介在物が存在していた。これらの非延性介在物の存在により断線指数が高くなったものと考えられる。Ｃａ固溶量が０．０１〜０．５ppm の範囲内では結晶質な介在物は見られなかった。
【００１２】
Ｍｇ：０．１５ ppm 以上３ ppm 未満
図４に示されている通り、鋼中のＭｇ固溶量が０．１５ppm 未満３ppm 以上の場合には断線指数が高くなった。Ｍｇ固溶量が０．１５ppm 未満の場合には鋼中のＭｎＯ−ＳｉＯ2 −Ａｌ2 Ｏ3 系介在物を主体として介在物組成がばらついており、非延性介在物が多く発生していた。またＭｇ固溶量が３ppm 以上の場合には、Ａｌが２．５ppm 未満であるとＭｇＯ・ＳｉＯ2 結晶が生成しており、Ａｌが２．５ppm 以上の場合にはＭｇＯ・Ａｌ2 Ｏ3 結晶が観察された。従って鋼中のＭｇ固溶量を０．１５ppm 以上３ppm 未満とすることが必要である。
【００１３】
Ｔｉ：５ ppm 未満（０ ppm を含む）
図５から明らかな様に、鋼中のＴｉ固溶量が５ppm 以上の場合には断線指数が高くなった。鋼中Ｔｉ固溶量が５ppm 以上ではＴｉ系の結晶質な非金属介在物が多く存在したことから、鋼中Ｔｉ固溶量は５ppm 未満とすることが必要である。
【００１４】
Ｚｒ：０．５ ppm 未満（０ ppm を含む）
図６に示されている通り、鋼中のＺｒ固溶量が０．５ppm 以上の場合には断線指数が高くなった。鋼中のＺｒ固溶量が０．５ppm 以上ではＺｒＯ2 ・ＳｉＯ2 やＣａＯ−ＳｉＯ2 −ＺｒＯ2 系介在物が多く存在しており、この様な非延性な結晶系介在物の存在により断線回数が高くなったと考えられる。
尚、本発明では必要に応じて、炭素鋼線材にＣｒ及び／又はＣｕを含有させても良い。
【００１５】
Ｃｒ：０．１〜０．６％
図７に示すように、Ｃｒ含有量が０．１％から０．６％までは、含有量が増えるに従い、引張強さが増加する。但し、０．６％を超えると硬度が高くなり過ぎ、断線が発生し易くなるので０．６％を上限とした。また０．１％未満では十分な強度上昇効果が得られない。従って、Ｃｒ含有量は０．１〜０．６％とすることが望ましい。
【００１６】
Ｃｕ：０．１〜１．０％
Ｃｕを添加すれば、炭素鋼の耐食性向上に有効であるが、図８から明らかな様に、Ｃｕ含有量を０．１％以上にすると耐食性が良くなるばかりでなく、スケールの剥離性も向上する。但し、Ｃｕ含有量が１．０％を超えると割れが発生し易くなるので、Ｃｕ含有量は０．１〜１．０％とすることが望ましい。
【００１７】
ところで本発明は、Ａｌ，Ｃａ，Ｍｇ，Ｔｉ，Ｚｒの各元素の鋼中固溶量を制御する方法により限定されるものではなく、例えば鋼中固溶量が多過ぎる元素は、溶銑処理時にスラグ中に捕捉し、一方少な過ぎる場合には添加して補充すればよい。
【００１８】
尚、本発明が対象とする炭素鋼は、強度及び靭性の点からＣを０．３〜１．０％、Ｓｉを０．１〜０．５％、Ｍｎを０．１〜０．７％含有し、残部鉄および不可避的不純物からなる炭素鋼であり、夫々の成分限定理由は以下の通りである。
【００１９】
Ｃは、鋼線に十分な強度を与えるのに不可欠な元素であり、少なくとも０．３％以上含有していることが必要である。Ｃ含有量を多くするほど線材の強度は向上するが、多過ぎると初析セメンタイトが析出し、伸線加工時やより線加工時に断線を引き起こす。従って、Ｃ量の上限は１．０％とした。
【００２０】
Ｓｉは、フェライトを固溶強化して引張強さを高めると共に、脱酸に有効な元素であるので０．１％以上含有させるが、多過ぎるとフェライトの靭性及び延性が低下し、極細鋼線としての強度特性を満足できなくなるので、０．５％を上限とした。
【００２１】
Ｍｎは、加工硬化率を高めて引張強さを高めるのに有効な元素であるので０．１％以上含有させるが、多過ぎると偏析が大きくなり、それを起点とするマイクロクラックが発生して断線の原因となるので、０．７％を上限とした。
【００２２】
以下、本発明を実施例によって更に詳細に説明するが、下記実施例は本発明を限定する性質のものではなく、前・後記の趣旨に徴して設計変更することはいずれも本発明の技術的範囲に含まれるものである。
【００２３】
【実施例】
実施例１
２４０トンの溶鋼を取鍋で、表１に示す所定の成分に調整し、ブルーム連鋳機で鋳片として線材にし、その後０．２３０ｍｍまで伸線したときの極細鋼線の断線指数（１トン当りの断線回数）を調べた。
【００２４】
上記ＳＩＭＳとしてはＣＡＭＥＣＡ製のｉｍｓ５ｆを用い、分析条件は以下の通りである。
［分析条件］
１次イオン条件： Ｏ2 −８ｋｅＶ−０．１μＡ
照射および分析領域：８０×８０μｍ−φ１４μｍ
試料室真空度： ６×１０-10 Ｔｏｒｒ
結果は、表１に示す。
【００２５】
【表１】
Ｎｏ．１〜６は本発明例であり、鋼中固溶量が本発明範囲を満足しているので、トン当りの断線回数が平均で０〜０．２であり、非常に優れた伸線性を示した。
一方Ｎｏ．７〜２５は、Ａｌ，Ｃａ，Ｍｇ，Ｔｉ，Ｚｒの１種以上の鋼中固溶量が本発明範囲を満足しない比較例であり、断線指数が高いことが分かる。
【００３１】
【００３４】
【発明の効果】
本発明は以上の様に構成されているので、結晶質で非延性な介在物の量を著しく低減でき、冷間加工時の断線の発生を非常に少なくすることが可能となり、伸線性に優れ、断線の発生することのない信頼性の高い炭素鋼線材が提供できることとなった。
【図面の簡単な説明】
【図１】Ａｌ含有量に関して、酸溶解−ＩＣＰ法による分析値とＳＩＭＳ法による鋼中固溶量の分析値を対比するグラフである。
【図２】断線指数と鋼中Ａｌ固溶量の関係を示すグラフである。
【図３】断線指数と鋼中Ｃａ固溶量の関係を示すグラフである。
【図４】断線指数と鋼中Ｍｇ固溶量の関係を示すグラフである。
【図５】断線指数と鋼中Ｔｉ固溶量の関係を示すグラフである。
【図６】断線指数と鋼中Ｚｒ固溶量の関係を示すグラフである。
【図７】引張強さとＣｒ含有量の関係を示すグラフである。
【図８】スケール剥離率とＣｕ含有量の関係を示すグラフである。[0001]
BACKGROUND OF THE INVENTION
The present invention is a carbon steel wire having high strength, toughness, and high fatigue strength, and used for ultra fine steel wires such as belt cords, tire cords, piano wires, fishing lines, golf shaft reinforcing wires, etc. It is related with the carbon steel wire excellent in.
[0002]
[Prior art]
The production method of ultra fine steel wire used as a reinforcing material for various products is based on the first elongation for steel wire obtained by hot rolling steel adjusted to a predetermined composition to a wire diameter of about 4 to 5.5 mmφ. Wire drawing, patenting and secondary wire drawing are performed, and patenting and brass plating are performed again if necessary. Finally, wet wire drawing is used to make ultra-fine steel wire. It has been adopted. For example, tire cords are manufactured by twisting the above-mentioned ultrafine steel wires, but there is a problem that disconnection occurs during the wire drawing and twisting steps. One of the causes of disconnection resulting from the ultrafine steel wire as a material is non-ductile inclusions present in the wire. Moreover, it has been pointed out that the presence of this non-ductile inclusion may cause a reduction in the die life and cause fatigue fracture of the tire cord.
[0003]
Conventionally, in order to solve this problem, for the purpose of adjusting the composition so as to become a ductile inclusion, a carbon steel wire rod (for example, Japanese Patent Laid-open No. Sho 62-130258) in which the composition of the inclusion and the combination thereof are defined. Etc.) have been proposed.
[0004]
However, according to the techniques proposed so far, it has been pointed out that, for example, if wire is drawn to an ultrafine wire using carbon steel per ton, disconnection is inevitably generated. It was not disclosed.
[0005]
[Problems to be solved by the invention]
The present invention has been made by paying attention to the above circumstances, and an object of the present invention is to provide a carbon steel wire that is excellent in wire drawability and highly reliable against occurrence of wire breakage.
[0006]
[Means for Solving the Problems]
The carbon steel wire of the present invention that has solved the above problems is C: 0.3-1.0%, Si: 0.1-0.5%, Mn: 0.1-0.7%, the balance Fe and A carbon steel wire made of inevitable impurities, and the solid solution amount of Al, Ca, Mg, Ti, and Zr in the steel is Al: 0.1 ppm or more and less than 3.0 ppm, Ca: 0.01 ppm or more and 0.5 ppm or less Mg: 0.15 ppm or more and less than 3.0 ppm, Ti: less than 5.0 ppm (including 0 ppm), Zr: less than 0.5 ppm (including 0 ppm), and Cr: 0 0.1 to 0.6% is effective for improving the strength, and Cu: 0.1 to 1.0% can improve the scale peelability.
The amount of solid solution in the steel can be analyzed with high accuracy by using a secondary ion mass spectrometer (hereinafter referred to as SIMS).
[0007]
DETAILED DESCRIPTION OF THE INVENTION
The present inventors have found that there is a very high correlation between the amount of trace elements dissolved in steel and the disconnection index. Previously, consideration was given to providing inclusions with high ductility by providing a range in the inclusion composition, but because of the inclusion of crystalline inclusions, disconnection during wire drawing could not be prevented. . According to the present invention, by controlling the amount of solid solution in steel, it is possible to greatly improve the disconnection at the time of wire drawing and twisting.
[0008]
In addition, the quantitative analysis of trace elements in the prior art is generally measured by dissolving a test material with an acid and, for example, by ICP emission spectroscopic analysis, and the content of the trace component is the composition of inclusions. It was the total value of the component and the solid solution component in steel. FIG. 1 is a graph showing a comparison between an analytical value of Al content by a combination of acid dissolution and ICP emission spectroscopic analysis, which is a conventional general analysis method, and a value of Al solid solution in steel analyzed by SIMS. is there. The difference between the two analysis values corresponds to the amount of inclusions.
[0009]
As a result of intensive studies, the present inventors have found that it is difficult to reliably control disconnection with the component values analyzed by the conventional method, and the solid elements of trace elements such as Al, Ca, Mg, Ti, and Zr are dissolved in steel. The inventors have found that it is possible to surely prevent disconnection only after controlling the amount, and have arrived at the present invention. Therefore, in the present invention, it is important to limit the solid solution amount of each trace element in the steel as follows. The solid solution amounts of Al, Ca, Mg, Ti, and Zr in the steels in FIGS. 2 to 6 and the Cr and Cu contents in FIGS. 7 and 8 are disconnected from the analytical values measured in Examples described later. It is a graph arranged in relation to the index.
[0010]
Al: 0.1 ppm or more and less than 3.0 ppm As is apparent from the results of Fig. 2 showing the relationship between the amount of Al dissolved in steel and the disconnection index, the amount of Al solid solution in steel is When it was less than 0.1 ppm or more than 3.0 ppm, the disconnection index increased. When the Al solid solution amount is less than 0.1 ppm, CaO—SiO 2 and MnO—SiO 2 based crystals exist as inclusions. When the Al solution amount is 3.0 ppm or more, the Al 2 O 3 content is 40%. The above non-ductile inclusions are present, and it is considered that these non-ductile inclusions increased the disconnection index.
Therefore, the amount of Al solid solution in the steel is specified to be not less than 0.1 ppm and less than 3.0 ppm.
[0011]
Ca: 0.01 ppm or more and 0.5 ppm or less As is apparent from FIG. 3, disconnection occurs when the amount of Ca solid solution in the steel is less than 0.01 ppm or more than 0.5 ppm . The index has increased. When the amount of Ca solid solution in the steel is less than 0.01 ppm, the inclusion composition varies mainly from MnO—SiO 2 —Al 2 O 3 inclusions, and many non-ductile inclusions are generated. . When the Ca dissolved amount in the steel exceeds 0.5ppm is crystalline inclusions such as 2CaO · SiO 2 and 2CaO · SiO 2 · Al 2 O 3 was present. It is considered that the disconnection index was increased due to the presence of these non-ductile inclusions. Crystalline inclusions were not observed when the Ca solid solution amount was in the range of 0.01 to 0.5 ppm.
[0012]
Mg: 0.15 ppm or more and less than 3 ppm As shown in FIG. 4, the disconnection index increased when the Mg solid solution amount in the steel was less than 0.15 ppm and 3 ppm or more . When the Mg solid solution amount is less than 0.15 ppm, the inclusion composition varies mainly from MnO—SiO 2 —Al 2 O 3 inclusions in the steel, and many non-ductile inclusions are generated. Further, when the Mg solid solution amount is 3 ppm or more, MgO · SiO 2 crystals are formed when Al is less than 2.5 ppm, and when Al is 2.5 ppm or more, MgO · Al 2 O 3 crystals are formed. Was observed. Therefore, it is necessary that the Mg solid solution amount in the steel is 0.15 ppm or more and less than 3 ppm.
[0013]
Ti: Less than 5 ppm ( including 0 ppm )
As is apparent from FIG. 5, the disconnection index increased when the Ti solid solution amount in the steel was 5 ppm or more. When the Ti solid solution amount in steel is 5 ppm or more, there are many Ti-based crystalline non-metallic inclusions, so the Ti solid solution amount in steel must be less than 5 ppm.
[0014]
Zr: less than 0.5 ppm ( including 0 ppm )
As shown in FIG. 6, the disconnection index increased when the Zr solid solution amount in the steel was 0.5 ppm or more. When the Zr solid solution amount in steel is 0.5 ppm or more, there are many ZrO 2 · SiO 2 and CaO-SiO 2 -ZrO 2 type inclusions, and disconnection is caused by the presence of such non-ductile crystalline inclusions. It is thought that the number of times has increased.
In the present invention, if necessary, the carbon steel wire may contain Cr and / or Cu.
[0015]
Cr: 0.1 to 0.6%
As shown in FIG. 7, when the Cr content is from 0.1% to 0.6%, the tensile strength increases as the content increases. However, if it exceeds 0.6%, the hardness becomes too high and disconnection tends to occur, so 0.6% was made the upper limit. If it is less than 0.1%, a sufficient strength increasing effect cannot be obtained. Therefore, the Cr content is desirably 0.1 to 0.6%.
[0016]
Cu: 0.1 to 1.0%
Addition of Cu is effective for improving the corrosion resistance of carbon steel, but as is clear from FIG. 8, when the Cu content is 0.1% or more, not only the corrosion resistance is improved, but also the peelability of the scale is improved. To do. However, if the Cu content exceeds 1.0%, cracks are likely to occur, so the Cu content is preferably 0.1 to 1.0%.
[0017]
By the way, this invention is not limited by the method of controlling the solid solution amount of each element of Al, Ca, Mg, Ti, and Zr, for example, an element with too much solid solution amount in steel is used at the time of hot metal processing. If it is trapped in the slag, but too little, it may be added and replenished.
[0018]
In addition, the carbon steel which this invention makes object is 0.3 to 1.0% of C, 0.1 to 0.5% of Si, and 0.1 to 0.7% of Mn from the point of intensity | strength and toughness. It is a carbon steel containing the balance iron and unavoidable impurities, and the reasons for limiting the respective components are as follows.
[0019]
C is an element indispensable for giving sufficient strength to the steel wire, and it is necessary to contain at least 0.3% or more. As the C content is increased, the strength of the wire is improved. However, if it is too much, pro-eutectoid cementite is precipitated, causing breakage during wire drawing or wire drawing. Therefore, the upper limit of the C amount is set to 1.0%.
[0020]
Si enhances the tensile strength by solid solution strengthening of ferrite and is contained in an amount of 0.1% or more because it is an element effective for deoxidation, but if it is too much, the toughness and ductility of ferrite will decrease, and the ultrafine steel wire Therefore, the upper limit is set to 0.5%.
[0021]
Mn is an element effective for increasing the work hardening rate and increasing the tensile strength, so it is contained in an amount of 0.1% or more. However, if it is too much, segregation increases and microcracks originating from it occur. Since it causes disconnection, the upper limit is set to 0.7%.
[0022]
Hereinafter, the present invention will be described in more detail by way of examples. However, the following examples are not intended to limit the present invention, and any design changes in accordance with the gist of the preceding and following descriptions are technical aspects of the present invention. It is included in the range.
[0023]
【Example】
Example 1
240 tons of molten steel is adjusted to the prescribed components shown in Table 1 with a ladle, and is made into a wire rod as a slab with a bloom continuous caster and then drawn to 0.230 mm (1 ton). The number of hits per break) was investigated.
[0024]
As SIMS, ims5f manufactured by CAMECA is used, and the analysis conditions are as follows.
[Analysis conditions]
Primary ion condition: O 2 -8 keV-0.1 μA
Irradiation and analysis area: 80 × 80 μm-φ14 μm
Sample chamber vacuum: 6 × 10 −10 Torr
The results are shown in Table 1.
[0025]
[Table 1]
No. 1 to 6 are examples of the present invention, and the amount of solid solution in the steel satisfies the scope of the present invention. Therefore, the average number of disconnections per ton is 0 to 0.2, indicating excellent wire drawing. It was.
On the other hand, no. 7 to 25 are comparative examples in which the amount of solid solution in one or more of Al, Ca, Mg, Ti, and Zr does not satisfy the scope of the present invention, and it can be seen that the disconnection index is high.
[0031]
[0034]
【The invention's effect】
Since the present invention is configured as described above, it is possible to remarkably reduce the amount of crystalline and non-ductile inclusions, it is possible to greatly reduce the occurrence of disconnection during cold working, and excellent wire drawability. Thus, it is possible to provide a highly reliable carbon steel wire without wire breakage.
[Brief description of the drawings]
FIG. 1 is a graph comparing the analysis value of acid dissolution-ICP method and the analysis value of solid solution amount in steel by SIMS method for Al content.
FIG. 2 is a graph showing the relationship between the disconnection index and the amount of Al solid solution in steel.
FIG. 3 is a graph showing the relationship between the disconnection index and the amount of Ca solid solution in steel.
FIG. 4 is a graph showing the relationship between the disconnection index and the amount of Mg solid solution in steel.
FIG. 5 is a graph showing the relationship between the disconnection index and the amount of Ti solid solution in steel.
FIG. 6 is a graph showing the relationship between the disconnection index and the Zr solid solution amount in steel.
FIG. 7 is a graph showing the relationship between tensile strength and Cr content.
FIG. 8 is a graph showing the relationship between the scale peeling rate and the Cu content.
Claims (2)
Ｓｉ：０．１〜０．５％
Ｍｎ：０．１〜０．７％
であると共に、Ａｌ，Ｃａ，Ｍｇについては鋼中の固溶量が以下の通りであり、
Ａｌ：０．１ ppm （質量 ppm 、以下同じ）以上３．０ ppm 未満
Ｃａ：０．０１ ppm 以上０．５ ppm 以下
Ｍｇ：０．１５ ppm 以上３．０ ppm 未満
且つ、鋼中にはＴｉとＺｒの固溶量が夫々
Ｔｉ：５．０ ppm 未満（０ ppm を含む）
Ｚｒ：０．５ ppm 未満（０ ppm を含む）
に抑制され、
残部Ｆｅおよび不可避的不純物からなることを特徴とする伸線性に優れた炭素鋼線材。C: 0.3 to 1.0% (mass%, the same applies hereinafter)
Si: 0.1 to 0.5%
Mn: 0.1 to 0.7%
In addition, for Al, Ca, Mg, the amount of solid solution in the steel is as follows,
Al: 0.1 ppm (mass ppm , the same applies hereinafter) or more and less than 3.0 ppm
Ca: 0.01 ppm or 0.5 ppm or less
Mg: 0.15 ppm or more and less than 3.0 ppm
And the amount of solid solution of Ti and Zr in steel is
Ti: less than 5.0 ppm ( including 0 ppm )
Zr: less than 0.5 ppm ( including 0 ppm )
Restrained by
Excellent carbon steel wire rod drawability characterized by the Turkey a balance of Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03833396A JP3709600B2 (en) | 1996-02-26 | 1996-02-26 | Carbon steel wire rod with excellent drawability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03833396A JP3709600B2 (en) | 1996-02-26 | 1996-02-26 | Carbon steel wire rod with excellent drawability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH09227994A JPH09227994A (en) | 1997-09-02 |
| JP3709600B2 true JP3709600B2 (en) | 2005-10-26 |
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ID=12522364
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03833396A Expired - Lifetime JP3709600B2 (en) | 1996-02-26 | 1996-02-26 | Carbon steel wire rod with excellent drawability |
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| Country | Link |
|---|---|
| JP (1) | JP3709600B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100384629B1 (en) * | 1998-10-16 | 2003-08-19 | 주식회사 포스코 | A high strength wire-rod having superior wire drawability and a method therefor |
-
1996
- 1996-02-26 JP JP03833396A patent/JP3709600B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH09227994A (en) | 1997-09-02 |
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