JPH04272134A - Production of high strength bead wire - Google Patents
Production of high strength bead wireInfo
- Publication number
- JPH04272134A JPH04272134A JP5019391A JP5019391A JPH04272134A JP H04272134 A JPH04272134 A JP H04272134A JP 5019391 A JP5019391 A JP 5019391A JP 5019391 A JP5019391 A JP 5019391A JP H04272134 A JPH04272134 A JP H04272134A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- steel
- strength
- pro
- content
- 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
- 239000011324 bead Substances 0.000 title claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 37
- 239000010959 steel Substances 0.000 claims abstract description 37
- 238000001816 cooling Methods 0.000 claims abstract description 26
- 229910001567 cementite Inorganic materials 0.000 claims description 32
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 32
- 238000000034 method Methods 0.000 claims description 29
- 229910001562 pearlite Inorganic materials 0.000 claims description 10
- 238000010438 heat treatment Methods 0.000 claims description 8
- 239000003507 refrigerant Substances 0.000 claims description 8
- 230000009466 transformation Effects 0.000 claims description 7
- 229910001566 austenite Inorganic materials 0.000 claims description 4
- 238000010791 quenching Methods 0.000 claims description 3
- 230000000171 quenching effect Effects 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 239000002826 coolant Substances 0.000 abstract 1
- 238000005491 wire drawing Methods 0.000 description 23
- 230000015572 biosynthetic process Effects 0.000 description 11
- 230000000694 effects Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 6
- 230000009467 reduction Effects 0.000 description 5
- 238000007796 conventional method Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000007792 addition Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 150000003568 thioethers Chemical class 0.000 description 3
- 238000013459 approach Methods 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000007747 plating Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000906 Bronze Inorganic materials 0.000 description 1
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 239000010974 bronze Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 230000029052 metamorphosis Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- OXNIZHLAWKMVMX-UHFFFAOYSA-N picric acid Chemical compound OC1=C([N+]([O-])=O)C=C([N+]([O-])=O)C=C1[N+]([O-])=O OXNIZHLAWKMVMX-UHFFFAOYSA-N 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、タイヤ用高強度ビード
ワイヤ、さらに詳しくは、引張強さ２５０ｋｇｆ／ｍｍ
２ 以上の高強度ビードワイヤの製造方法に関する。[Industrial Application Field] The present invention relates to a high-strength bead wire for tires, more specifically, a tensile strength of 250 kgf/mm.
2. The present invention relates to a method for manufacturing a high-strength bead wire.
【０００２】0002
【従来の技術】ビードワイヤ等の高炭素鋼線の強度を上
げる方策として、Ｃ含有率を上げることは、安価で高い
効果が得られるため工業的には最も望ましい方法である
。しかし、過共析領域、すなわち、通常Ｃが０．９％を
超える領域では、パテンティング時に旧オーステナイト
粒界に沿って脆い初析セメンタイトがネットワーク状に
生成する。このため、伸線加工時、初析セメンタイトに
沿った粒界われが発生しやすくなり、高減面率の伸線加
工は不可能となる。BACKGROUND OF THE INVENTION As a measure to increase the strength of high carbon steel wires such as bead wires, increasing the C content is the most desirable method from an industrial perspective because it is inexpensive and highly effective. However, in a hypereutectoid region, that is, a region where C usually exceeds 0.9%, brittle proeutectoid cementite is formed in a network along prior austenite grain boundaries during patenting. Therefore, during wire drawing, grain boundary cracking along the pro-eutectoid cementite tends to occur, making wire drawing with a high area reduction ratio impossible.
【０００３】従来、過共析鋼の伸線加工性を向上させる
方法として、熱処理ないしは合金元素の添加により初析
セメンタイトの生成を抑制する方法、あるいは伸線方法
を工夫することにより初析セメンタイト起因の延性劣化
を防止する方法が開発されている。Conventionally, methods for improving the wire drawability of hypereutectoid steel include suppressing the formation of pro-eutectoid cementite by heat treatment or adding alloying elements, or devising the wire drawing method to suppress the formation of pro-eutectoid cementite. A method to prevent ductility deterioration has been developed.
【０００４】たとえば、特公昭５６−８８９３号公報に
は、熱処理により組織を粒状セメンタイトが分散したパ
ーライト組織に変える方法が開示されている。これは、
過共析鋼線をオーステナイト化し、油焼き入れ処理して
マルテンサイト組織とした後、７７０〜９３０℃の温度
域に急速加熱して粒状セメンタイトを析出させ、目標加
熱温度に到達後直ちに５３５〜６６０℃の温度でパテン
ティング処理する方法である。この方法は、伸線加工限
界を高める方法としてはすぐれているが、粒状化したセ
メンタイトは層状に発達したセメンタイトと異なり、強
化への寄与が小さい（パテンティング後の強度が低く、
伸線時の加工硬化も小さい）ため、Ｃ含有率を高めた効
果を生かすことができない。For example, Japanese Patent Publication No. 56-8893 discloses a method of changing the structure into a pearlite structure in which granular cementite is dispersed by heat treatment. this is,
After austenitizing the hypereutectoid steel wire and making it into a martensitic structure through oil quenching treatment, it is rapidly heated to a temperature range of 770 to 930 °C to precipitate granular cementite, and immediately after reaching the target heating temperature, it is heated to a temperature of 535 to 660 °C. This is a method of patenting at a temperature of °C. Although this method is excellent as a method for increasing the wire drawing processing limit, granular cementite, unlike cementite developed in layers, has a small contribution to strengthening (strength after patenting is low,
The work hardening during wire drawing is also small), so the effect of increasing the C content cannot be utilized.
【０００５】本発明者らは、これまでに、合金元素の添
加効果を利用して初析セメンタイトの発生を抑制する方
法を研究し、特開平２−２６３９５１号公報および特開
平２−２５８９５３号公報に開示している。これらはい
ずれも０．１〜０．３％のＣｒを添加することを特徴と
しているが、これらによっても小量の初析セメンタイト
の生成は防止できない。The present inventors have so far researched a method of suppressing the generation of pro-eutectoid cementite by utilizing the effect of adding alloying elements, and have published Japanese Patent Application Laid-Open Nos. 2-263951 and 2-258953. has been disclosed. All of these are characterized by the addition of 0.1 to 0.3% Cr, but even these cannot prevent the formation of a small amount of pro-eutectoid cementite.
【０００６】また、特開昭６３−１８６８５２号公報に
は、５〜５０ｐｐｍのＲＥＭおよびＣａ、Ｍｇ、Ｂａ、
Ｓｒのうちの１種類以上を合計で５〜５０ｐｐｍ添加す
る方法が開示されている。これらの元素はいずれも硫化
物と酸化物を同時に生成させる元素である。これらの添
加により生成したＲＥＭ、Ｃａ、Ｍｇ、Ｂａ、Ｓｒを含
む微細な硫化物、酸化物を核としてパーライト変態を促
進させ、マルテンサイトや初析セメンタイトの生成を抑
制しようとする方法である。しかし、この方法はこれら
微量元素の添加のみならず、微細な硫化物、酸化物を出
現させるためにＳ、Ｏ、Ａｌの含有率も抑制しなければ
ならず、製造管理はきわめて複雑なものとなる。[0006] Furthermore, in Japanese Patent Application Laid-open No. 186852/1986, 5 to 50 ppm of REM and Ca, Mg, Ba,
A method is disclosed in which one or more types of Sr are added in a total amount of 5 to 50 ppm. All of these elements are elements that simultaneously generate sulfides and oxides. This is a method in which pearlite transformation is promoted using fine sulfides and oxides containing REM, Ca, Mg, Ba, and Sr generated by these additions as nuclei, and the formation of martensite and pro-eutectoid cementite is suppressed. However, this method requires not only the addition of these trace elements, but also the content of S, O, and Al in order to produce fine sulfides and oxides, making manufacturing control extremely complicated. Become.
【０００７】一方、初析セメンタイトが存在しても伸線
加工性が低下しないように塑性加工面からの改善を行っ
た例としては、伸線前にローラーダイス加工ないしは冷
間圧延を行う方法が特開昭６３−４０１６号公報に、ま
た、ダイスのアプローチ角を１０度前後に下げて伸線す
る方法が、前記特開平２−２６３９５１号公報に記載さ
れている。これらは、いずれも伸線加工時に鋼線中心部
にかかる引張り応力を軽減させることにより初析セメン
タイト起因の内部クラックの発生を抑制しようとしたも
のである。しかし、この方法が効果を有するのは、生成
した初析セメンタイトの量が少なくかつ粒界に薄く存在
している場合、すなわちＣが１％以下の場合や、小量の
Ｃｒ添加により初析セメンタイトの生成が抑制されてい
る場合に限られる。一方、これらの方法は伸線機とは別
に新たにローラーダイスや圧延機を装備しなければなら
ないこと、また、ダイスの管理を厳しくしなければなら
ないことなど製造上の問題も少なくない。[0007] On the other hand, as an example of an improvement from the perspective of plastic working so that wire drawability does not deteriorate even in the presence of pro-eutectoid cementite, there is a method of performing roller die processing or cold rolling before wire drawing. Japanese Unexamined Patent Publication No. 63-4016 discloses a method of drawing wire by lowering the approach angle of the die to around 10 degrees, and the aforementioned Japanese Unexamined Patent Publication No. 2-263951 discloses a method of drawing wire by lowering the approach angle of the die to around 10 degrees. These methods all attempt to suppress the occurrence of internal cracks caused by pro-eutectoid cementite by reducing the tensile stress applied to the center of the steel wire during wire drawing. However, this method is effective when the amount of pro-eutectoid cementite produced is small and exists thinly at grain boundaries, that is, when C is less than 1%, or when a small amount of Cr is added, pro-eutectoid cementite limited to cases where the production of is suppressed. On the other hand, these methods have many manufacturing problems, such as the need to newly equip a roller die or rolling mill in addition to the wire drawing machine, and the need to strictly manage the dies.
【０００８】[0008]
【発明が解決しようとする課題】以上述べたように、従
来技術では過共析鋼における粒界初析セメンタイトの発
生を完全に阻止することはできない。本発明の目的は、
過共析鋼における粒界初析セメンタイトの生成を完全に
阻止することにより高減面率の伸線加工を可能とし、Ｃ
含有率を高めた効果を十分生かした高強度ビードワイヤ
の製造方法を提供することにある。As described above, the conventional techniques cannot completely prevent the generation of grain boundary pro-eutectoid cementite in hypereutectoid steel. The purpose of the present invention is to
By completely preventing the formation of grain boundary pro-eutectoid cementite in hypereutectoid steel, wire drawing with a high area reduction ratio is possible, and C
It is an object of the present invention to provide a method for manufacturing a high-strength bead wire that fully takes advantage of the effect of increasing the content.
【０００９】[0009]
【課題を解決するための手段】すなわち、本発明は、Ｃ
：０．９０〜１．２５％、Ｓｉ：０．１５〜１．５％、
Ｍｎ：０．３〜１．０％、Ｃｒ：０．１〜１．０％を含
有し、残余がＦｅおよび不可避的不純物からなる鋼線を
加熱してオーステナイト化したのち、（１）式数２
で規定される範囲の冷却速度で４００〜６５０℃に保持
された冷媒中に焼き入れ、引き続き該冷媒中で恒温変態
を完了させることにより初析セメンタイトを含まない微
細パーライト組織としたのち、加工度８６．０〜９４．
０％で伸線加工を施し、さらに伸線加工後の鋼線を３５
０〜４５０℃でブルーイングすることを特徴とする高強
度ビードワイヤの製造方法である。[Means for Solving the Problems] That is, the present invention provides C
:0.90~1.25%, Si:0.15~1.5%,
After heating and austenitizing a steel wire containing Mn: 0.3 to 1.0%, Cr: 0.1 to 1.0%, and the remainder consisting of Fe and inevitable impurities, the formula (1) 2
After quenching in a refrigerant maintained at 400 to 650°C at a cooling rate within the range specified by , and then completing isothermal transformation in the refrigerant to create a fine pearlite structure that does not contain pro-eutectoid cementite, 86.0-94.
The wire is drawn at 0%, and the steel wire after wiredrawing is further reduced to 35%.
This is a method for manufacturing a high-strength bead wire, which is characterized by blueing at 0 to 450°C.
【００１０】0010
【数２】
Ｙ≦０．１６ｌｏｇＸ＋０．８２
（１）
ただし、Ｙは鋼のＣ含有率（％）、Ｘは冷却速度（℃／
ｓｅｃ）を示す。[Math. 2] Y≦0.16logX+0.82
(1)
However, Y is the C content (%) of the steel, and X is the cooling rate (°C/
sec).
【００１１】[0011]
【作用】以下に、本発明を詳細に説明する。[Operation] The present invention will be explained in detail below.
【００１２】本発明者らは、過共析鋼の伸線加工性を改
善すべく多くの実験を行い、以下に示すように、オース
テナイト化温度からの冷却条件を選ぶことにより、初析
セメンタイトの生成を阻止できるという新たな知見を得
た。The present inventors have conducted many experiments to improve the wire drawability of hypereutectoid steel, and as shown below, by selecting cooling conditions from the austenitizing temperature, pro-eutectoid cementite can be improved. We have obtained new knowledge that it is possible to prevent the formation.
【００１３】すなわち、本発明者らは、表１に示す組成
の真空溶解鋼を熱間圧延した線材より直径３ｍｍ、高さ
１０ｍｍの円柱状試料を製作し、これをＡｒガス中で９
５０〜１０００℃に誘導加熱してオーステナイト化した
のち、種々の冷却速度で連続冷却した。冷却後の試料を
研磨し、ＪＩＳＧ０５５１に規定された方法でエッチン
グしたのち光学顕微鏡により初析セメンタイトの生成状
況を調べた。また、粒界の薄いフィルム状セメンタイト
の生成状況は、研磨後の試料をピクラールでエッチング
したのち走査型電子顕微鏡を用いて観察した。図１に、
初析セメンタイトの発生限界とＣ含有率ならびに冷却速
度の関係を示す。このように、初析セメンタイトの生成
はＣ含有率以外に冷却速度にも依存し、同一Ｃ含有率で
も冷却速度を上げることによりその生成を防ぐことがで
きる。図１より、初析セメンタイトの発生しない条件を
鋼のＣ含有率とオーステナイト域からの冷却速度で表す
と、式（１） 数３ のようになる。That is, the present inventors fabricated a cylindrical sample with a diameter of 3 mm and a height of 10 mm from a wire rod obtained by hot rolling vacuum melted steel having the composition shown in Table 1, and heated it in Ar gas for 90 minutes.
After induction heating to 50 to 1000°C to austenite, continuous cooling was performed at various cooling rates. After cooling, the sample was polished and etched according to the method specified in JIS G0551, and then the formation of pro-eutectoid cementite was examined using an optical microscope. Furthermore, the formation of film-like cementite with thin grain boundaries was observed using a scanning electron microscope after etching the polished sample with Picral. In Figure 1,
The relationship between the generation limit of pro-eutectoid cementite, C content, and cooling rate is shown. In this way, the formation of pro-eutectoid cementite depends not only on the C content but also on the cooling rate, and even with the same C content, its formation can be prevented by increasing the cooling rate. From FIG. 1, the conditions under which pro-eutectoid cementite does not occur are expressed by the C content of the steel and the cooling rate from the austenite region as shown in Equation (1).
【００１４】[0014]
【数３】
Ｙ≦０．１６ｌｏｇＸ＋０．８２
（１）
ただし、Ｙは鋼のＣ含有率（％）、Ｘ は冷却速度（
℃／ｓｅｃ）を示す。[Math 3] Y≦0.16logX+0.82
(1)
However, Y is the C content (%) of the steel, and X is the cooling rate (
°C/sec).
【００１５】[0015]
【表１】試料の化学成分 （％）[Table 1] Chemical composition of sample (%)
【００１６】高強度鋼線の実際のパテンティングにおい
ては、連続冷却ではパーライト変態時間が不足するため
、鉛パテンティングないしは流動層パテンティング処理
を行い、微細パーライトに恒温変態させる必要がある。
その際、冷媒である溶融鉛や流動層の温度を制御して鋼
線の冷却速度を（１）式を満足する範囲に選択すれば、
初析セメンタイトの発生を完全に防止することが可能で
ある。しかし、冷媒温度が４００℃未満では鋼線表層に
ベイナイトが生成し、伸線可能限界が低下する。また、
６５０℃を超えるとパーライトの層状構造が崩れ、この
ため強度、伸線加工限界ともに低下する。したがって、
冷媒温度は４００〜６５０℃とする。なお、冷却槽内の
温度は均一である必要はない。すなわち、（１）式の冷
却速度を得るために、赤熱した鋼線が侵入する側の冷媒
温度は低く設定し、その他の部分の温度は、鋼組成に応
じて微細な層状パーライトが得られる温度に保持すべき
である。このような目的のためには、冷却槽は傾斜加熱
できるような構造が望ましく、さらには、複数の冷却帯
に分割された冷却槽を採用すればなお良い。In actual patenting of high-strength steel wires, continuous cooling does not provide enough time for pearlite transformation, so it is necessary to perform isothermal transformation into fine pearlite by performing lead patenting or fluidized bed patenting treatment. At that time, if the temperature of the molten lead refrigerant and the fluidized bed are controlled and the cooling rate of the steel wire is selected within a range that satisfies equation (1),
It is possible to completely prevent the generation of pro-eutectoid cementite. However, if the refrigerant temperature is less than 400° C., bainite is generated on the surface layer of the steel wire, lowering the wire drawability limit. Also,
When the temperature exceeds 650°C, the layered structure of pearlite collapses, resulting in a decrease in both strength and wire drawing processing limit. therefore,
The refrigerant temperature is 400 to 650°C. Note that the temperature within the cooling tank does not need to be uniform. In other words, in order to obtain the cooling rate of equation (1), the temperature of the refrigerant on the side where the red-hot steel wire enters is set low, and the temperature of the other parts is set at a temperature that allows fine layered pearlite to be obtained depending on the steel composition. should be kept at For this purpose, it is desirable that the cooling tank has a structure that allows gradient heating, and it is even better to adopt a cooling tank that is divided into a plurality of cooling zones.
【００１７】次に、本発明の成分限定理由について説明
する。Next, the reason for limiting the components of the present invention will be explained.
【００１８】Ｃは強度を上げるための有効かつ経済的な
元素であり、本発明の最も重要な元素の一つである。Ｃ
含有率を上げるに伴い、パテンティング後の強度ならび
に伸線時の加工硬化量が増大する。したがって，伸線加
工により高強度鋼線を得るためにはＣ含有量は高い方が
有利であり、本発明では０．９０％以上とする。一方、
Ｃ含有率が１．２５％を超した場合、（１）式が示すよ
うに、初析セメンタイトの発生を防止するために必要な
冷却速度は４８０℃／ｓｅｃを超えるため、工業的に実
現が困難となる。したがって、Ｃ含有率の上限は１．２
５％とする。C is an effective and economical element for increasing strength, and is one of the most important elements in the present invention. C
As the content increases, the strength after patenting and the amount of work hardening during wire drawing increase. Therefore, in order to obtain a high-strength steel wire by wire drawing, it is advantageous to have a high C content, and in the present invention, it is set to 0.90% or more. on the other hand,
When the C content exceeds 1.25%, as shown in equation (1), the cooling rate required to prevent the formation of pro-eutectoid cementite exceeds 480°C/sec, which is not industrially possible. It becomes difficult. Therefore, the upper limit of C content is 1.2
5%.
【００１９】Ｓｉは脱酸剤として０．１５％以上添加す
る。一方、Ｓｉは合金元素としてフェライトに固溶して
顕著な固溶強化作用を示す。また、フェライト中のＳｉ
は伸線後の溶融亜鉛めっきやブルーイング時の強度低下
を低減させる効果を有するため、高強度鋼線の製造には
不可欠な元素である。しかし、１．５％を越えると伸線
後の鋼線の延性が低下するため、１．５％を上限とする
。Si is added as a deoxidizing agent in an amount of 0.15% or more. On the other hand, Si is dissolved in ferrite as an alloying element and exhibits a remarkable solid solution strengthening effect. In addition, Si in ferrite
Since it has the effect of reducing strength loss during hot-dip galvanizing and bluing after wire drawing, it is an essential element in the production of high-strength steel wire. However, if it exceeds 1.5%, the ductility of the steel wire after drawing will decrease, so the upper limit is set at 1.5%.
【００２０】Ｍｎも脱酸剤として０．３％以上添加する
。また、Ｍｎは焼入れ性向上効果が大きいため、線径が
大きい場合には、Ｍｎ含有率を上げることにより断面内
の均一性を高めることが可能であり、伸線後の鋼線の延
性向上に有効である。しかし、１．０％を超えると中心
偏析部にマルテンサイトが生成して伸線加工性が劣化す
るため、１．０％を上限とする。Mn is also added as a deoxidizing agent in an amount of 0.3% or more. In addition, since Mn has a large effect on improving hardenability, when the wire diameter is large, it is possible to increase the uniformity in the cross section by increasing the Mn content, which can improve the ductility of the steel wire after wire drawing. It is valid. However, if it exceeds 1.0%, martensite will be generated in the central segregation part and wire drawability will deteriorate, so 1.0% is the upper limit.
【００２１】Ｃｒはパーライトのラメラー間隔を低減し
、鋼線の強度と伸線加工性を向上させるため、０．１％
以上添加する。０．１％未満ではその効果が十分でなく
、一方、１．０％を超えると変態に要する時間が長くな
り、生産性が著しく低下するため、１．０％を上限とす
る。[0021] Cr is added at 0.1% in order to reduce the lamellar spacing of pearlite and improve the strength and wire drawability of the steel wire.
Add more. If it is less than 0.1%, the effect will not be sufficient, while if it exceeds 1.0%, the time required for transformation will become longer and productivity will drop significantly, so 1.0% is set as the upper limit.
【００２２】次に、本発明における熱処理後の加工条件
について説明する。Next, processing conditions after heat treatment in the present invention will be explained.
【００２３】恒温変態により微細なパーライトとした鋼
線に、断面減少率８６．０〜９４．０％の伸線加工を施
す。８６．０％未満では加工硬化量が不足し、目標とす
る強度が得られないため、８６．０％を下限とする。一
方、９４．０％を超えると延性が低下し、ブルーイング
後の鋼線（ビードワイヤ）の伸びが不足するため、９４
．０％を上限とする。[0023] A steel wire made into fine pearlite by isothermal transformation is subjected to a wire drawing process with a cross-section reduction rate of 86.0 to 94.0%. If it is less than 86.0%, the amount of work hardening is insufficient and the target strength cannot be obtained, so 86.0% is set as the lower limit. On the other hand, if it exceeds 94.0%, the ductility will decrease and the elongation of the steel wire (bead wire) after bluing will be insufficient.
．． The upper limit is 0%.
【００２４】伸線後の鋼線にはブルーイングを行う。ブ
ルーイングの目的は、鋼線に必要な伸びを付与すること
であり、通常、鋼線を溶融鉛ないしは流動層中を連続的
に通過させる方法で行われる。ブルーイング温度は、３
５０℃未満では必要な伸びが得られず、一方、４５０℃
を超えると強度が低下するのみならず、捻回値も低下す
る。このため、ブルーイング温度の下限および上限は、
それぞれ３５０℃および４５０℃とする。[0024] The steel wire after wire drawing is subjected to bluing. The purpose of bluing is to impart the necessary elongation to the steel wire, and is usually carried out by passing the steel wire continuously through molten lead or a fluidized bed. The bluing temperature is 3
Below 50°C, the necessary elongation cannot be obtained;
If it exceeds, not only the strength decreases, but also the torsion value decreases. Therefore, the lower and upper limits of bluing temperature are
The temperatures are 350°C and 450°C, respectively.
【００２５】[0025]
【実施例】以下、２５０ｋｇｆ／ｍｍ２ 以上の引張強
さを有する高強度ビードワイヤの製造結果について説明
する。なお、ビードワイヤの目標とする延性は、伸びが
５％以上、捻回値が３０回以上である。EXAMPLES The results of manufacturing a high-strength bead wire having a tensile strength of 250 kgf/mm2 or more will be described below. Note that the target ductility of the bead wire is an elongation of 5% or more and a twist value of 30 turns or more.
【００２６】表２に示す化学成分の直径２．６０〜４．
２０ｍｍの鋼線を鉛パテンティング後、伸線加工して直
径１．００ｍｍの細線を製造した。次に、これらを３４
０〜４６０℃に保持した鉛浴中で１５ｓブルーイングし
、その後、置換めっき法によりブロンズめっきを行って
高強度ビードワイヤを製造した。The chemical components shown in Table 2 have a diameter of 2.60 to 4.
A 20 mm steel wire was subjected to lead patenting and then wire drawn to produce a thin wire with a diameter of 1.00 mm. Next, add these to 34
Blueing was performed for 15 seconds in a lead bath maintained at 0 to 460°C, and then bronze plating was performed using a displacement plating method to produce a high-strength bead wire.
【００２７】表２〜５には、鋼の化学成分、パテンティ
ング条件、パテンティング後の組織、伸線加工度、ブル
ーイング温度、およびビードワイヤの機械的性質を示す
。Tables 2 to 5 show the chemical composition of the steel, the patenting conditions, the structure after patenting, the degree of wire drawing, the bluing temperature, and the mechanical properties of the bead wire.
【００２８】Ａ、Ｂ、Ｃ、Ｄの各群は、主として、それ
ぞれＣ、Ｓｉ、Ｍｎ、Ｃｒ含有率の影響を示したもので
ある。Groups A, B, C, and D mainly show the influence of C, Si, Mn, and Cr contents, respectively.
【００２９】Ｃ含有率が０．８６％（Ａ−１）では目標
強度が得られず、一方、１．３５％（Ａ−７）では冷却
速度不足のため初析セメンタイトが生成し、伸線できな
かった。同様に、Ｃ含有率が１．２０％（Ａ−５）でも
、冷却速度が２０℃／ｓｅｃと（１）式を満足しない場
合は初析セメンタイトが生成し、製品の伸びおよび捻回
値が低下したため、目標とするビードワイヤの製造はで
きなかった。[0029] When the C content is 0.86% (A-1), the target strength cannot be obtained, while when the C content is 1.35% (A-7), pro-eutectoid cementite is formed due to insufficient cooling rate, resulting in wire drawing. could not. Similarly, even if the C content is 1.20% (A-5), if the cooling rate is 20°C/sec and does not satisfy equation (1), pro-eutectoid cementite will be formed and the elongation and torsion values of the product will be reduced. Because of this, the target bead wire could not be manufactured.
【００３０】Ｓｉ含有率の増加により強度は増大するが
、１．６３％（Ｂ−４）では延性不足となり、めっき鋼
線の伸びおよび捻回値が低下した。[0030] As the Si content increases, the strength increases, but at 1.63% (B-4), the ductility becomes insufficient, and the elongation and twist value of the plated steel wire decrease.
【００３１】Ｍｎが１．０６％（Ｃ−３）の場合は、中
心偏析部に生成したマルテンサイトによりめっき鋼線の
伸びおよび捻回値が著しく低下した。When Mn was 1.06% (C-3), the elongation and torsion value of the plated steel wire were significantly reduced due to martensite generated in the center segregation area.
【００３２】Ｃｒ含有率は０．０５％（Ｄ−１）ではそ
の効果が小さく、目標強度が得られない。一方、１．２
０％（Ｄ−７）では、変態時間不足のためパテンティン
グ組織にマルテンサイトが発生したため断線が頻発し、
伸び、捻回値も著しく劣化した。[0032] When the Cr content is 0.05% (D-1), the effect is small and the target strength cannot be obtained. On the other hand, 1.2
At 0% (D-7), martensite was generated in the patenting structure due to insufficient metamorphosis time, resulting in frequent disconnections.
The elongation and torsion values also deteriorated significantly.
【００３３】従来法１（Ｅ−１）は特開昭６３−４０１
６号公報に開示された方法であり、ローラーダイス伸線
後、通常の伸線を行ったものである。また、従来法２（
Ｆ−１）は特開昭６３−１８６８５２号公報に開示され
た方法で、表２の化学成分以外にＲＥＭを０．００１２
％、Ｃａを０．０００８％含有する。いずれも目標強度
に到達しないのみならず、初析セメンタイトを内蔵して
いるため伸び、絞り値もともに低い。Conventional method 1 (E-1) is disclosed in Japanese Patent Application Laid-Open No. 63-401.
This is a method disclosed in Japanese Patent No. 6, in which normal wire drawing is performed after roller die wire drawing. In addition, conventional method 2 (
F-1) is a method disclosed in JP-A-63-186852, in which 0.0012% of REM is added in addition to the chemical components shown in Table 2.
%, and contains 0.0008% of Ca. Not only do none of them reach the target strength, but both elongation and aperture value are low because they contain pro-eutectoid cementite.
【００３４】Ｂ−２は鉛浴温度が４００℃未満の場合、
またＤ−３は鉛浴温度が６５０℃を超える場合であり、
それぞれマルテンサイトおよび初析セメンタイトが発生
したためビードワイヤの延性が低下した。B-2: When the lead bath temperature is less than 400°C,
D-3 is a case where the lead bath temperature exceeds 650°C,
The ductility of the bead wire decreased due to the generation of martensite and pro-eutectoid cementite, respectively.
【００３５】Ａ−３は伸線加工度が８６．０％未満の場
合、またＤ−４は伸線加工度が９４．０％を超える場合
であり、前者は強度、後者は伸びおよび絞り値が目標値
を下まわった。A-3 is the case where the degree of wire drawing is less than 86.0%, and D-4 is the case where the degree of wire drawing is more than 94.0%, the former is the strength, and the latter is the elongation and reduction of area was below the target value.
【００３６】Ａ−６はブルーイング温度が３５０℃未満
の場合、またＤ−６はブルーイング温度が４５０℃を超
える場合であり、前者は伸びが不足し、一方、後者は捻
回値が目標値を下まわった。[0036] A-6 is when the bluing temperature is less than 350°C, and D-6 is when the bluing temperature is over 450°C. It fell below the value.
【００３７】本発明法で製造されたビードワイヤはいず
れも２５０ｋｇｆ／ｍｍ２ 以上の強度を有し、従来法
で製造されたものに比べて強度が高く、延性（伸び、絞
り値）に優れている。All of the bead wires manufactured by the method of the present invention have a strength of 250 kgf/mm 2 or more, which is higher than those manufactured by the conventional method, and are excellent in ductility (elongation, reduction of area).
【００３８】[0038]
【表２】[Table 2]
【００３９】[0039]
【表３】[Table 3]
【００４０】[0040]
【表４】[Table 4]
【００４１】[0041]
【表５】[Table 5]
【００４２】[0042]
【発明の効果】以上説明したように、本発明法によれば
、従来より強度が高くかつ伸びおよび捻回特性に優れた
ビードワイヤを製造することが可能である。As explained above, according to the method of the present invention, it is possible to produce a bead wire that has higher strength than conventional wires and has excellent elongation and twisting properties.
【図１】初析セメンタイトの発生限界とＣ含有率ならび
に冷却速度の関係を示す図である。FIG. 1 is a diagram showing the relationship between the generation limit of pro-eutectoid cementite, C content, and cooling rate.
Claims (1)
線を加熱してオーステナイト化したのち、（１）式
数１ で規定される範囲の冷却速度で４００〜６５０
℃に保持された冷媒中に焼き入れ、引き続き該冷媒中で
恒温変態を完了させることにより初析セメンタイトを含
まない微細パーライト組織としたのち、加工度８６．０
〜９４．０％で伸線加工を施し、さらに伸線加工後の鋼
線を３５０〜４５０℃でブルーイングすることを特徴と
する高強度ビードワイヤの製造方法。 【数１】 Ｙ≦０．１６ｌｏｇＸ＋０．８２
（
１）ただし、Ｙは鋼のＣ含有率（％）、Ｘは冷却速度（
℃／ｓｅｃ）を示す。Claim 1: In weight ratio, C: 0.90-1.25%, Si: 0.15-1.5%, Mn: 0.3-1.0%, Cr: 0.1-1. After heating a steel wire containing 0% and the remainder consisting of Fe and unavoidable impurities to austenite, the formula (1) is obtained.
400 to 650 at a cooling rate within the range specified by Equation 1.
After quenching in a refrigerant kept at ℃ and then completing isothermal transformation in the refrigerant to create a fine pearlite structure that does not contain pro-eutectoid cementite, the workability is 86.0.
A method for manufacturing a high-strength bead wire, which comprises drawing the steel wire at a temperature of 94.0% to 94.0%, and then blueing the drawn steel wire at 350 to 450°C. [Math. 1] Y≦0.16logX+0.82
(
1) However, Y is the C content (%) of the steel, and X is the cooling rate (
°C/sec).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5019391A JP2939770B2 (en) | 1991-02-25 | 1991-02-25 | Method of manufacturing high strength bead wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5019391A JP2939770B2 (en) | 1991-02-25 | 1991-02-25 | Method of manufacturing high strength bead wire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04272134A true JPH04272134A (en) | 1992-09-28 |
| JP2939770B2 JP2939770B2 (en) | 1999-08-25 |
Family
ID=12852321
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5019391A Expired - Fee Related JP2939770B2 (en) | 1991-02-25 | 1991-02-25 | Method of manufacturing high strength bead wire |
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| Country | Link |
|---|---|
| JP (1) | JP2939770B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2011089782A1 (en) * | 2010-01-25 | 2011-07-28 | 新日本製鐵株式会社 | Wire material, steel wire, and process for production of wire material |
| CN102301024A (en) * | 2010-02-01 | 2011-12-28 | 新日本制铁株式会社 | Wire material, steel wire, and processes for production of those products |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4970562B2 (en) * | 2009-04-21 | 2012-07-11 | 新日本製鐵株式会社 | High strength steel wire rod excellent in ductility and method for manufacturing steel wire |
| US8470099B2 (en) | 2009-04-21 | 2013-06-25 | Nippon Steel & Sumitomo Metal Corporation | Wire rod, steel wire, and manufacturing method thereof |
| KR101767763B1 (en) * | 2015-12-22 | 2017-08-14 | 주식회사 포스코 | Pearlite steel material having excellent ductility and impact toughness, and method for manufacturing the same |
-
1991
- 1991-02-25 JP JP5019391A patent/JP2939770B2/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2011089782A1 (en) * | 2010-01-25 | 2011-07-28 | 新日本製鐵株式会社 | Wire material, steel wire, and process for production of wire material |
| JP4842408B2 (en) * | 2010-01-25 | 2011-12-21 | 新日本製鐵株式会社 | Wire, steel wire, and method for manufacturing wire |
| CN102301024A (en) * | 2010-02-01 | 2011-12-28 | 新日本制铁株式会社 | Wire material, steel wire, and processes for production of those products |
| KR101318009B1 (en) * | 2010-02-01 | 2013-10-14 | 신닛테츠스미킨 카부시키카이샤 | Wire rod, steel wire, and manufacturing method thereof |
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| Publication number | Publication date |
|---|---|
| JP2939770B2 (en) | 1999-08-25 |
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