JP3267833B2 - High-strength extra-fine steel wire with excellent fatigue properties and method for producing the same - Google Patents
High-strength extra-fine steel wire with excellent fatigue properties and method for producing the sameInfo
- Publication number
- JP3267833B2 JP3267833B2 JP09386495A JP9386495A JP3267833B2 JP 3267833 B2 JP3267833 B2 JP 3267833B2 JP 09386495 A JP09386495 A JP 09386495A JP 9386495 A JP9386495 A JP 9386495A JP 3267833 B2 JP3267833 B2 JP 3267833B2
- Authority
- JP
- Japan
- Prior art keywords
- steel wire
- wire
- strength
- die
- less
- 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.)
- Expired - Fee Related
Links
Classifications
-
- D—TEXTILES; PAPER
- D07—ROPES; CABLES OTHER THAN ELECTRIC
- D07B—ROPES OR CABLES IN GENERAL
- D07B1/00—Constructional features of ropes or cables
- D07B1/06—Ropes or cables built-up from metal wires, e.g. of section wires around a hemp core
- D07B1/0606—Reinforcing cords for rubber or plastic articles
- D07B1/066—Reinforcing cords for rubber or plastic articles the wires being made from special alloy or special steel composition
Description
【０００１】[0001]
【産業上の利用分野】本発明は、スチールタイヤコー
ド、スチールベルトコード等の素線として使用され、線
径が０．０５〜０．４mmである疲労特性の優れた高強度
極細鋼線およびその製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength ultrafine steel wire which is used as a strand of steel tire cords, steel belt cords and the like, has a wire diameter of 0.05 to 0.4 mm, and has excellent fatigue properties. It relates to a manufacturing method.
【０００２】[0002]
【従来の技術】軽量化などのために極細鋼線に対する高
強度化の要求は一段と高まっている。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
る極細鋼線は、高炭素鋼の熱間圧延線材から中間伸線、
パテンティング処理を繰り返し所定の線径にした後、最
終パテンティング処理を行い、伸線加工性およびゴムと
の接着性を向上させるめっき処理を施し所定の線径まで
湿式伸線加工することにより製造される。例えばスチー
ルタイヤコードは、上記のように製造される素線を最終
的にダブルツイスタなどの撚り線機を用いて撚り線加工
することによって製造される。2. Description of the Related Art The demand for higher strength of ultrafine steel wires for weight reduction and the like is increasing more and more. Conventionally, ultra-fine steel wires used for reinforcement of automobile tires, industrial belts, etc. are made from hot-rolled high-carbon steel wire,
After the patenting process is repeatedly performed to a predetermined wire diameter, a final patenting process is performed, a plating process is performed to improve the wire drawing processability and the adhesion to rubber, and wet drawing is performed to a predetermined wire diameter. Is done. For example, a steel tire cord is manufactured by finally twisting a strand manufactured as described above using a twisting machine such as a double twister.
【０００３】上記のような製造工程において、極細鋼線
の高強度化を図るためには、最終パテンティング処理後
の素線強度を上げるか、最終の伸線加工歪を増加させる
必要がある。ところが、最終パテンティング処理後の素
線強度ないしは伸線加工歪を増加させて極細鋼線の高強
度化を図っても、極細鋼線の疲労特性は向上せず、むし
ろ劣化するという問題点があり、極細鋼線の高強度化を
阻害する要因の一つであった。In the above-described manufacturing process, in order to increase the strength of the ultrafine steel wire, it is necessary to increase the wire strength after the final patenting process or to increase the final drawing strain. However, even if the strength of the ultrafine steel wire is increased by increasing the wire strength or drawing strain after the final patenting process, the fatigue characteristics of the ultrafine steel wire do not improve, but rather deteriorate. This was one of the factors that hindered the strengthening of ultrafine steel wires.
【０００４】これに対して極細鋼線の疲労特性を向上さ
せる手段として、例えば特開平２−１７９３３３号公報
には極細鋼線にショットピーニング処理を適用する技術
が開示されており、極細線表面層の引張残留応力を圧縮
残留応力に改善して耐疲労性の高い極細鋼線を製造する
方法が提案されている。本発明者らの詳細な試験によれ
ば、ショットピーニング処理によって極細鋼線表面の引
張残留応力を圧縮残留応力に改善することは可能である
が、圧縮残留応力に変えるためには非常に強いショット
ピーニング処理が必要である。このようなショットピー
ニング処理を行うと、伸線加工によって非常に薄くなっ
た極細鋼線表層のブラスめっき層が剥離してしまい、ゴ
ムとの密着性が劣化するという問題点が生じ、極細鋼線
の疲労特性を改善するためには限界があった。また、特
開平５−１９５４５７号公報には極細線中の微細不均一
歪の分布を制御することにより、特開平６−１８４９６
２号公報には極細鋼線の表層と内部の強度差を制御する
ことにより、極細鋼線の疲労特性を向上させる技術が開
示されているが、本発明者らの詳細な研究によれば、こ
のような技術を適用しても極細鋼線の高疲労強化には限
界があった。On the other hand, as a means for improving the fatigue characteristics of an ultrafine steel wire, for example, Japanese Patent Application Laid-Open No. 2-179333 discloses a technique in which shot peening is applied to an ultrafine steel wire. There has been proposed a method for improving the tensile residual stress of steel to a compressive residual stress to produce an ultrafine steel wire having high fatigue resistance. According to the present inventors' detailed tests, it is possible to improve the tensile residual stress on the surface of ultrafine steel wire to compressive residual stress by shot peening, but to convert it to compressive residual stress, a very strong shot Peening is required. When such a shot peening treatment is performed, the brass plating layer on the surface layer of the ultrafine steel wire, which has become extremely thin due to the wire drawing, is peeled off, resulting in a problem that the adhesion to rubber is deteriorated. There are limits to improving the fatigue properties of steel. Further, Japanese Patent Application Laid-Open No. Hei 5-195457 discloses a method of controlling the distribution of minute non-uniform strain in a very fine line, which is disclosed in Japanese Patent Application Laid-Open No. Hei 6-18496.
No. 2 discloses a technique for improving the fatigue properties of the ultrafine steel wire by controlling the difference in strength between the surface layer and the inside of the ultrafine steel wire, but according to the detailed research of the present inventors, Even if such a technique is applied, there is a limit to the high fatigue strengthening of ultrafine steel wires.
【０００５】[0005]
【発明が解決しようとする課題】本発明は上記の如き実
状に鑑みなされたものであって、伸線加工によって線径
０．０５〜０．４mmである極細鋼線を製造する際に生じ
る疲労特性の劣化を防止し、疲労特性の優れた高強度極
細鋼線を実現するとともにその製造方法を提供すること
を目的とするものである。SUMMARY OF THE INVENTION The present invention has been made in view of the above-mentioned situation, and has been developed in view of the fatigue generated when producing an ultrafine steel wire having a wire diameter of 0.05 to 0.4 mm by wire drawing. It is an object of the present invention to prevent the deterioration of the properties, to realize a high-strength ultrafine steel wire having excellent fatigue properties, and to provide a manufacturing method thereof.
【０００６】[0006]
【課題を解決するための手段】本発明者らはまず、鋼
線材の化学成分、パテンティング熱処理条件、伸線
加工に用いるダイス形状、伸線加工歪、伸線加工後
の曲げ加工、等を変化させることにより極細鋼線の引張
強さおよび降伏比を変化させた種々の試料を用いて疲労
特性の支配要因を詳細に解析した。この結果、極細鋼線
の表層の残留応力以外に、鋼線の降伏比が高強度極細鋼
線の疲労に対して顕著な影響を及ぼすことを見出した。
そこで、高強度極細鋼線の疲労強度を向上するための降
伏比と残留応力の影響について定量的な検討を重ねた。
更に、降伏比および残留応力を制御する手段として、伸
線加工時に用いるダイス形状、および伸線加工後の曲げ
加工が極めて有効であること明らかにした。Means for Solving the Problems First, the present inventors first examined the chemical composition of a steel wire, the conditions of heat treatment for patenting, the shape of a die used for wire drawing, the strain of wire drawing, the bending after wire drawing, and the like. The dominant factors of the fatigue properties were analyzed in detail using various samples in which the tensile strength and the yield ratio of the ultrafine steel wire were changed by changing. As a result, it was found that, besides the residual stress on the surface layer of the ultrafine steel wire, the yield ratio of the steel wire significantly affects the fatigue of the high-strength ultrafine steel wire.
Therefore, the effects of yield ratio and residual stress for improving the fatigue strength of high-strength ultrafine steel wire were quantitatively studied.
Furthermore, as a means for controlling the yield ratio and the residual stress, it was clarified that a die shape used in wire drawing and bending after wire drawing were extremely effective.
【０００７】以上の検討結果に基づき、伸線加工に用い
るダイス形状、および伸線加工後の曲げ加工条件を限定
することにより、極細鋼線の降伏比と表層の残留応力を
最適に制御することが可能となり、疲労特性の優れた高
強度極細鋼線を製造できるとの結論に達し、本発明をな
したものである。本発明は以上の知見に基づいてなされ
たものであって、その要旨とするところは、重量％で、 Ｃ：０．８〜１．１％、 Ｓｉ：０．１〜０．５
％、 Ｍｎ：０．２〜０．７％、 Ａｌ：０．００５％以
下、 を含有するか、あるいは更に Ｃｒ：０．０５〜０．５％、 Ｎｉ：０．１〜１．０
％、 Ｖ：０．０５〜０．３％ の１種または２種以上を含み、残部はＦｅおよび不可避
的不純物からなる熱間圧延線材から中間伸線、パテンテ
ィング処理を繰り返し所定の線径にした後、最終パテン
ティング処理を行い、めっき処理を施し、０．０５〜
０．４mmの線径まで湿式伸線加工された鋼線において、
鋼線材を前記最終パテンティング処理後、 ダイスのアプローチ角度：８〜１２° ダイスのベアリング長さ：０．２〜０．５Ｄ（Ｄ：ダイ
ス径） の条件を満たすダイスを用いて伸線加工を行い、引き続
き鋼線の引張破断荷重の１０％以上の張力を鋼線に付与
しつつ複数個のロール間を曲げ角度１５〜３０°で通過
させることにより製造された、 引張強さが３７０２MPa
以上で、降伏比が０．９３以上、表層の残留応力が＋２
００MPa以下であることを特徴とする疲労特性の優れた
高強度極細鋼線、およびその製造方法にある。[0007] Based on the above study results, used for wire drawing
Die shape and bending conditions after wire drawing are limited
By doing so, the yield ratio of ultrafine steel wire and residual stress on the surface layer
Optimum control is possible, and high fatigue characteristics
We concluded that we could manufacture high-strength ultrafine steel wire, and
It was done. The present invention has been made based on the above findings.
The main point is that in weight%, C: 0.8 to 1.1%, Si: 0.1 to 0.5
%, Mn: 0.2-0.7%, Al: 0.005% or less
Or Cr or 0.05 to 0.5%, Ni: 0.1 to 1.0
%, V: one or more of 0.05 to 0.3%, with the balance being Fe and inevitable
Consist of natural impuritiesIntermediate wire drawing from hot rolled wire rods, patente
After repeating the printing process to the specified wire diameter,
And then plating, 0.05 ~
Wet wire drawing to 0.4mm wire diameterIn steel wire,
After the final patenting treatment of the steel wire rod, Die approach angle: 8-12 ° Die bearing length: 0.2 ~ 0.5D (D: Die
Diameter) Wire drawing using a die that satisfies the conditions of
10% or more of the tensile breaking load of the steel wire
While passing between multiple rolls at a bending angle of 15 to 30 °
Manufactured by 3702MPa tensile strength
As described above, the yield ratio is 0.93 or more, and the residual stress of the surface layer is +2.
Excellent fatigue properties characterized by being less than 00MPa
A high-strength ultrafine steel wire and a method for manufacturing the same.
【０００８】[0008]
【作用】以下に本発明を詳細に説明する。まず、本発明
の対象とする鋼の化学成分の限定理由について説明す
る。Ｃ ：Ｃはパテンティング処理後の引張強さの増加および
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。０．
８％未満では合金元素を添加してもパテンティング処理
後の引張強さが低く、伸線加工硬化率も小さいため最終
的に高強度の極細鋼線が得られないために下限を０．８
％に制限した。一方１．１％を越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あるいは撚り線加
工工程で断線が頻発するため０．８〜１．１％の範囲に
限定した。The present invention will be described below in detail. First, the reasons for limiting the chemical components of the steel targeted by the present invention will be described. C : C has the effect of increasing the tensile strength after the patenting treatment and increasing the drawing work hardening rate, and can increase the tensile strength of the ultrafine steel wire with less drawing strain. 0.
If it is less than 8%, even if an alloy element is added, the tensile strength after the patenting treatment is low, and the wire work hardening rate is also small, so that a high-strength ultrafine steel wire cannot be finally obtained, so the lower limit is 0.8.
%. On the other hand, if it exceeds 1.1%, proeutectoid cementite precipitates at the austenite grain boundaries during the patenting treatment, deteriorating the wire drawing workability, and frequently causes wire breakage in the wire drawing step or the stranded wire processing step. .1%.
【０００９】Ｓｉ：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。
０．１％未満では上記の効果が期待できず、一方０．５
％を越えて添加してもその効果が飽和するため、０．１
〜０．５％の範囲に制限した。Ｍｎ ：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が、０．２％未満
では上記の効果が得られず、一方０．７％を越えると上
記の効果が飽和しさら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
生産性が低下するため、０．２〜０．７％の範囲に限定
した。[0009] Si : Si is an effective element for strengthening ferrite in pearlite and for deoxidizing steel.
If it is less than 0.1%, the above effect cannot be expected.
%, The effect is saturated.
Limited to the range of ~ 0.5%. Mn : Mn is an element effective not only for deoxidation and desulfurization but also for improving the hardenability of steel and increasing the tensile strength after patenting, but is less than 0.2% If the above effect is not obtained, on the other hand, if it exceeds 0.7%, the above effect is saturated, and the processing time for completing the pearlite transformation at the time of the patenting process becomes too long, thereby lowering the productivity. It was limited to the range of 0.2 to 0.7%.
【００１０】Ａｌ：Ａｌは０．００５％を越えると鋼中
の介在物の中で最も硬質なＡｌ2 Ｏ 3 系介在物が生成し
やすくなり、伸線加工あるいは撚り線加工の際の断線原
因となるため、０．００５％以下に制限した。本発明に
よる疲労特性の優れた高強度極細鋼線においては、上記
の元素に加えて、更にＣｒ：０．０５〜０．５％、Ｎ
ｉ：０．１〜１．０％、Ｖ：０．０５〜０．３％の範囲
で１種または２種以上を含有することができる。[0010]Al: Al exceeds 0.005% in steel
Al hardest among inclusionsTwoO ThreeSystem inclusions
Wire breakage during wire drawing or stranded wire processing
Therefore, the content was limited to 0.005% or less. In the present invention
In the case of high-strength extra-fine steel wire with excellent fatigue characteristics
In addition to the elements, Cr: 0.05-0.5%, N
i: 0.1-1.0%, V: 0.05-0.3%
May be used alone or in combination of two or more.
【００１１】Ｃｒ：Ｃｒはパーライトのセメンタイト間
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
とともに特に伸線加工硬化率を向上させる作用があり、
極細鋼線を高強度化するために有効な元素である。０．
００５％未満では前記作用の効果が少なく、一方０．５
％を越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するため、０．０５〜
０．５％の範囲に限定した。 Cr : Cr has the effect of making the cementite spacing of pearlite finer, increasing the tensile strength after the patenting treatment, and particularly improving the wire drawing work hardening rate,
It is an effective element for increasing the strength of ultrafine steel wires. 0.
If it is less than 005%, the effect of the above effect is small, while
%, The finish time of the pearlite transformation during the patenting process becomes longer and the productivity is reduced.
The range was limited to 0.5%.
【００１２】Ｎｉ：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し、更
に腐食疲労強度も向上させる効果があるが、０．１％未
満では上記の効果が得られず、１．０％を越えても添加
量に見合うだけの効果が少ないためこれを上限とした。Ｖ ：Ｖはパーライトのセメンタイト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。０．
０５％未満では、その効果が期待できず、一方０．３％
を越えると効果が飽和するため０．０５〜０．３％の範
囲に制限した。 Ni : Ni has the effect of improving the drawability of the pearlite generated during transformation during the patenting process and further improving the corrosion fatigue strength. However, if it is less than 0.1%, the above effects can be obtained. However, even if the content exceeds 1.0%, the effect corresponding to the added amount is small, so that the upper limit was set. V : V has the effect of reducing the pearlite cementite spacing and increasing the tensile strength after patenting. 0.
If it is less than 05%, the effect cannot be expected, while 0.3%
Is exceeded, the effect saturates, so the range is limited to 0.05 to 0.3%.
【００１３】他の元素は特に限定しないが、Ｐ：０．０
１５％以下、Ｓ：０．０１５％以下、Ｎ：０．００５％
以下が望ましい範囲である。次に、本発明で目的とする
高強度極細鋼線の高疲労強度化に極めて有効な鋼線の降
伏比と表層の残留応力の限定理由について述べる。図１
に鋼線の降伏比と０．２mmの鋼線の疲労限の関係につい
て解析した一例を示す。ここで降伏比とは、０．２％耐
力と引張強さの比を表す。通常に伸線加工を行った場合
の鋼線の降伏比は０．９０程度であるが、同図から０．
９０では疲労限が低いことがわかる。これに対して、降
伏比を０．９３以上にすると疲労限が大幅に向上するこ
とから、極細鋼線の降伏比を０．９３以上に限定した。
なお、０．９５以上の領域で顕著な効果があることか
ら、好ましい条件は０．９５以上である。図２に極細鋼
線の表層残留応力と疲労限の関係について解析した一例
を示す。表層の残留応力が＋２００MPa 以下で、鋼線の
疲労限が著しく向上することから、表層の残留応力を＋
２００MPa 以下に制限した。なお、従来の知見では、表
層の残留応力を圧縮側にしないと効果がないという報告
例が多いが、本発明では、降伏比の効果が大きいため、
残留応力が引張側でも疲労側が著しく向上することが特
徴である。The other elements are not particularly limited, but P: 0.0
15% or less, S: 0.015% or less, N: 0.005%
The following are desirable ranges. Next, the reasons for limiting the yield ratio of the steel wire and the residual stress in the surface layer, which are extremely effective in increasing the fatigue strength of the high-strength ultrafine steel wire, which are the objectives of the present invention, will be described. FIG.
Fig. 1 shows an example of analysis of the relationship between the yield ratio of steel wires and the fatigue limit of 0.2 mm steel wires. Here, the yield ratio indicates a ratio between 0.2% proof stress and tensile strength. The yield ratio of the steel wire when wire drawing is performed normally is about 0.90.
90 indicates that the fatigue limit is low. On the other hand, when the yield ratio is 0.93 or more, the fatigue limit is greatly improved. Therefore, the yield ratio of the ultrafine steel wire is limited to 0.93 or more.
In addition, since a remarkable effect is obtained in a region of 0.95 or more, a preferable condition is 0.95 or more. FIG. 2 shows an example in which the relationship between the residual stress in the surface layer of the ultrafine steel wire and the fatigue limit is analyzed. When the residual stress of the surface layer is +200 MPa or less and the fatigue limit of the steel wire is significantly improved, the residual stress of the surface layer is reduced by +200 MPa.
It was limited to 200MPa or less. In addition, in the conventional knowledge, there are many reports that there is no effect unless the residual stress of the surface layer is on the compression side, but in the present invention, since the effect of the yield ratio is large,
It is characterized that the residual stress is significantly improved on the fatigue side even on the tensile side.
【００１４】次に、降伏比を０．９３以上、表層の残留
応力を２００MPa 以下にするための方法について述べ
る。ここで、鋼線の降伏比に対しては、伸線加工後の曲
げ加工条件が、残留応力に対しては曲げ加工条件と伸線
加工に用いるダイスのアプローチ角度およびベアリング
長さがそれぞれ影響を及ぼす。まず、残留応力である
が、図３はダイスのアプローチ角度と極細鋼線の残留応
力について解析した一例を示す。なお、同図において、
○印は伸線加工後に曲げ加工を施さなかった例であり、
また●印は曲げ加工を行った例である。アプローチ角度
が低くなるにつれて残留応力が低下するが、伸線加工後
に曲げ加工を行わないと、２００MPa 以下にならないこ
とがわかる。また、曲げ加工を行っても、アプローチ角
度が１２°を越えると残留応力を２００MPa 以下にする
ことが困難であるためアプローチ角度の上限を１２°に
限定した。一方、アプローチ角度は８°未満でも残留応
力を２００MPa 以下にすることが可能であるが、伸線加
工時の引き抜き力が増加するため、下限を８°とした。
同様に、ベアリング長さが０．５Ｄ（Ｄ：ダイス径）を
越えると、適正な曲げ加工を行っても残留応力を２００
MPa 以下にすることが困難であるため、ベアリング長さ
の上限を０．５Ｄに制限した。また、ベアリング長さが
０．２Ｄ未満では極細鋼線の直線性が劣化するために、
下限を０．２Ｄに限定した。Next, a method for reducing the yield ratio to 0.93 or more and the residual stress in the surface layer to 200 MPa or less will be described. Here, the bending conditions after wire drawing have an effect on the yield ratio of the steel wire, and the bending angle and the approach angle and bearing length of the die used for wire drawing have an effect on the residual stress. Exert. First, regarding the residual stress, FIG. 3 shows an example in which the approach angle of the die and the residual stress of the ultrafine steel wire are analyzed. In the figure,
○ marks are examples where bending was not performed after wire drawing.
The mark ● indicates an example of bending. It can be seen that the residual stress decreases as the approach angle decreases, but it does not become less than 200 MPa unless bending is performed after wire drawing. Further, even if bending is performed, if the approach angle exceeds 12 °, it is difficult to reduce the residual stress to 200 MPa or less, so the upper limit of the approach angle is limited to 12 °. On the other hand, although the residual stress can be reduced to 200 MPa or less even when the approach angle is less than 8 °, the lower limit is set to 8 ° because the drawing force during wire drawing increases.
Similarly, when the bearing length exceeds 0.5D (D: die diameter), the residual stress is reduced to 200 even if proper bending is performed.
Since it is difficult to reduce the pressure to MPa or less, the upper limit of the bearing length is limited to 0.5D. If the bearing length is less than 0.2D, the linearity of the ultrafine steel wire will deteriorate,
The lower limit was limited to 0.2D.
【００１５】次に鋼線の降伏比と残留応力に対して影響
のある曲げ加工条件について述べる。鋼線の降伏比に及
ぼす張力の影響について解析した一例を図４に示す。引
張破断加重の１０％以上の張力を付与しなければ、降伏
比が０．９３以上にならないことがわかる。また、上記
に述べたダイスを用いても表層の残留応力を２００MPa
以下にすることが困難なため、曲げ加工時の張力の下限
を引張破断加重の１０％に制限した。一方、引張破断加
重の５０％を越えるような張力を付与しても極細鋼線の
疲労限の向上量が少なく、断線する危険性も高まるため
上限を５０％に制限した。また、曲げ加工は図５に示す
ような５個以上のロールを有する治具を用いて実施する
ことができる。ここで曲げ角度は角度が１５°未満で
は、張力が適正な範囲にあっても、降伏比を０．９３以
上にすることが困難であると共に残留応力を２００MPa
以下にできないため、曲げ角度の下限を１５°に限定し
た。一方３０°を越えて実施しても効果が飽和し、更に
曲げ加工後の鋼線の直線性が劣化するために上限を３０
°に制限した。Next, the bending conditions which affect the yield ratio and residual stress of the steel wire will be described. FIG. 4 shows an example of analyzing the effect of tension on the yield ratio of a steel wire. It is understood that the yield ratio does not become 0.93 or more unless a tension of 10% or more of the tensile breaking load is applied. In addition, the residual stress of the surface layer can be reduced to 200 MPa by using the above-described die.
Since it is difficult to reduce the tension below, the lower limit of the tension during bending is limited to 10% of the tensile breaking load. On the other hand, even if a tension exceeding 50% of the tensile breaking load is applied, the amount of improvement in the fatigue limit of the ultrafine steel wire is small and the risk of disconnection increases, so the upper limit was limited to 50%. The bending can be performed using a jig having five or more rolls as shown in FIG. If the bending angle is less than 15 °, it is difficult to increase the yield ratio to 0.93 or more and to reduce the residual stress to 200 MPa even when the tension is in an appropriate range.
Since the angle cannot be reduced below, the lower limit of the bending angle is limited to 15 °. On the other hand, the effect is saturated even if it is performed beyond 30 °, and the linearity of the steel wire after bending is deteriorated.
°.
【００１６】[0016]
【実施例】以下、実施例により本発明の効果をさらに具
体的に説明する。表１に供試材の化学組成を示す。EXAMPLES Hereinafter, the effects of the present invention will be described more specifically with reference to examples. Table 1 shows the chemical composition of the test materials.
【００１７】[0017]
【表１】 [Table 1]
【００１８】これらの供試材を熱間圧延により線径５．
５mmにし、一次伸線加工、一次パテンティング処理、二
次伸線加工を行った。その後、最終パテンティング処理
（オーステナイト化温度：９５０℃、鉛浴温度：５６０
〜６００℃）、引き続きブラスめっき処理を行い、伸線
速度６００ｍ／分の条件で湿式伸線加工を行った。表２
に伸線加工時に用いたダイス形状、伸線加工後の曲げ加
工条件を示す。表３に表２に示した伸線加工および曲げ
加工条件で処理された極細鋼線の降伏比、残留応力並び
に疲労強度等の機械的性質を示す。なお、疲労強度（１
０7 サイクル）は、温度：２０〜２５℃、湿度：５０〜
６０％の条件で行い、回転曲げ疲労試験で評価した結果
である。These test materials were hot-rolled to a wire diameter of 5.
It was set to 5 mm and subjected to primary drawing, primary patenting, and secondary drawing. Thereafter, a final patenting treatment (austenitizing temperature: 950 ° C., lead bath temperature: 560)
〜600 ° C.), followed by brass plating, and wet drawing at a drawing speed of 600 m / min. Table 2
The die shape used during wire drawing and the bending conditions after wire drawing are shown in FIG. Table 3 shows the mechanical properties such as the yield ratio, residual stress, and fatigue strength of the ultrafine steel wire processed under the drawing and bending conditions shown in Table 2. The fatigue strength (1
0 7 cycles), temperature: 20~25 ℃, Humidity: 50
This is a result of performing the test under a condition of 60% and evaluating by a rotating bending fatigue test.
【００１９】[0019]
【表２】 [Table 2]
【００２０】[0020]
【表３】 [Table 3]
【００２１】同表において、試験No．（１），（４），
（５），（７），（９），（１２），（１３），（１
４）が本発明例で、その他は比較例である。表３に見ら
れるように、本発明例はいずれも引張強さが3702MPa以
上で、極細鋼線の降伏比が０．９３以上であるとともに
表層の残留応力が２００MPa 以下となっており、この結
果、疲労強度の高い極細鋼線が実現されている。In the table, test No. (1), (4),
(5), (7), (9), (12), (13), (1
4) is an example of the present invention, and the others are comparative examples. As can be seen from Table 3, all of the examples of the present invention have a tensile strength of 3702 MPa or less.
Above, the yield ratio of the ultrafine steel wire is 0.93 or more, and the residual stress of the surface layer is 200 MPa or less. As a result, an ultrafine steel wire with high fatigue strength is realized.
【００２２】これに対して比較例であるNo．２，１１，
１５は、伸線加工時のダイス形状が不適切なために、伸
線加工後に適正な曲げ加工を施しても表層の残留応力を
２００MPa 以下にすることができず、疲労強度が向上し
なかった例である。即ち、No．２，１４はアプローチ角
度が１２°を越えており、また、No．１１はベアリング
長さが０．５Ｄを越えているために、いずれも残留応力
が２００MPa を越えている。On the other hand, the comparative example No. 2,11,
In No. 15, the residual stress of the surface layer could not be reduced to 200 MPa or less even if proper bending was performed after the wire drawing because the die shape at the time of wire drawing was inappropriate, and the fatigue strength was not improved. It is an example. That is, No. In Nos. 2 and 14, the approach angle exceeded 12 °. 11 has a residual stress exceeding 200 MPa because the bearing length exceeds 0.5D.
【００２３】また、No．３，８は伸線加工後に曲げ加工
を施さなかったために、降伏比が０．９３未満であると
ともに、残留応力も２００MPa 以下にすることが出来な
かった例である。この結果、疲労強度も本発明例に比べ
大幅に劣っている。更に、比較例であるNo．６，１０，
１６は伸線加工後の曲げ加工条件が不適切な例である。
即ち、No．６は曲げ角度が低すぎて残留応力が２００MP
a を越えており、No．１０は曲げ加工時の張力を付与し
なかったために降伏比が０．９３未満となっている。ま
た、No．１６は張力が低すぎるために降伏比を高めるこ
とが出来なかった例である。この結果、いずれも疲労強
度の改善が達成できていない。In addition, No. Nos. 3 and 8 are examples in which the bending process was not performed after the wire drawing process, so that the yield ratio was less than 0.93 and the residual stress could not be reduced to 200 MPa or less. As a result, the fatigue strength is also significantly inferior to the examples of the present invention. Further, in Comparative Example No. 6,10,
Reference numeral 16 denotes an example in which the bending conditions after the wire drawing are inappropriate.
That is, No. 6: bending angle is too low and residual stress is 200MP
a. In No. 10, the yield ratio was less than 0.93 because no tension was applied during bending. No. No. 16 is an example in which the yield ratio could not be increased because the tension was too low. As a result, none of them has achieved improvement in fatigue strength.
【００２４】[0024]
【発明の効果】以上の実施例からも明かなごとく、本発
明は、高強度極細鋼線の疲労強度向上に対して、表層の
残留応力制御以外に降伏比の増加が極めて有効であるこ
とを見出すとともに、伸線加工時のダイス形状、伸線加
工後の曲げ加工条件を最適に選択すれば降伏比と残留応
力制御が可能であることを明らかにすることによって、
疲労特性の優れた高強度極細鋼線を実現したものであ
り、産業上の効果は極めて顕著なものがある。As is clear from the above embodiments, the present invention shows that an increase in the yield ratio is extremely effective for improving the fatigue strength of a high-strength ultrafine steel wire, in addition to controlling the residual stress in the surface layer. In addition to finding out, it is possible to control the yield ratio and residual stress if the die shape during wire drawing and the bending conditions after wire drawing are optimally selected.
This realizes a high-strength ultrafine steel wire with excellent fatigue characteristics, and has extremely remarkable industrial effects.
【図１】高強度極細鋼線の疲労強度に及ぼす降伏比の影
響について解析した一例を示す図である。FIG. 1 is a diagram showing an example of analyzing the effect of the yield ratio on the fatigue strength of a high-strength ultrafine steel wire.
【図２】高強度極細鋼線の疲労強度に及ぼす残留応力の
影響について解析した一例を示す図である。FIG. 2 is a diagram showing an example of analyzing the effect of residual stress on the fatigue strength of a high-strength ultrafine steel wire.
【図３】極細鋼線の残留応力に及ぼすダイスのアプロー
チ角度と曲げ加工の影響について解析した一例を示す図
である。FIG. 3 is a diagram showing an example in which the influence of a die approach angle and bending on the residual stress of an ultrafine steel wire is analyzed.
【図４】極細鋼線の降伏比と曲げ加工時の張力の関係に
ついて解析した一例を示す図である。FIG. 4 is a diagram showing an example in which the relationship between the yield ratio of ultrafine steel wires and the tension during bending is analyzed.
【図５】高強度極細鋼線に曲げ加工を施す治具の一例を
示す図である。FIG. 5 is a diagram showing an example of a jig for bending a high-strength ultrafine steel wire.
１…ロール ２…鋼線 1 ... roll 2 ... steel wire
フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｄ０７Ｂ 1/06 Ｄ０７Ｂ 1/06 Ａ (56)参考文献 特開 平２−217421（ＪＰ，Ａ) 特開 平６−158225（ＪＰ，Ａ) 特開 平６−346190（ＪＰ，Ａ) 特開 平８−27539（ＪＰ，Ａ) 特開 平６−254647（ＪＰ，Ａ) 特開 平６−312209（ＪＰ，Ａ) 特開 平７−1027（ＪＰ，Ａ) 特公 昭50−19512（ＪＰ，Ｂ１) (58)調査した分野(Int.Cl.7，ＤＢ名) B21F 1/00 - 1/06 C22C 38/00 - 38/60 B21C 1/00 D06B 1/02 Continuation of the front page (51) Int.Cl. 7 Identification symbol FI D07B 1/06 D07B 1/06 A (56) References JP-A-2-217421 (JP, A) JP-A-6-158225 (JP, A JP-A-6-346190 (JP, A) JP-A-8-27539 (JP, A) JP-A-6-254647 (JP, A) JP-A-6-312209 (JP, A) 1027 (JP, A) JP 50-19512 (JP, B1) (58) Fields investigated (Int. Cl. 7 , DB name) B21F 1/00-1/06 C22C 38/00-38/60 B21C 1/00 D06B 1/02
Claims (4)
％、 Ｍｎ：０．２〜０．７％、 Ａｌ：０．００５％以
下、 を含有し残部はＦｅおよび不可避的不純物からなる熱間
圧延線材から中間伸線、パテンティング処理を繰り返し
所定の線径にした後、最終パテンティング処理を行い、
めっき処理を施し、０．０５〜０．４mmの線径まで湿式
伸線加工された鋼線において、鋼線材を前記最終パテン
ティング処理後、 ダイスのアプローチ角度：８〜１２° ダイスのベアリング長さ：０．２〜０．５Ｄ（Ｄ：ダイ
ス径） の条件を満たすダイスを用いて伸線加工を行い、引き続
き鋼線の引張破断荷重の１０％以上の張力を鋼線に付与
しつつ複数個のロール間を曲げ角度１５〜３０°で通過
させることにより製造された、 引張強さが３７０２MPa
以上で、降伏比が０．９３以上、表層の残留応力が＋２
００MPa以下であることを特徴とする疲労特性の優れた
高強度極細鋼線。C .: 0.8 to 1.1% by weight, Si: 0.1 to 0.5% by weight
%, Mn: 0.2-0.7%, Al: 0.005% or less
Below, with the balance being Fe and unavoidable impuritiesHot
Repeated intermediate drawing and patenting from rolled wire
After the specified wire diameter, perform the final patenting process,
Plating process, wet type up to 0.05-0.4mm wire diameter
Wire-drawnIn steel wire,The steel wire rod is applied to the final patent
After the Die approach angle: 8-12 ° Die bearing length: 0.2 ~ 0.5D (D: Die
Diameter) Wire drawing using a die that satisfies the conditions of
10% or more of the tensile breaking load of the steel wire
While passing between multiple rolls at a bending angle of 15 to 30 °
Manufactured by 3702MPa tensile strength
As described above, the yield ratio is 0.93 or more, and the residual stress of the surface layer is +2.
Excellent fatigue properties characterized by being less than 00MPa
High strength extra fine steel wire.
項１記載の疲労特性の優れた高強度極細鋼線。2. The method according to claim 1, wherein one or more of Cr: 0.05 to 0.5%, Ni: 0.1 to 1.0%, and V: 0.05 to 0.3% are contained in% by weight. High strength ultra-fine steel wire with excellent fatigue properties.
圧延線材から中間伸線、パテンティング処理を繰り返し
所定の線径にした後、最終パテンティング処理を行い、
めっき処理を施し０．０５〜０．４mmの線径まで湿式伸
線加工する方法であって、鋼線材を前記最終パテンティ
ング処理後、 ダイスのアプローチ角度：8〜12゜ ダイスのベアリング長さ：0.2〜0.5Ｄ（Ｄ：ダイス径） の条件を満たすダイスを用いて伸線加工を行い、引き続
き鋼線の引張破断荷重の10％以上の張力を鋼線に付与し
つつ複数個のロール間を曲げ角度15〜30゜で通過させ、
引張強さが3702MPa以上で、降伏比が0.93以上、表層の
残留応力が＋200MPa以下である鋼線を製造することを特
徴とする疲労特性の優れた高強度極細鋼線の製造方法。In wherein wt%, C: 0.8~1.1%, Si : 0.1~0.5%, Mn: 0.2~0.7%, Al: 0.005% or less, containing the balance between heat consisting of Fe and unavoidable impurities
Repeated intermediate drawing and patenting from rolled wire
After the specified wire diameter, perform the final patenting process,
Plating treatment and wet drawing to 0.05-0.4mm wire diameter
In this method, a steel wire rod is subjected to the final patenting process, and a die approach angle: 8 to 12 mm. A die bearing length: 0.2 to 0.5 D (D: die diameter) is used. The steel wire is passed through a plurality of rolls at a bending angle of 15 to 30 ° while applying a tension of 10% or more of the tensile breaking load of the steel wire to the steel wire .
Tensile strength is 3702MPa or more, yield ratio is 0.93 or more,
Excellent process for producing a high-strength ultra-fine steel wire fatigue residual stress characterized that you produce steel wire is less than + 200 MPa.
項３記載の疲労特性の優れた高強度極細鋼線の製造方
法。4. The method according to claim 3, further comprising one or more of Cr: 0.05 to 0.5%, Ni: 0.1 to 1.0%, and V: 0.05 to 0.3% by weight%. Method for producing high-strength ultrafine steel wire with excellent fatigue characteristics.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP09386495A JP3267833B2 (en) | 1995-04-19 | 1995-04-19 | High-strength extra-fine steel wire with excellent fatigue properties and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP09386495A JP3267833B2 (en) | 1995-04-19 | 1995-04-19 | High-strength extra-fine steel wire with excellent fatigue properties and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08291369A JPH08291369A (en) | 1996-11-05 |
| JP3267833B2 true JP3267833B2 (en) | 2002-03-25 |
Family
ID=14094319
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP09386495A Expired - Fee Related JP3267833B2 (en) | 1995-04-19 | 1995-04-19 | High-strength extra-fine steel wire with excellent fatigue properties and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3267833B2 (en) |
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-
1995
- 1995-04-19 JP JP09386495A patent/JP3267833B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114811207A (en) * | 2021-01-28 | 2022-07-29 | 横滨橡胶株式会社 | Method for determining specification of metal wire for hose and hose |
| CN114811207B (en) * | 2021-01-28 | 2023-11-10 | 横滨橡胶株式会社 | Method for determining specification of metal wire for hose and hose |
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| Publication number | Publication date |
|---|---|
| JPH08291369A (en) | 1996-11-05 |
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