JPS63179017A - Manufacture of extra high tension steel wire having superior ductility - Google Patents
Manufacture of extra high tension steel wire having superior ductilityInfo
- Publication number
- JPS63179017A JPS63179017A JP997787A JP997787A JPS63179017A JP S63179017 A JPS63179017 A JP S63179017A JP 997787 A JP997787 A JP 997787A JP 997787 A JP997787 A JP 997787A JP S63179017 A JPS63179017 A JP S63179017A
- Authority
- JP
- Japan
- Prior art keywords
- steel wire
- wire
- diameter
- ductility
- tensile strength
- 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 44
- 239000010959 steel Substances 0.000 title claims abstract description 44
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 238000005452 bending Methods 0.000 claims abstract description 12
- 229910000677 High-carbon steel Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract 3
- 238000005491 wire drawing Methods 0.000 claims description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims 4
- 239000012535 impurity Substances 0.000 claims 2
- 229910052742 iron Inorganic materials 0.000 claims 2
- 239000002184 metal Substances 0.000 claims 1
- 229910052751 metal Inorganic materials 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 abstract 1
- 238000000034 method Methods 0.000 description 12
- 230000000694 effects Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 6
- 238000011282 treatment Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 241000446313 Lamella Species 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000006378 damage Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 230000032683 aging Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000009931 harmful effect Effects 0.000 description 1
- 230000020169 heat generation Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- LRXTYHSAJDENHV-UHFFFAOYSA-H zinc phosphate Chemical compound [Zn+2].[Zn+2].[Zn+2].[O-]P([O-])([O-])=O.[O-]P([O-])([O-])=O LRXTYHSAJDENHV-UHFFFAOYSA-H 0.000 description 1
- 229910000165 zinc phosphate Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Metal Extraction Processes (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は延性の優れた超高張力鋼線の製造方法に関する
。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a method for producing ultra-high tensile strength steel wire with excellent ductility.
［従来の技術とその問題点］
ピアノ線およびこれに準じる鋼線は、ＰＷＳワイヤ、ば
ね、ホースワイヤ、タイヤコード等広い分野で使用され
ているが、近年、ＪＩＳ以上の強度レベルを有する鋼線
の開発に対する要望が高まっている。[Prior art and its problems] Piano wire and similar steel wires are used in a wide range of fields such as PWS wires, springs, hose wires, and tire cords, but in recent years, steel wires with a strength level higher than JIS have been used. There is a growing demand for the development of
通常、高張力鋼線という場合、 Ｊ Ｉｓ Ｇ ３５
２２ピアノ線相当の強度を有する鋼線を指すのが通例で
あるため、以上１本発明においては、それ以上の強度を
有する鋼線を「超高張力鋼線」と称することとする。Usually, when referring to high tensile strength steel wire, J Is G 35
Since it is customary to refer to a steel wire having a strength equivalent to that of a No. 22 piano wire, in the present invention, a steel wire having a strength higher than that is referred to as an "ultra-high tensile steel wire."
Ｊ Ｉ Ｓ Ｇ３５２２では、直径６■から０．０８
ｍｍ迄の鋼線の引張強さを規定しているが、引張強さは
線径に依存し、線径の細いほど容易に高強度を達成しう
ろため、 、Ｊ Ｉ Ｓにおいてもこれに準じた体系を
なしており、引張強さの上限は±１０ｋｇｆ／ａｍ”以
内の誤差で次式で表わせる。JIS G3522 has a diameter of 6 to 0.08
The tensile strength of steel wires up to mm is specified, but the tensile strength depends on the wire diameter, and the thinner the wire diameter, the easier it is to achieve high strength. The upper limit of the tensile strength can be expressed by the following formula with an error within ±10 kgf/am.
’ｌ’ Ｓ ＝２５０−＋００ｌｏｇｄ （ｋｇｆ／ｍ
ｍ２）・・・・・・（１）但し、ｄは鋼線の直径（ｍ−
）である。'l' S =250-+00logd (kgf/m
m2)...(1) However, d is the diameter of the steel wire (m-
).
（１）式は、６〜０．０８ｗｔｍの鋼線について求めた
ものであるが、凡そ１０〜０．０５ｍ園の範囲で妥当な
ものである。鋼線の断面形状は、円形が多く用いられる
が、角形、梯形１台形等であっても良い、この場合、ｄ
としては同じ断面積を有する円の直径を用いる。Equation (1) was determined for a steel wire of 6 to 0.08 wtm, and is appropriate within the range of approximately 10 to 0.05 m. The cross-sectional shape of the steel wire is often circular, but it may also be square, trapezoidal, trapezoidal, etc. In this case, d
For , use the diameter of a circle with the same cross-sectional area.
ピアノ線およびこれに準じる鋼線は、ピアノ線材相当の
線材を用い、これにパテンティング処理を施したのち、
常温で伸線して、製造されるのが一般的である。Piano wire and similar steel wire use wire rod equivalent to piano wire, and after applying patenting treatment to it,
It is generally manufactured by drawing wire at room temperature.
従来の伸線法で、（１）弐以上の強度レベルの超高張力
鋼線を製造しようとした場合、以下のような問題を生じ
る。When attempting to manufacture ultra-high tensile strength steel wire with a strength level of (1) 2 or higher using conventional wire drawing methods, the following problems arise.
即ち強度を高めるためには、パテンティング処理時の強
度を高める方法と、伸線減面率を大きくする方法がある
が、いずれの方法においても、通常の伸線方法で製造す
るかぎり、強度を高めることは可能であっても、超高張
力鋼線にとって重要な特性である延性、特に捻り特性お
よび絞りの低下が著しく、撚り線やコイリング等の工程
で、割れや断線などのトラブルが発生しやすくなる。In other words, there are two ways to increase strength: one is to increase the strength during the patenting process, and the other is to increase the wire drawing area reduction rate. In either method, as long as the wire is manufactured using the normal wire drawing method, the strength cannot be increased. Even if it is possible to increase the ductility, which is an important characteristic for ultra-high tensile strength steel wires, the deterioration of ductility, especially torsional properties and drawing area, will be significant, and problems such as cracking and wire breakage will occur during processes such as stranding and coiling. It becomes easier.
またピアノ線は、めっきあるいはブルーイング処理をし
て用いることが多いが、これらの処理により１時効が生
じ延性が低下し、超高張力レベルを達成することは困難
である。Piano wire is often used after being plated or blued, but these treatments cause aging and reduce ductility, making it difficult to achieve an ultra-high tensile strength level.
硬引高炭素鋼線に繰返し曲げを加えることにより延性を
改善する方法が特公昭６０−２６８０５．２６８０６に
示されているが、ここに示されている実施例は２．０ｍ
■φ以−ヒのピアノ線相当の高炭素鋼線におけるもので
あり、「超高張力＃ＲＩＩ！」を製造する場合には、鋼
成分に特別の配慮を要するばかりでなく、加工条件も「
超高張力」レベルに対応した特殊なものとなり、該特許
においては十分な効果を得ることはできない。A method of improving ductility by repeatedly bending a hard drawn high carbon steel wire is shown in Japanese Patent Publication No. 60-26805.26806, but the example shown here is 2.0 m long.
■This is a high-carbon steel wire equivalent to a piano wire of
It is a special product that corresponds to the "ultra-high tension" level, and it is not possible to obtain sufficient effects in this patent.
本発明は、このような延性の低下を来たすことなく、超
高張力を達成するための１１線製造方法を提供すること
にある。The object of the present invention is to provide a method for manufacturing 11 wires that achieves ultra-high tensile strength without causing such a decrease in ductility.
［問題点を解決するための手段］
本発明は（］）Ｃ： ０．６〜１．０％、Ｓｉ：０．１
〜２．０％。[Means for solving the problems] The present invention includes (]) C: 0.6 to 1.0%, Si: 0.1
~2.0%.
Ｍｎ ： ０．１〜２．０％の高炭素鋼線材を、減面率
５０％以上の伸線加工の途中、又は、伸線加工後、直径
が０．００２≦ｄ／Ｄ≦０．０３（ｄ：鋼線の直経−−
、Ｄ＝ロールの直径ａｒｍ）であるロールにより２方向
以上の曲げ加工をすることにより、２５０−１００ｌｏ
ｇｄ （ｋｇ／ｍｍ２）以１−の引張り強さとなすこと
を特徴とする、延性の優れた超高張力鋼線の１２造方法
であり又（２）高炭素鋼線材がＣ： ０．６０〜１．０
％、８ｊ：０．１〜２．０％。Mn: 0.1 to 2.0% high carbon steel wire during or after wire drawing with an area reduction of 50% or more, the diameter is 0.002≦d/D≦0.03 (d: Straight line of steel wire--
, D = roll diameter arm) by bending in two or more directions, 250-100 lo
This is a manufacturing method for ultra-high tensile steel wire with excellent ductility, characterized by having a tensile strength of 1- or less than gd (kg/mm2), and (2) the high carbon steel wire has a C: 0.60~ 1.0
%, 8j: 0.1-2.0%.
Ｍｎ ： ０．ｌ〜２．０％、を含み、さらに、 Ｃｒ
： ０．１”ｌ。Mn: 0. l~2.0%, further comprising Cr
: 0.1”l.
θ％、 Ｖ ： ０．００２〜０．５％、 Ｎｂ
： ０．００２〜０．２％。θ%, V: 0.002-0.5%, Nb
: 0.002-0.2%.
Ｔ Ｌ ： ０．００２〜０．２％、の１種以」二を含
む高炭素鋼線材である。前記の（１）に記載の延性に優
れた超高張力鋼線の製造方法である。T L : A high carbon steel wire rod containing one or more of the following: 0.002 to 0.2%. This is a method for producing an ultra-high tensile strength steel wire with excellent ductility as described in (1) above.
鋼組成の限定理由は下記による。The reason for limiting the steel composition is as follows.
Ｃは経済的かつ有効な強化元素であるが、（１）弐以上
の強度を達成するには０．６％以上必要である。又１．
０％以−ヒでは、パテンティング時に初析セメンタイト
を生成し、冷間加工に適さない、但し、（１）弐以上の
強度において、より優れた延性を得るためには、後述の
ような合金元素を含有させることが望ましい。C is an economical and effective reinforcing element, but (1) 0.6% or more is required to achieve a strength of 2 or higher. Also 1.
If it is less than 0%, pro-eutectoid cementite will be formed during patenting, making it unsuitable for cold working. It is desirable to contain elements.
Ｓｉは脱酸のために０．１％以−１−必要である。ｓｉ
は固溶硬化元素として強化にも効果があるが、０゜３５
％５％以上その効果は小さく、２％以上では延性が劣化
するため適当でない。0.1% or more of Si is necessary for deoxidation. si
is effective in strengthening as a solid solution hardening element, but at 0°35
%5% or more, the effect is small, and 2% or more is not suitable because the ductility deteriorates.
鋼線の絞りはパーライトラメラ−間隔と密接な関係があ
り、約２８０人で最大となるが、ｓｌは素材のパーライ
トラメラ−間隔をほとんど変えずに、フェライト層を強
化するため、延性の低下はほとんどなしに、鋼線の強度
をあげることに有効である。The reduction of the steel wire is closely related to the pearlite lamella spacing, reaching a maximum at about 280, but since SL strengthens the ferrite layer without changing the pearlite lamella spacing of the material, the decrease in ductility is It is effective in increasing the strength of steel wire with little effort.
Ｍｎは脱酸およびＳの害を除くために０．１％以上必要
である。Ｍｎは焼入性向上元素として、特に太いサイズ
の線材のパテンティング強度を上げるのに有効であるが
、２％を越えると延性が劣化するため適当でない。Mn is required to be present in an amount of 0.1% or more in order to deoxidize and remove the harmful effects of S. Mn is an element that improves hardenability and is particularly effective in increasing the patenting strength of thick wire rods, but if it exceeds 2%, it is not suitable because the ductility deteriorates.
Ｃｒはパーライトラメラ−間隔の微細化に有効な元素で
あり、細いサイズから太いサイズ迄、Ｍ材の強化に効果
があるが、１％を超えるとその効果を１・分に発揮させ
ることは困難である。Cr is an effective element for refining the spacing between pearlite lamellae, and is effective in strengthening M materials from thin to thick sizes, but if it exceeds 1%, it is difficult to demonstrate the effect in 1 min. It is.
■は焼入性向上元素として、特に太いサイズの線材のパ
テンティング強度を上げるのに有効である。またオース
テナイト結晶粒度を微細化し、延性の向１−に有効であ
る。 ０．００２％以下ではその効果は少なく、Ｏ，Ｓ
％を超えるとかえって延性が劣化するため適当でない。(2) is an element that improves hardenability and is particularly effective in increasing the patenting strength of thick wire rods. It also refines the austenite grain size and is effective in improving ductility. The effect is small below 0.002%, and O,S
%, it is not suitable because the ductility deteriorates.
Ｎｂおよび’ｌ’ ｊはオーステナイト結晶粒度を微細
化し、延性の向Ｉ〕に有効であるが、０．００２％以下
では効果がなく、０．２％を超えると、かえって延性が
劣化するため適当でない。Nb and 'l'j are effective in refining the austenite grain size and improving ductility, but if it is less than 0.002%, it has no effect, and if it exceeds 0.2%, the ductility deteriorates, so it should not be used properly. Not.
なおＡＱについては、細粒鋼が望ましい場合には０．０
１〜０．１％ＰＡＬαを加え、粗粒鋼あるいは介在物の
軟質化が必要な場合には、０．０１％以下とする。Regarding AQ, if fine-grained steel is desired, it should be 0.0.
Add 1 to 0.1% PALα, and if it is necessary to soften coarse-grained steel or inclusions, reduce the amount to 0.01% or less.
これらのいずれの場合もあるため、ＡＱの含有址は特に
規定しない。Since any of these cases may occur, the content of AQ is not particularly specified.
以１−の鋼組成を有する鋼を５０％以上の伸線加工する
ことにより延性の優れた超高張力鋼線を製造することが
可能であるが１通常の伸線加工では、「超高張ノ月レベ
ルまで強度を高めた場合、延性の低ドが大きく、何等か
の対策が必要である。It is possible to produce an ultra-high tensile strength steel wire with excellent ductility by drawing a steel having the following steel composition by 50% or more. If the strength is increased to the same level as the previous month, the ductility will be significantly lower, and some kind of countermeasure will be required.
延性の低下は伸線中の発熱、或は伸線後のブルーイング
処理により、可動転位が固定される場合に顕著に現れる
。これに対し、発明者らが種々の調査を行った結果、材
料の破壊に至らないような軽微な加工を加えた場合、新
たに可動転位が導入される結果、延性の回復が起ること
が観察された。The decrease in ductility becomes noticeable when mobile dislocations are fixed due to heat generation during wire drawing or bluing treatment after wire drawing. On the other hand, as a result of various investigations conducted by the inventors, it was found that when a slight processing that does not lead to material destruction is applied, new mobile dislocations are introduced, resulting in recovery of ductility. observed.
曲げ加］二に関して詳細な調査を行った結果鋼線の強度
が高まると、伸びが低下するため、過大な曲げ加工を行
うと１表層部に微細な割れを生じ。As a result of a detailed study on bending]2, as the strength of the steel wire increases, its elongation decreases, so if excessive bending is performed, minute cracks will occur in the surface layer.
却って延性の低ドを招＜、（１）式以上の強度を有する
超高張力鋼線では１表層の伸びを３％以下にすることが
必要である。一方、延性回復の効果をｔｌ）るためには
、降伏点以上の変形が必要であるため、効果の得られる
下限値は０．２％であった。On the contrary, this leads to a decrease in ductility, and therefore, in ultra-high tensile steel wires having a strength equal to or higher than formula (1), it is necessary to keep the elongation of one surface layer to 3% or less. On the other hand, in order to reduce the effect of ductility recovery, deformation exceeding the yield point is required, so the lower limit for obtaining the effect was 0.2%.
これらの条件は鋼線の直径ｄとロールの直径りの比を０
．００２≦ｄ／１）≦０．０３とすることにより達成さ
れる。These conditions set the ratio of the steel wire diameter d to the roll diameter to 0.
．． This is achieved by satisfying 002≦d/1)≦0.03.
ロールによる曲げ加工の場合、一定の表層伸びを得るた
めにロールと鋼線が密着することが必要であるが、」−
記のｄ／１）の範囲において特に問題はない、またロー
ルと密着している限り、曲げ変形はロールとの接触開始
点および接触終了点の２点のみで起きるため、接触角の
大小には関係しない。In the case of bending using rolls, it is necessary for the rolls and steel wire to be in close contact in order to obtain a certain level of surface elongation.
There is no particular problem within the range of d/1), and as long as the contact is in close contact with the roll, bending deformation occurs only at two points, the contact start point and the contact end point, so the contact angle does not matter. It doesn't matter.
鋼線の断面内で均一な変形を与えるために、２方向以」
〕から曲げ加工することが有効である。In order to give uniform deformation within the cross section of the steel wire,
] is effective.
［実施例］
鋼線材を鉛パテンテイング後酸洗し、スケールを除去し
た後、リン酸亜鉛被膜処理を施した。伸線時には伸線潤
滑剤を用いて、伸線した。[Example] After lead patenting, a steel wire rod was pickled to remove scale, and then subjected to a zinc phosphate coating treatment. A wire drawing lubricant was used during wire drawing.
伸線後、又は伸線の途中で鋼線とローラーの径比ｄ／Ｄ
、曲げ加工の方向を変えて曲げ加工を行った。加工後
の鋼線は、加工ままの状態または４５０℃で、４５秒間
のブルーイング処理を施して、引張試験と捻回試験によ
り材質評価を行った。After wire drawing or during wire drawing, the diameter ratio d/D of steel wire and roller
, the bending process was performed by changing the direction of the bending process. The steel wire after processing was subjected to bluing treatment for 45 seconds at 450° C. or as-processed, and the material quality was evaluated by a tensile test and a twist test.
第１表に各種鋼成分により製造した結果を示す。Table 1 shows the results of manufacturing with various steel components.
従来法の伸線まま、あるいは伸線後ブルーイング処理を
行ったものは、「超高張ノ月レベルを達成しようとする
と、捻回値が低下し、十分な性能が得られないが、本発
明の曲げ加工を施した第１表の発明法によれば、捻回値
および絞りが高く、優れた延性が得られた。With the conventional wire drawing method, or with the bluing treatment applied after drawing, the torsion value decreases and sufficient performance cannot be obtained when trying to achieve the ultra-high tension level. According to the invention method shown in Table 1, in which the bending process was performed, the torsion value and reduction of area were high, and excellent ductility was obtained.
［発明の効果］
本発明は以」〕のように特定の成分を有する鋼線材を、
伸線加工の途中、又は伸線加工後、適正な曲げ加にをす
ることにより延性の劣化なしに、超高張力鋼線を製造す
ることを１１ｆ能とした０本発明により伸線および撚り
線時の断線、成形時の加工割れ、使用時の破壊を著しく
減少せしめることができた。[Effects of the Invention] The present invention provides a steel wire rod having a specific composition as shown below.
Wire drawing and stranding according to the present invention makes it possible to produce ultra-high tensile steel wire without deterioration of ductility by applying appropriate bending during or after wire drawing. We were able to significantly reduce wire breakage during manufacturing, processing cracks during molding, and destruction during use.
Claims (2)
線材を、減面率５０％以上の伸線加工の途中、又は伸線
加工後、直径が０．００２≦ｄ／Ｄ≦０．０３（ｄ：鋼
線の直径ｍｍ、Ｄ：ロールの直径ｍｍ）であるロールに
より２方向以上の曲げ加工をすることにより、２５０−
１００ｌｏｇｄ（ｋｇ／ｍｍ＾２）以上の引張り強さと
なすことを特徴とする、延性の優れた超高張力鋼線の製
造方法。(1) High carbon steel wire rod containing C: 0.60 to 1.0%, Si: 0.1 to 2.0%, Mn: 0.1 to 2.0%, with the balance consisting of iron and inevitable impurities. During wire drawing with an area reduction rate of 50% or more, or after wire drawing, the diameter is 0.002≦d/D≦0.03 (d: steel wire diameter mm, D: roll diameter mm) By bending in two or more directions with a roll of 250-
A method for producing an ultra-high tensile strength steel wire with excellent ductility, characterized by having a tensile strength of 100 logd (kg/mm^2) or more.
Ｔｉ：０．００２〜０．２％、Ｎｂ：０．００２〜０．
２％の１種以上を含み、残部鉄および不可避的不純物か
らなる高炭素鋼線材を、減面率５０％以上の伸線加工の
途中、又は伸線加工後、直径が０．００２≦ｄ／Ｄ≦０
．０３（ｄ：鋼線の直径ｍｍ、Ｄ：ロールの直径ｍｍ）
であるロールにより２方向以上の曲げ加工をすることに
より、２５０−１００ｌｏｇｄ（ｋｇ／ｍｍ＾２）以上
の引張り強さとなすことを特徴とする、延性の優れた超
高張力鋼線の製造方法。(2) Contains C: 0.60 to 1.0%, Si: 0.1 to 2.0%, Mn: 0.1 to 2.0%, and further includes Cr: 0.1 to 1.0. %, V: 0.002-0.5%,
Ti: 0.002-0.2%, Nb: 0.002-0.
During or after wire drawing with an area reduction of 50% or more, a high carbon steel wire rod containing one or more of 2% of the metal and the remainder iron and unavoidable impurities has a diameter of 0.002≦d/ D≦0
．． 03 (d: steel wire diameter mm, D: roll diameter mm)
A method for producing an ultra-high tensile strength steel wire with excellent ductility, characterized in that the wire is bent in two or more directions using a roll, thereby achieving a tensile strength of 250-100 logd (kg/mm^2) or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP997787A JPS63179017A (en) | 1987-01-21 | 1987-01-21 | Manufacture of extra high tension steel wire having superior ductility |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP997787A JPS63179017A (en) | 1987-01-21 | 1987-01-21 | Manufacture of extra high tension steel wire having superior ductility |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63179017A true JPS63179017A (en) | 1988-07-23 |
Family
ID=11734968
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP997787A Pending JPS63179017A (en) | 1987-01-21 | 1987-01-21 | Manufacture of extra high tension steel wire having superior ductility |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63179017A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0708183A1 (en) * | 1993-05-25 | 1996-04-24 | Nippon Steel Corporation | High-carbon steel rod wire or steel wire excellent in workability in wire drawing and process for producing the same |
| US6901782B2 (en) * | 2001-07-30 | 2005-06-07 | Hitachi Metals, Ltd. | Method and apparatus for forming a modified a cross-section wire material |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61165219A (en) * | 1985-01-17 | 1986-07-25 | Nippon Steel Corp | Production of high tensile steel wire excellent in twisting property |
-
1987
- 1987-01-21 JP JP997787A patent/JPS63179017A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61165219A (en) * | 1985-01-17 | 1986-07-25 | Nippon Steel Corp | Production of high tensile steel wire excellent in twisting property |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0708183A1 (en) * | 1993-05-25 | 1996-04-24 | Nippon Steel Corporation | High-carbon steel rod wire or steel wire excellent in workability in wire drawing and process for producing the same |
| EP0708183A4 (en) * | 1993-05-25 | 1996-11-06 | Nippon Steel Corp | High-carbon steel rod wire or steel wire excellent in workability in wire drawing and process for producing the same |
| US6901782B2 (en) * | 2001-07-30 | 2005-06-07 | Hitachi Metals, Ltd. | Method and apparatus for forming a modified a cross-section wire material |
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