JPH08295932A - High strength steel wire excellent in fatigue characteristic - Google Patents
High strength steel wire excellent in fatigue characteristicInfo
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- JPH08295932A JPH08295932A JP9731795A JP9731795A JPH08295932A JP H08295932 A JPH08295932 A JP H08295932A JP 9731795 A JP9731795 A JP 9731795A JP 9731795 A JP9731795 A JP 9731795A JP H08295932 A JPH08295932 A JP H08295932A
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明はタイヤ、ベルト、ホース
などのゴムおよび有機材料の補強用に使用されているス
チールコード、ベルトコードなどの高強度で高延性の極
細鋼線やロープ、ＰＣワイヤなどの高強度の鋼線に関す
るものである。これらの鋼線は、長尺ゴムベルト、スチ
ールタイヤ用コードなどに使用される。BACKGROUND OF THE INVENTION The present invention relates to a steel cord used for reinforcing rubber and organic materials such as tires, belts and hoses, and a high-strength and highly ductile ultrafine steel wire or rope, PC wire such as a belt cord. And high strength steel wire. These steel wires are used for long rubber belts, steel tire cords, and the like.
【０００２】[0002]
【従来の技術】一般にスチールコードなど伸線された高
炭素鋼極細線は、通常必要に応じて熱間圧延した後に調
整冷却した直径４．０〜５．５ｍｍの線材を一次伸線加
工後、最終パテンティング処理を行ない、その後ブラス
メッキ処理をへて最終湿式伸線加工により製造されてい
る。このような極細鋼線の多くは、２本撚り、５本撚り
などの撚り線加工を施した状態でスチールコードとして
使用されている。2. Description of the Related Art In general, drawn high carbon steel ultrafine wire such as steel cord is usually hot-rolled as necessary, and then adjusted and cooled to obtain a wire having a diameter of 4.0 to 5.5 mm, which is subjected to primary wire drawing. The final patenting process is performed, and then the brass plating process is performed to finish the final wet drawing process. Most of such ultra-fine steel wires are used as steel cords in a state in which a twisted wire process such as two-ply twist and five-ply twist is applied.
【０００３】これらのワイヤが具備すべき特性として １．より高強度であること、 ２．高速伸線性が優れていること、 ３．疲労特性が優れていること、 ４．高速撚り線性が優れていること 等が上げられる。The characteristics that these wires must have are: Higher strength, 1. 2. Excellent high-speed drawability, 3. Excellent fatigue characteristics, The high-speed twistability is excellent.
【０００４】このため、従来から要望に応じた高品質の
鋼材が開発されている。例えば、特開昭６０−２０４８
６５号公報には、Ｍｎ含有量を０．３％未満に規制して
鉛パテンティング後の過冷組織の発生を抑え、Ｃ、Ｓ
ｉ、Ｍｎ等の元素量を規制することによって、撚り線時
の断線が少なく高強度および高靭延性の極細線およびス
チールコード用高炭素鋼線材が開示されており、また、
特開昭６３−２４０４６号公報には、Ｓｉ含有量を１．
００％以上とすることによって鉛パテンティング材の引
張強さを高くして伸線加工率を小さくした高靭性高延性
極細線用線材が開示されている。Therefore, high-quality steel materials have been conventionally developed in response to demands. For example, JP-A-60-2048
In Japanese Patent Publication No. 65, the Mn content is restricted to less than 0.3% to suppress the generation of a supercooled structure after lead patenting, and
By controlling the amount of elements such as i and Mn, there is disclosed a high-strength wire and a high-carbon steel wire material for steel cords, which has less breakage when twisted and has high strength and ductility.
JP-A-63-24046 discloses that the Si content is 1.
A wire rod for high toughness and high ductility ultrafine wire in which the tensile strength of the lead patenting material is increased and the wire drawing work ratio is reduced by setting the content to be at least 00% is disclosed.
【０００５】また、一方でこれらの特性に悪影響を与え
るものの一つとして硬質の酸化物系非金属介在物があげ
られる。一般に酸化物系介在物の中でもＡｌ2Ｏ3、Ｓｉ
Ｏ2、ＣａＯ、ＴｉＯ2、ＭｇＯ等の単組成の介在物は硬
度も高く非延性である。従って伸線性に優れた高炭素鋼
線材製造のためには、溶鋼の清浄性を高めるとともに、
酸化物系介在物を低融点化し軟質化する必要がある。On the other hand, a hard oxide type non-metallic inclusion is one of those which adversely affect these characteristics. Generally, among oxide-based inclusions, Al 2 O 3 , Si
Inclusions having a single composition such as O 2 , CaO, TiO 2 , and MgO have high hardness and are non-ductile. Therefore, in order to produce high carbon steel wire rods with excellent wire drawability, while enhancing the cleanliness of molten steel,
It is necessary to lower the melting point and soften the oxide inclusions.
【０００６】この様に鋼の清浄度を上げ、非延性介在物
の軟質化を図る方法として、特公昭５７−２２９６９号
公報に示される伸線性の良好な高炭素鋼線材用鋼の製造
法及び特開昭５５−２４９６１号公報に示される極細線
の製造方法が示されているが、これらの技術の基本思想
は、Ａｌ2Ｏ3−ＳｉＯ2−ＭｎＯの三元系の酸化物系非
金属介在物の組成制御によるものである。[0006] As a method for increasing the cleanliness of steel and softening non-ductile inclusions as described above, a method for producing a steel for high carbon steel wire rod having good wire drawability, which is disclosed in Japanese Patent Publication No. 57-22969. Japanese Unexamined Patent Publication (Kokai) No. 55-24961 discloses a method for producing an ultrafine wire. The basic idea of these techniques is that Al 2 O 3 —SiO 2 —MnO ternary oxide nonmetal. This is because the composition of the inclusions is controlled.
【０００７】一方、特開昭５０−７１５０７号公報で
は、非金属介在物をＡｌ2Ｏ3、 ＳｉＯ2、ＭｎＯの三
元状態図におけるスペーサータイト領域にすることによ
って製品の伸線性を改善することが提案され、また特開
昭５０−８１９０７号公報では溶鋼中に添加するＡｌ量
を規制することによって有害な介在物を減少せしめて、
伸線性を改善する方法が開示されている。On the other hand, in Japanese Unexamined Patent Publication (Kokai) No. 50-71507, the non-metallic inclusion is made into a spacer tight region in the ternary phase diagram of Al 2 O 3 , SiO 2 , and MnO to improve the wire drawability of the product. In Japanese Patent Laid-Open No. 50-81907, the amount of Al added to molten steel is regulated to reduce harmful inclusions.
A method of improving drawability is disclosed.
【０００８】また、特公昭５７−３５２４３号公報にお
いては、非延性介在物指数２０以下のスチールコード製
造に関し、Ａｌ完全規制の下で取鍋溶鋼内にキャリアー
ガス（不活性ガス）と共にＣａＯ含有フラックスを吹込
み、予備脱酸した後、Ｃａ、Ｍｇ、ＲＥＭの一種または
二種以上を含む合金を吹込み介在物を軟質化する方法が
提案されている。Further, Japanese Patent Publication No. 57-35243 discloses a steel cord having a non-ductile inclusion index of 20 or less, and a CaO-containing flux in a ladle molten steel together with a carrier gas (inert gas) under the complete Al regulation. It has been proposed to blow alloys and pre-deoxidize them, and then blow an alloy containing one or more of Ca, Mg and REM to soften inclusions.
【０００９】しかしながら、さらに高強度、高延性、高
疲労強度の鋼線が求められるようになった。However, steel wires having higher strength, higher ductility and higher fatigue strength have been demanded.
【００１０】[0010]
【発明が解決しようとする課題】本発明は、従来の鋼線
では達成し得なかった高強度でかつ疲労特性の優れた鋼
線を提供することを目的とする。SUMMARY OF THE INVENTION It is an object of the present invention to provide a steel wire having high strength and excellent fatigue characteristics which cannot be achieved by the conventional steel wire.
【００１１】[0011]
【課題を解決するための手段】本発明は、（１）Ｃ量が
０．６％以上の鋼において、熱処理によって得られる擬
似パーライト組織が８０％以上となる鋼材を伸線加工に
する事によって得られる引張強さが３６００ＭＰａ以上
の強度を有する疲労特性の優れた高強度鋼線。According to the present invention, (1) a steel having a C content of 0.6% or more has a pseudo-pearlite structure of 80% or more obtained by heat treatment by wire drawing. A high-strength steel wire having excellent tensile properties and a tensile strength of 3600 MPa or more.
【００１２】（２）鋼成分が重量％で Ｃ ：０．６％以上１．５％以下 Ｓｉ：０．１％以上２．０％以下 Ｍｎ：０．１％以上２．０％以下 となる鋼からなることを特徴とする前記（１）の疲労特
性の優れた高強度鋼線。(2) Steel composition in wt% C: 0.6% or more and 1.5% or less Si: 0.1% or more and 2.0% or less Mn: 0.1% or more and 2.0% or less A high-strength steel wire having excellent fatigue properties according to (1) above, which is made of steel.
【００１３】（３）以下の成分の一種以上添加する事を
特徴とする前記（２）の疲労特性の優れた高強度鋼線。 Ｃｒ：０．１％以上２．０％以下 Ｎｉ：０．１％以上２．０％以下 Ｃｕ：０．１％以上２．０％以下 Ｍｏ：０．１％以上２．０％以下 Ｃｏ：０．０１％以上２．０％以下。(3) A high-strength steel wire excellent in fatigue properties according to the above (2), characterized by adding one or more of the following components. Cr: 0.1% or more and 2.0% or less Ni: 0.1% or more and 2.0% or less Cu: 0.1% or more and 2.0% or less Mo: 0.1% or more and 2.0% or less Co: 0.01% or more and 2.0% or less.
【００１４】（４）以下の成分の一種以上を添加する事
を特徴とする前記（２）または（３）の疲労特性の優れ
た高強度鋼線。 Ｔｉ：０．００５％以上０．０３％以下 Ｎｂ：０．００５％以上０．０３％以下 Ｖ ：０．００５％以上０．０３％以下 Ａｌ：０．００５％以上０．０３％以下 Ｂ ：０．０００１％以上０．００３％以下。(4) A high-strength steel wire excellent in fatigue properties according to (2) or (3), characterized in that one or more of the following components are added. Ti: 0.005% or more and 0.03% or less Nb: 0.005% or more and 0.03% or less V: 0.005% or more and 0.03% or less Al: 0.005% or more and 0.03% or less B: 0.0001% or more and 0.003% or less.
【００１５】（５） Ｐ ：０．０２％以下 Ｓ ：０．０２％以下 であることを特徴とする前記（２）または（３）または
（４）の疲労特性の優れた高強度鋼線。(5) P: 0.02% or less S: 0.02% or less A high-strength steel wire excellent in fatigue properties according to the above (2), (3) or (4).
【００１６】[0016]
【作用】以下本発明を詳細に説明する。先ず本発明の限
定理由に関して説明する。なお、以下に示す％は重量％
である。本発明の鋼組成の限定理由は下記の通りであ
る。The present invention will be described in detail below. First, the reason for limitation of the present invention will be described. In addition,% shown below is% by weight
Is. The reasons for limiting the steel composition of the present invention are as follows.
【００１７】Ｃは経済的かつ有効な強化元素である。鋼
線としての必要強度を確保するためにはＣは少なくとも
０．６％以上とすることが必要である。高すぎると延性
が低下するので上限は１．５％とする。C is an economical and effective strengthening element. In order to secure the required strength as a steel wire, it is necessary that C be at least 0.6% or more. If it is too high, the ductility decreases, so the upper limit is made 1.5%.
【００１８】Ｓｉは鋼の脱酸のために必要な元素であ
り、従ってその含有量があまりに少ないとき脱酸効果が
不十分になるので下限を０．１％とする。また、Ｓｉは
熱処理後に形成されるパーライト中のフェライト相に固
溶しパテンティング後の強度を上げるが、反面フェライ
トの延性を低下させるので、伸線後性に悪影響を与えな
い２．０％以下とする。Si is an element necessary for deoxidizing steel. Therefore, if its content is too small, the deoxidizing effect becomes insufficient, so the lower limit is made 0.1%. Further, Si dissolves in the ferrite phase in the pearlite formed after heat treatment to increase the strength after patenting, but on the other hand, it reduces the ductility of the ferrite, so it does not adversely affect the post-drawability. And
【００１９】Ｍｎは鋼の焼き入れ性を確保するために
０．１％以上添加する。しかし、多量のＭｎ添加は偏析
を引き起こしパテンティングの際にベイナイト、マルテ
ンサイトという過冷組織が発生しその後の伸線性を害す
るため２．０％以下とする。Mn is added in an amount of 0.1% or more in order to secure the hardenability of steel. However, addition of a large amount of Mn causes segregation and causes a supercooled structure such as bainite and martensite during patenting, which impairs the subsequent wire drawability, so the content is made 2.0% or less.
【００２０】Ｓは多量に含まれると線材の延性を害する
のでその含有量を０．０２％以下とするのが望ましい。
ＰもＳと同様に線材の延性を害するのでその含有量を
０．０２％以下とするのが望ましい。If a large amount of S is contained, the ductility of the wire is impaired, so the content is preferably 0.02% or less.
Like P, P also impairs the ductility of the wire, so its content is preferably 0.02% or less.
【００２１】Ｃｒはこのようなセメンタイトの異常部の
出現を抑制しさらに、パーライトを微細にする効果を持
っている。しかし、多量の添加は熱処理後のフェライト
中の転移密度を上昇させるため、引き抜き加工後の極細
線の延性を著しく害することになる。従って、Ｃｒの添
加量はその効果が期待できる０．１％以上としフェライ
ト中の転移密度を増加させ延性を害することの無い２．
０％以下とする。Cr has the effect of suppressing the appearance of such abnormal portions of cementite and further refining pearlite. However, addition of a large amount increases the dislocation density in the ferrite after heat treatment, and therefore significantly impairs the ductility of the ultrafine wire after drawing. Therefore, the addition amount of Cr is set to 0.1% or more, which is expected to have the effect, without increasing the dislocation density in ferrite and impairing ductility.
It is 0% or less.
【００２２】ＮｉもＣｒと同じ効果があるため、必要に
よりその効果を発揮する０．１％以上添加する。Ｎｉも
添加量が多くなり過ぎるとフェライト相の延性を低下さ
せるので上限を２．０％とする。Since Ni has the same effect as Cr, if necessary, 0.1% or more is added so that the effect is exhibited. If Ni is added too much, the ductility of the ferrite phase deteriorates, so the upper limit is made 2.0%.
【００２３】Ｃｕは線材の腐食疲労特性を向上させる元
素であるので、必要によりその効果を発揮する０．１％
以上添加することが望ましい。Ｃｕも添加量が多くなり
過ぎるとフェライト相の延性を低下させるので上限を
２．０％とする。Since Cu is an element that improves the corrosion fatigue characteristics of the wire, 0.1% to exert its effect if necessary.
It is desirable to add the above. If Cu is added too much, the ductility of the ferrite phase will be reduced, so the upper limit is made 2.0%.
【００２４】Ｍｏは線材の焼き入れ性を向上するために
添加する元素で、必要によりその効果を発揮する０．１
％以上添加することが望ましい。Ｍｏも添加量が多くな
り過ぎると焼入れ性が高まり、偏析部にミクロマルテン
サイトが析出しやすくなるので上限を２．０％とする。Mo is an element added to improve the hardenability of the wire rod, and if necessary, it exerts its effect.
% Or more is desirable. If Mo is added too much, the hardenability is improved and micro martensite is likely to precipitate in the segregated portion, so the upper limit is made 2.0%.
【００２５】Ｃｏは線材の延性を向上するために添加す
る元素で、必要によりその効果を発揮する０．０１％以
上添加する事が望ましい。Ｃｏは高価な元素であるので
経済性を損なわない２．０％以下の添加とする。Co is an element added to improve the ductility of the wire, and if necessary, it is desirable to add 0.01% or more to exert its effect. Since Co is an expensive element, it is added at 2.0% or less so as not to impair economic efficiency.
【００２６】Ｔｉ、Ｎｂ、Ｖ、Ａｌはγ粒径を微細にし
その後に形成される組織単位を微細にし、靭性値を向上
することが出来るのでその効果を発揮する０．００５％
以上を添加し、その他の特性に悪影響を与える事のない
０．０３％以下とする。Ti, Nb, V, and Al are effective in improving the toughness value by making the γ grain size fine and making the structural unit formed thereafter fine. 0.005%
The above is added to make it 0.03% or less so as not to adversely affect other characteristics.
【００２７】Ｂは焼入れ性を改善するのに添加し、その
効果が認められる０．０００１％以上添加し、焼入れ性
が高くなり過ぎるためその処理が困難となる０．００３
％以下とする。B is added to improve the hardenability, and is added in an amount of 0.0001% or more where the effect is recognized. The hardenability becomes too high and the treatment becomes difficult. 0.003
% Or less.
【００２８】これらの成分からなる材料は一般的には
１．０ｍｍから２．０ｍｍの間で最終パテンティング処
理を行い、伸線加工によって目的の強度にされる。そこ
で、１．７ｍｍφにおいてパーライト組織、擬似パーラ
イト組織、ベイナイト組織のそれぞれを作製し、加工硬
化特性を比較したのが図１である。図１に示されるよう
に、擬似パーライト組織は、パーライト組織より加工硬
化率は落ちるもののベイナイト組織より加工硬化率が大
きくなっている事が判る。The material composed of these components is generally subjected to a final patenting treatment in the range of 1.0 mm to 2.0 mm, and is drawn to a desired strength. Therefore, in FIG. 1, a pearlite structure, a pseudo-pearlite structure, and a bainite structure were produced at 1.7 mmφ and the work hardening characteristics were compared. As shown in FIG. 1, it can be seen that the pseudo-pearlite structure has a work hardening rate lower than that of the pearlite structure, but has a work hardening rate higher than that of the bainite structure.
【００２９】また、先の３つの組織を用いて同一強度に
なるように初線径を変えて熱処理を行い伸線加工により
０．３ｍｍφに加工を行った。引張強さはいずれも、ほ
ぼ３６００ＭＰａとなるように調整されている。図２に
示されるように擬似パーライト組織が最も優れた疲労特
性を示す。これは、擬似パーライト組織の場合、セメン
タイトが粒状に分布していることによる、疲労破壊過程
におけるフェライトとセメンタイトの界面でのクラック
の伝播が起りにくい事と、伸線加工における加工硬化率
もベイナイト組織ほど小さくならない事から、疲労特性
を向上させることができる。Further, using the above three structures, the initial wire diameter was changed so as to have the same strength, heat treatment was performed, and wire drawing was performed to 0.3 mmφ. Each of the tensile strengths is adjusted to be approximately 3600 MPa. As shown in FIG. 2, the pseudo-pearlite structure exhibits the most excellent fatigue characteristics. This is because in the case of the pseudo-pearlite structure, the cementite is distributed in a granular form, so that crack propagation at the interface between ferrite and cementite is less likely to occur in the fatigue fracture process, and the work hardening rate in the wire drawing is also the bainite structure. Since it does not become so small, fatigue characteristics can be improved.
【００３０】[0030]
【実施例】以下に実施例に基づいて本発明の効果を記
す。EXAMPLES The effects of the present invention will be described below based on examples.
【００３１】[0031]
【表１】 [Table 1]
【００３２】[0032]
【表２】 [Table 2]
【００３３】表１に本発明ワイヤと比較ワイヤの化学成
分を示す。表１に示す成分の線材を伸線加工により表２
に示す線径のワイヤとし、９５０℃に８０ｓのγ化処理
を行った後、４８０℃から６００℃の温度範囲でパテン
ティング処理を行い、表２に示す組織のワイヤとした。
その後さらに伸線加工を行い、０．３ｍｍφのフィラメ
ントとした。Table 1 shows the chemical composition of the wire of the present invention and the comparative wire. The wire rods with the components shown in Table 1 were subjected to wire drawing to obtain Table 2
The wire having the wire diameter shown in Table 2 was subjected to γ-conversion treatment at 950 ° C. for 80 s, and then subjected to patenting treatment in the temperature range of 480 ° C. to 600 ° C.
After that, wire drawing was further performed to obtain a filament of 0.3 mmφ.
【００３４】表２に示されるように、いづれのワイヤも
引張強さがほぼ３６００ＭＰａとなるように調整されて
いる。As shown in Table 2, each of the wires is adjusted so that the tensile strength will be approximately 3600 MPa.
【００３５】本発明鋼１から４５は本発明に従って製造
されているので、比較鋼に比べ優れた疲労強度を有す
る。Since the invention steels 1 to 45 are manufactured according to the present invention, they have superior fatigue strength to the comparative steels.
【００３６】比較鋼４６は組織をベイナイト組織として
いるため疲労限強度が本発明鋼と比べて劣っている。比
較鋼４７は組織をパーライト組織としているため疲労限
強度が本発明鋼と比べて劣っている。比較鋼４８〜５０
は、擬似パーライト組織の割合が８０％未満となってい
るため疲労限応力が劣っている。The comparative steel 46, which has a bainite structure, is inferior in fatigue limit strength to the steel of the present invention. Since the comparative steel 47 has a pearlite structure, its fatigue limit strength is inferior to that of the steel of the present invention. Comparative steel 48-50
Indicates that the fatigue limit stress is inferior because the proportion of the pseudo-pearlite structure is less than 80%.
【００３７】[0037]
【発明の効果】本発明の高強度高延性鋼線は高い引張強
さと優れた疲労特性を示すワイヤを得るこができる。。The high-strength and high-ductility steel wire of the present invention makes it possible to obtain a wire exhibiting high tensile strength and excellent fatigue properties. .
【図１】は、加工硬化特性の比較図。FIG. 1 is a comparative diagram of work hardening characteristics.
【図２】は、材料組織と疲労限強度の関係を示す図。FIG. 2 is a diagram showing a relationship between a material structure and a fatigue limit strength.
Claims (5)
によって得られる擬似パーライト組織が８０％以上とな
る鋼材を伸線加工にする事によって得られる引張強さが
３６００ＭＰａ以上の強度を有する疲労特性の優れた高
強度鋼線。1. A steel having a C content of 0.6% or more has a tensile strength of 3600 MPa or more obtained by wire drawing of a steel material having a pseudo-pearlite structure of 80% or more obtained by heat treatment. High strength steel wire with excellent fatigue properties.
の優れた高強度鋼線。2. Steel in which the weight percentage of steel is C: 0.6% or more and 1.5% or less Si: 0.1% or more and 2.0% or less Mn: 0.1% or more and 2.0% or less A high-strength steel wire having excellent fatigue characteristics according to claim 1.
する請求２の疲労特性の優れた高強度鋼線。 Ｃｒ：０．１％以上２．０％以下 Ｎｉ：０．１％以上２．０％以下 Ｃｕ：０．１％以上２．０％以下 Ｍｏ：０．１％以上２．０％以下 Ｃｏ：０．０１％以上２．０％以下3. A high-strength steel wire with excellent fatigue characteristics according to claim 2, characterized in that one or more of the following components are added. Cr: 0.1% or more and 2.0% or less Ni: 0.1% or more and 2.0% or less Cu: 0.1% or more and 2.0% or less Mo: 0.1% or more and 2.0% or less Co: 0.01% or more and 2.0% or less
とする請求項２または３の疲労特性の優れた高強度鋼
線。 Ｔｉ：０．００５％以上０．０３％以下 Ｎｂ：０．００５％以上０．０３％以下 Ｖ ：０．００５％以上０．０３％以下 Ａｌ：０．００５％以上０．０３％以下 Ｂ ：０．０００１％以上０．００３％以下4. A high-strength steel wire excellent in fatigue properties according to claim 2, wherein one or more of the following components are added. Ti: 0.005% or more and 0.03% or less Nb: 0.005% or more and 0.03% or less V: 0.005% or more and 0.03% or less Al: 0.005% or more and 0.03% or less B: 0.0001% or more and 0.003% or less
労特性の優れた高強度鋼線。5. A high-strength steel wire having excellent fatigue characteristics according to claim 2, 3 or 4, wherein P: 0.02% or less and S: 0.02% or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9731795A JPH08295932A (en) | 1995-04-21 | 1995-04-21 | High strength steel wire excellent in fatigue characteristic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9731795A JPH08295932A (en) | 1995-04-21 | 1995-04-21 | High strength steel wire excellent in fatigue characteristic |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH08295932A true JPH08295932A (en) | 1996-11-12 |
Family
ID=14189115
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9731795A Pending JPH08295932A (en) | 1995-04-21 | 1995-04-21 | High strength steel wire excellent in fatigue characteristic |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH08295932A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2006088019A1 (en) * | 2005-02-16 | 2006-08-24 | Nippon Steel Corporation | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
| JP2006225701A (en) * | 2005-02-16 | 2006-08-31 | Nippon Steel Corp | Steel wire rod excellent in cold-forgeability after spheroidizing-treatment and producing method therefor |
| JP2006312771A (en) * | 2005-05-09 | 2006-11-16 | Nippon Steel Corp | Wire rod superior in cold forgeability and manufacturing method therefor |
| JP2017186632A (en) * | 2016-04-08 | 2017-10-12 | 新日鐵住金株式会社 | Steel wire and producing method for steel wire thereof |
| CN115852254A (en) * | 2022-12-03 | 2023-03-28 | 江苏新核合金科技有限公司 | Heat-resistant steel wire and preparation process thereof |
| WO2023162615A1 (en) * | 2022-02-22 | 2023-08-31 | 住友電気工業株式会社 | Steel wire |
-
1995
- 1995-04-21 JP JP9731795A patent/JPH08295932A/en active Pending
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2006088019A1 (en) * | 2005-02-16 | 2006-08-24 | Nippon Steel Corporation | Hot rolled wire material excellent in cold forging property after spheroidizing treatment, spheroidizing-annealed steel wire having excellent cold forging property, and method for production thereof |
| JP2006225701A (en) * | 2005-02-16 | 2006-08-31 | Nippon Steel Corp | Steel wire rod excellent in cold-forgeability after spheroidizing-treatment and producing method therefor |
| JP4669300B2 (en) * | 2005-02-16 | 2011-04-13 | 新日本製鐵株式会社 | Steel wire rod excellent in cold forgeability after spheroidizing treatment and method for producing the same |
| JP2006312771A (en) * | 2005-05-09 | 2006-11-16 | Nippon Steel Corp | Wire rod superior in cold forgeability and manufacturing method therefor |
| JP2017186632A (en) * | 2016-04-08 | 2017-10-12 | 新日鐵住金株式会社 | Steel wire and producing method for steel wire thereof |
| WO2023162615A1 (en) * | 2022-02-22 | 2023-08-31 | 住友電気工業株式会社 | Steel wire |
| CN115852254A (en) * | 2022-12-03 | 2023-03-28 | 江苏新核合金科技有限公司 | Heat-resistant steel wire and preparation process thereof |
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