JP3298688B2 - Manufacturing method of high strength deformed steel wire - Google Patents
Manufacturing method of high strength deformed steel wireInfo
- Publication number
- JP3298688B2 JP3298688B2 JP02150493A JP2150493A JP3298688B2 JP 3298688 B2 JP3298688 B2 JP 3298688B2 JP 02150493 A JP02150493 A JP 02150493A JP 2150493 A JP2150493 A JP 2150493A JP 3298688 B2 JP3298688 B2 JP 3298688B2
- Authority
- JP
- Japan
- Prior art keywords
- wire
- steel wire
- strength
- deformed steel
- molten salt
- 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 - Lifetime
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- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Metal Extraction Processes (AREA)
- Heat Treatment Of Steel (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、引張強さ２００kgf/mm
2 以上の高強度鋼線の製造方法に関し、さらに詳しく
は、高圧流体輸送用フレキシブルパイプ等の製造に供さ
れる高強度異形鋼線の製造方法に関するものである。The present invention relates to a tensile strength of 200 kgf / mm.
The present invention relates to a method for producing two or more high-strength steel wires, and more particularly, to a method for producing a high-strength deformed steel wire used for producing a flexible pipe for high-pressure fluid transport or the like.
【０００２】[0002]
【従来の技術】従来、原油や天然ガス等の高圧流体輸送
用フレキシブルパイプの鎧装線等は、Ｃ０．７％以下の
高炭素鋼線材を伸線後、異形引抜き、ローラーダイス加
工、圧延等の異形加工により所定の断面形状の異形鋼線
（平圧線や溝形線）とし、さらに、球状化焼鈍を施した
のち使用に供せられていた。例えば、特開平１−２７９
７１０号公報には「耐水素誘起割れ特性に優れた高強度
鋼線の製造法」として、０．４０〜０．７０％のＣを含
む高炭素鋼線材をパテンティング後、断面減少率２５〜
７５％の冷間加工を行ったのち、５００〜７００℃で球
状化焼鈍する方法が開示されている。しかし、これら従
来法は、サワー環境（Ｓｏｕｒ ｅｎｖｉｒｏｎｍｅｎ
ｔｓ，湿潤硫化水素環境）用鋼線を対象としているた
め、鋼線強度は８０kgf/mm2 以下と低い。2. Description of the Related Art Conventionally, armored wires of flexible pipes for transporting high-pressure fluids such as crude oil and natural gas are formed by drawing high-carbon steel wires having a carbon content of 0.7% or less, drawing irregular shapes, roller dies, rolling, and the like. Was formed into a deformed steel wire (flat pressure wire or grooved wire) having a predetermined cross-sectional shape, and was subjected to spheroidizing annealing before use. For example, JP-A-1-279
Japanese Patent Publication No. 710 discloses a method for producing a high-strength steel wire excellent in resistance to hydrogen-induced cracking, in which a high-carbon steel wire containing 0.40 to 0.70% of C is patented, and the cross-sectional reduction rate is 25 to 25%.
A method of performing spheroidizing annealing at 500 to 700 ° C. after performing 75% cold working is disclosed. However, in these conventional methods, a sour environment (Sour environment) is used.
(ts, wet hydrogen sulfide environment), the steel wire strength is as low as 80 kgf / mm 2 or less.
【０００３】一方、最近の大陸棚開発の進展に伴ない、
より高強度の鎧装線が必要とされるようになった。すな
わち、深海油田や深海ガス田から原油や天然ガスを採掘
する場合には、採掘した原油や天然ガスを海面まで引き
上げるための輸送管（フレキシブルパイプ）が長大なも
のになるため、鎧装線である異形線には高強度であるこ
とが要求されるようになった。この場合の環境は通常の
環境である。On the other hand, with the recent progress of continental shelf development,
Higher strength armor lines were required. In other words, when extracting crude oil or natural gas from deep sea oil fields or deep sea gas fields, the length of the transport pipe (flexible pipe) used to lift the extracted crude oil or natural gas to the sea surface is large. Certain deformed wires have been required to have high strength. The environment in this case is a normal environment.
【０００４】高炭素鋼線材の強度を高める手段として、
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割れが
発生しやすくなり、高減面率の伸線加工は不可能とな
る。As means for increasing the strength of high carbon steel wire rods,
Increasing the C content is the most industrially desirable method because it is inexpensive and has a high effect. However, in the hypereutectoid region, that is, the region where C is usually more than 0.9%,
During patenting, brittle proeutectoid cementite is formed in a network along the austenite grain boundaries. For this reason, at the time of wire drawing, grain boundary cracks are likely to occur along the proeutectoid cementite, and wire drawing with a high reduction in area becomes impossible.
【０００５】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。例えば、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℃の温度領域に急速加熱して粒状セメン
タイトを析出せしめ、目標加熱温度に到達後直ちに５３
５〜６６０℃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優
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。Conventionally, as a method for improving the drawability of a hypereutectoid steel, a method of suppressing the formation of proeutectoid cementite by heat treatment or addition of an alloy element, or a method of elongation by devising a drawing method, has been proposed. Methods have been developed to prevent ductility degradation due to cementite. For example, Japanese Patent Publication No. 56-8893 discloses a method of changing the structure to a pearlite structure in which granular cementite is dispersed by heat treatment. This is austenitized hypereutectoid steel wire, after oil quenching to martensite structure,
Rapid heating to a temperature range of 770 to 930 ° C. to precipitate granular cementite, and immediately after reaching the target heating temperature,
This is a method of performing a patenting process at a temperature of 5 to 660 ° C. This method is excellent as a method of raising the drawing limit, but the cementite that has been granulated has a small contribution to strengthening unlike cementite developed in a layered form (the strength after patenting is low, Work hardening is small)
Therefore, the effect of increasing the C content cannot be utilized.
【０００６】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としては、本発明者らが特
開平２−２６３９５１号公報あるいは特開平２−２５８
９５３号公報で提案しているように、０．１〜０．３％
のＣｒを添加する方法があるが、小量のセメンタイトの
生成を防ぐことはできない。また、特開昭６３−１８６
８５２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５〜５０
ppm 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
方法が適用できるのはＣ含有率が１％以下に限られ、さ
らに、これらの微量元素の添加のみならず、微細な酸化
物硫化物を出現させるために、Ｓ，Ｏ，Ａｌの含有率も
制御せねばならず、製造管理はきわめて複雑なものとな
る。As a method of suppressing the generation of proeutectoid cementite by utilizing the effect of adding an alloy element, the inventors of the present invention disclosed in JP-A-2-263951 or JP-A-2-258.
No. 953, as proposed.
However, the formation of a small amount of cementite cannot be prevented. Also, JP-A-63-186
No. 852 discloses that 5 to 50 ppm of REM and Ca,
One or more of Mg, Ba, and Sr in total of 5 to 50
A method of adding ppm is disclosed. All of these elements are elements that simultaneously generate sulfide and oxide. REM, Ca, Mg,
This is a method in which pearlite transformation is promoted using fine sulfide oxides containing Ba and Sr as nuclei to suppress the formation of martensite and proeutectoid cementite. However, this method can be applied only when the C content is 1% or less. Further, not only the addition of these trace elements but also the appearance of fine oxide sulfides, the S, O, Al The content must also be controlled and the production control becomes very complex.
【０００７】[0007]
【発明が解決しようとする課題】このような現状から本
発明は、過共析鋼のパテンティングにおいて、粒界初析
セメンタイトが生成することを完全に阻止すると同時
に、パテンティング後の鋼線材に、従来法では得られな
かった高強度と高延性を付与することのできるフレキシ
ブルパイプ用高強度異形鋼線の製造方法を提供するもの
である。Under such circumstances, the present invention completely prevents the formation of grain boundary pro-eutectoid cementite in the patenting of hypereutectoid steel, and at the same time, the patented steel wire rod Another object of the present invention is to provide a method for producing a high-strength deformed steel wire for a flexible pipe, which can provide high strength and high ductility that cannot be obtained by the conventional method.
【０００８】[0008]
【課題を解決するための手段】本発明は、Ｃ：０．９０
〜１．２５％、Ｓｉ：０．１５〜１．５％、Ｍｎ：０．
３〜１．０％、Ｃｒ：０．１〜１．０％、残余をＦｅお
よび不可避的不純物からなる鋼を、線材圧延後、直ちに
４５０〜６００℃に保持された溶融塩中に焼き入れ、該
溶融塩中で保持しパーライト変態を完了させたのち冷却
し、総減面率１０〜７５％の伸線加工を行ったのち、総
減面率２０〜８０％の異形加工をすることを特徴とする
高強度異形鋼線の製造方法である。According to the present invention, C is 0.90.
To 1.25%, Si: 0.15 to 1.5%, Mn: 0.
3 to 1.0%, Cr: 0.1 to 1.0%, the balance consisting of Fe and inevitable impurities is quenched immediately after the wire rod rolling in a molten salt maintained at 450 to 600 ° C, After holding in the molten salt to complete the pearlite transformation, cooling, performing wire drawing with a total area reduction of 10 to 75%, and then performing deforming with a total area reduction of 20 to 80%. This is a method for producing a high-strength deformed steel wire.
【０００９】以下に、本発明を詳細に説明する。本発明
者らは、過共析鋼線材のパテンティング時に初析セメン
タイトが生成するのを防止し、かつ、パテンティング後
の線材に、従来法では得られなかった高強度と高延性を
付与すべく、多くの実験を行った。その結果、以下に示
すように、線材圧延直後、赤熱線材を４５０〜６００℃
に保持された溶融塩中に焼き入れ、溶融塩中でパーライ
ト変態を完了させることにより、目標特性を具えた高強
度高延性線材が製造できるという新たな知見を得た。Hereinafter, the present invention will be described in detail. The present inventors prevent the formation of proeutectoid cementite during patenting of a hypereutectoid steel wire, and impart high strength and high ductility, which cannot be obtained by the conventional method, to the wire after patenting. To do so, we conducted many experiments. As a result, as shown below, immediately after the rolling of the wire rod, the glowing wire was heated to 450 to 600 ° C.
Quenched in molten salt held in
By completing the door transformation, high strength and high ductility wire rods equipped with target characteristic to obtain a new finding that can be produced.
【００１０】初析セメンタイトの生成を阻止するために
は、オーステナイト域からの冷却速度を十分高くとる必
要がある。通常のパテンティングのように、一旦冷却さ
れた線材を再加熱によりオーステナイト化した場合に
は、線材表面は厚いスケールに覆われている。このた
め、初析セメンタイトの生成を阻止するに十分な冷却速
度を得るには特別な工夫を要する。In order to prevent the formation of proeutectoid cementite, it is necessary to increase the cooling rate from the austenite region sufficiently. In the case where the once cooled wire is austenitized by reheating as in normal patenting, the surface of the wire is covered with a thick scale. For this reason, special measures are required to obtain a cooling rate sufficient to prevent the formation of proeutectoid cementite.
【００１１】これに対して、熱間圧延後の線材表面はき
わめて薄いスケールで均一に覆われており、地鉄との密
着も良好である。従って、再加熱パテンティングの場合
に比べ、安定した高い冷却速度を得ることが可能であ
る。溶融塩温度が４５０℃未満では、線材表層にベイナ
イトが生成するうえ、中心偏析部にマルテンサイトが発
生し、異形加工性が低下する。一方、６００℃を超える
と、パーライトの層状構造が崩れ、このため、伸線加工
性および異形加工性が低下する。なお、溶融塩槽内温度
は均一である必要はない。熱間圧延線材が進入する側の
溶融塩温度は低く設定して必要な冷却速度を得、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、溶融塩槽は複数の冷却帯に分割されたものが
望ましい。On the other hand, the surface of the wire after hot rolling is uniformly covered with an extremely thin scale, and has good adhesion to the ground iron. Therefore, a stable and high cooling rate can be obtained as compared with the case of reheating patenting. If the molten salt temperature is lower than 450 ° C., bainite is generated in the surface layer of the wire, and martensite is generated in the central segregation portion, resulting in reduced deformability. On the other hand, when the temperature exceeds 600 ° C., the layer structure of pearlite collapses, and therefore, wire drawing workability and deformability are reduced. The temperature in the molten salt bath does not need to be uniform. The molten salt temperature on the side where the hot-rolled wire enters should be set low to obtain the required cooling rate, and the temperature of the other parts should be maintained at a temperature at which fine layered pearlite can be obtained according to the steel composition. . For such a purpose, it is desirable that the molten salt tank is divided into a plurality of cooling zones.
【００１２】次に、本発明の成分限定理由について説明
する。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
を上げるに伴ない、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。従って、伸線加工および
異形加工により高強度鋼線を得るためには、Ｃ含有率は
高い方が有利であり、本発明では、０．９％以上とす
る。一方、Ｃ含有率が１．２５％を超えた場合、初析セ
メンタイトの発生を防止できなくなるため、Ｃ含有率の
上限は１．２５％とする。Next, the reasons for limiting the components of the present invention will be described. C is an effective and economical element for increasing the strength, and is one of the most important elements of the present invention. As the C content is increased, the strength after patenting and the amount of work hardening during drawing are increased. Therefore, in order to obtain a high-strength steel wire by drawing and deforming, a higher C content is advantageous, and in the present invention, it is set to 0.9% or more. On the other hand, if the C content exceeds 1.25%, the generation of proeutectoid cementite cannot be prevented, so the upper limit of the C content is 1.25%.
【００１３】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、
顕著な固溶強化作用を示す。しかし、１．５％を超える
と、鋼線の延性が低下するため、１．５％を上限とす
る。[0013] Si is added as a deoxidizing agent in an amount of 0.15% or more. On the other hand, Si dissolves in ferrite as an alloy element,
Shows remarkable solid solution strengthening action. However, if it exceeds 1.5%, the ductility of the steel wire is reduced, so the upper limit is 1.5%.
【００１４】Ｍｎも脱酸剤として０．３％以上添加す
る。また、Ｍｎは焼き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、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、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. Further, since Mn has a large effect of improving hardenability, when the wire diameter is large, by increasing the Mn content,
It is possible to increase the uniformity in the cross section, which is effective for improving the ductility of the steel wire. However, when the content exceeds 1.0%, martensite is generated in the central segregation portion, and the workability is deteriorated. Therefore, the upper limit is 1.0%.
【００１５】Ｃｒは、パーライトのラメラー間隔を低減
し、線材の強度と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、設備の大型化、あるいは、生産能率の低下をきたす
ため、１．０％を上限とする。[0015] Cr is added in an amount of 0.1% or more to reduce the lamella spacing of pearlite and improve the strength and workability of the wire. If less than 0.1%, the effect is not enough,
On the other hand, if it exceeds 1.0%, the time required for the transformation becomes longer, which leads to an increase in the size of the equipment or a decrease in the production efficiency. Therefore, the upper limit is made 1.0%.
【００１６】異形線に加工するのに先立って伸線加工を
行う。伸線加工の総減面率が１０％未満では異形加工後
の鋼線の伸びが不足する。一方、７５％を超えると異形
加工の際割れが発生する。従って、伸線加工の総減面率
は１０〜７５％とする。Prior to forming into a deformed wire, wire drawing is performed. If the total area reduction rate of the wire drawing is less than 10%, the elongation of the steel wire after the deforming is insufficient. On the other hand, if it exceeds 75%, cracks occur during deforming. Therefore, the total area reduction rate of the wire drawing is set to 10 to 75%.
【００１７】異形加工は、圧延、タークスヘッド加工、
ローラーダイス加工等により行う。異形加工時の総減面
率が２０％未満では目的とする形状が得られない。一
方、８０％を超えると、伸びが著しく劣化する。このた
め、異形加工時の総減面率は２０〜８０％とする。The deforming includes rolling, turks head processing,
This is performed by roller dies or the like. If the total area reduction rate during deforming is less than 20%, the desired shape cannot be obtained. On the other hand, if it exceeds 80%, the elongation is significantly deteriorated. For this reason, the total area reduction rate at the time of deforming is set to 20 to 80%.
【００１８】[0018]
【実施例】直径１１〜１２mmの線材を熱間圧延後、溶融
塩槽中で連続的にパテンティングを行った。次に、線材
を酸洗、潤滑処理したのち伸線し、その後、圧延により
異形鋼線を製造した。表１に、線材および鋼線の特性を
示す。Ｃ含有率が０．８６％（Ａ−１）では、目標強度
が得られず、一方、１．２９％（Ａ−５）では、初析セ
メンタイトが生成し、伸線できなかった。Ｓｉ含有率が
１．６５％のＢ−５は異形加工後の延性が著しく低い。
また、Ｃｒが下限以下のＡ−３は鋼線強度が目標以下と
なった。一方、Ｃｒが１．１０％と上限を超えたＢ−３
は線材にマルテンサイトが生成し伸線できなかった。同
様に、Ｍｎが上限を超えたＢ−４でも線材の偏析部にマ
ルテンサイトが生成し伸線時に断線した。Ｃ−１からＣ
−４は伸線減面率および異形加工減面率の影響を示した
ものである。Ｄ−１は従来法で製造されたもので、Ｃ：
０．８２％のピアノ線材（ＪＩＳ Ｇ３５０２）を圧延
後、溶融塩冷却を行ったものである。EXAMPLE A wire rod having a diameter of 11 to 12 mm was hot-rolled and then continuously patented in a molten salt bath. Next, the wire was pickled, lubricated, drawn, and then rolled to produce a deformed steel wire. Table 1 shows the properties of the wire and the steel wire. When the C content was 0.86% (A-1), the target strength could not be obtained. On the other hand, when the C content was 1.29% (A-5), proeutectoid cementite was formed and could not be drawn. B-5 having an Si content of 1.65% has remarkably low ductility after deforming.
In addition, the steel wire strength of A-3 in which Cr was lower than the lower limit was lower than the target. On the other hand, B-3 in which Cr exceeded the upper limit of 1.10%.
In the case of wire, martensite was formed in the wire and could not be drawn. Similarly, in B-4 in which Mn exceeded the upper limit, martensite was formed in the segregated portion of the wire, and the wire was broken during wire drawing. C-1 to C
-4 indicates the influence of the wire drawing reduction rate and the deforming processing reduction rate. D-1 was manufactured by a conventional method, and C:
After rolling 0.82% piano wire (JIS G3502), the molten salt was cooled.
【００１９】表１が示すように、本発明法により製造さ
れた異形鋼線は従来法に比較して強度が高く、それにも
かかわらず、延性の低下がほとんど認められない。すな
わち、本発明法によれば、従来法では不可能であった２
００kgf/mm2 級異形鋼線の製造が可能である。As shown in Table 1, the deformed steel wire produced by the method of the present invention has a higher strength than that of the conventional method, and in spite of this, almost no decrease in ductility is observed. That is, according to the method of the present invention, 2
It is possible to manufacture 00kgf / mm class 2 deformed steel wire.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【発明の効果】以上に説明したように、本発明法によれ
ば、引張強さ２００kgf/mm2 以上の高強度異形鋼線を製
造することが可能となる。As described above, according to the method of the present invention, a high-strength deformed steel wire having a tensile strength of 200 kgf / mm 2 or more can be manufactured.
フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 8/00 - 8/10 C21D 9/52 C22C 38/00 - 38/60 Continuation of the front page (58) Field surveyed (Int. Cl. 7 , DB name) C21D 8/00-8/10 C21D 9/52 C22C 38/00-38/60
Claims (1)
延後、直ちに４５０〜６００℃に保持された溶融塩中に
焼き入れ、該溶融塩中で保持しパーライト変態を完了さ
せたのち冷却し、総減面率１０〜７５％の伸線加工を行
ったのち総減面率２０〜８０％の異形加工をすることを
特徴とする高強度異形鋼線の製造方法。1. C: 0.90 to 1.25% by weight, Si: 0.15 to 1.5%, Mn: 0.3 to 1.0%, Cr: 0.1 to 1.0 by weight ratio. %, The balance consisting of Fe and inevitable impurities is quenched immediately after the wire rod rolling in a molten salt kept at 450 to 600 ° C., kept in the molten salt to complete the pearlite transformation, and then cooled. A method for producing a high-strength deformed steel wire, comprising performing wire drawing with a total area reduction of 10 to 75% and then deforming with a total area reduction of 20 to 80%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02150493A JP3298688B2 (en) | 1993-02-09 | 1993-02-09 | Manufacturing method of high strength deformed steel wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02150493A JP3298688B2 (en) | 1993-02-09 | 1993-02-09 | Manufacturing method of high strength deformed steel wire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06235024A JPH06235024A (en) | 1994-08-23 |
| JP3298688B2 true JP3298688B2 (en) | 2002-07-02 |
Family
ID=12056805
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP02150493A Expired - Lifetime JP3298688B2 (en) | 1993-02-09 | 1993-02-09 | Manufacturing method of high strength deformed steel wire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3298688B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014178303A1 (en) | 2013-04-30 | 2014-11-06 | 新日鐵住金株式会社 | Flat steel wire |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US9274298B2 (en) | 2012-10-04 | 2016-03-01 | Nippon Steel & Sumitomo Metal Corporation | Deformed steel wire for protection tube of submarine cable, method for manufacturing same, and pressure-resistant layer |
| EP3415654A4 (en) * | 2016-03-07 | 2019-08-14 | Nippon Steel Corporation | High-strength flat steel wire exhibiting superior hydrogen-induced crack resistance |
| CN106636581A (en) * | 2016-11-30 | 2017-05-10 | 青岛特殊钢铁有限公司 | Salt bath treatment method and equipment for wire rod for 1960 MPa and above bridge cable zinc-coated steel wire |
-
1993
- 1993-02-09 JP JP02150493A patent/JP3298688B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014178303A1 (en) | 2013-04-30 | 2014-11-06 | 新日鐵住金株式会社 | Flat steel wire |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH06235024A (en) | 1994-08-23 |
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