JP3370368B2 - Manufacturing method of high strength steel wire for suspended structure - Google Patents
Manufacturing method of high strength steel wire for suspended structureInfo
- Publication number
- JP3370368B2 JP3370368B2 JP02150393A JP2150393A JP3370368B2 JP 3370368 B2 JP3370368 B2 JP 3370368B2 JP 02150393 A JP02150393 A JP 02150393A JP 2150393 A JP2150393 A JP 2150393A JP 3370368 B2 JP3370368 B2 JP 3370368B2
- Authority
- JP
- Japan
- Prior art keywords
- steel wire
- plating
- wire
- strength
- corrosion resistance
- 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.)
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- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、吊橋、斜張橋等の吊構
造に使用される耐食性、直線性、ならびに耐クリープ性
に優れた引張強さ２００kgf/mm2 以上の高強度鋼線の製
造方法に関する。TECHNICAL FIELD The present invention relates to a high-strength steel wire having a tensile strength of 200 kgf / mm 2 or more excellent in corrosion resistance, linearity, and creep resistance, which is used for a suspension structure such as a suspension bridge and a cable-stayed bridge. It relates to a manufacturing method.
【０００２】[0002]
【従来の技術】吊橋や斜張橋等の吊構造に使用される鋼
線は、通常、ＪＩＳ Ｇ３５０２に規定されるピアノ線
材にパテンティングを行なった後、伸線し、その後、溶
融Ｚｎめっきを施す方法で製造されている。しかし、近
年、橋梁の長大化傾向が進展するのに伴ない、ケーブル
（パラレルワイヤストランド。以下、ＰＷＳと称する）
の軽量化、すなわち、使用される鋼線（ＰＷＳワイヤ）
の高強度化が要望されるようになった。2. Description of the Related Art A steel wire used in a suspension structure such as a suspension bridge or a cable-stayed bridge is usually formed by patenting a piano wire rod specified in JIS G3502, drawing it, and then hot-dip Zn plating. It is manufactured by the application method. However, in recent years, along with the tendency of lengthening bridges, cables (parallel wire strands, hereinafter referred to as PWS)
Weight reduction, ie used steel wire (PWS wire)
There has been a demand for higher strength.
【０００３】これに対処するため、従来、特開昭６３−
４０１６号公報が開示されている。これは、限定成分の
線材を、ローラーダイス引抜きまたは冷間圧延を行なっ
た後、断面減少率４０％以下の孔ダイス伸線を行なって
超高張力鋼線を得る方法である。しかし、この方法で
は、寸法精度の厳しい場合には適用が困難であり、ま
た、Ｚｎめっき厚みの不均一が生じるため耐食性が劣化
する。In order to deal with this, it has hitherto been disclosed in Japanese Patent Laid-Open No. 63-
Japanese Patent No. 4016 is disclosed. This is a method in which a wire rod having a limited component is subjected to roller die drawing or cold rolling, and then hole die wire drawing with a cross-section reduction rate of 40% or less is performed to obtain an ultra-high tensile steel wire. However, this method is difficult to apply when the dimensional accuracy is severe, and the Zn plating thickness becomes nonuniform, resulting in deterioration of corrosion resistance.
【０００４】一方、鋼線の耐食性を向上させるために、
従来のＺｎめっきに代り各種のＺｎ−Ａｌ合金めっきが
開発されている。たとえば、特公昭５５−２６７０２号
公報にはＺｎ−Ａｌ、特公昭５４−３３２２３号公報に
はＺｎ−Ａｌ−Ｍｇ、特表昭５７−５００４７５号公報
にはＺｎ−Ａｌ−ミッシュメタル、特開昭５６−１１２
４５２号公報にはＺｎ−Ａｌ−Ｎａ等が公表されてい
る。これらは、いずれも従来の溶融Ｚｎめっき法と同
様、溶融状態（約４５０℃）の合金めっき浴中に鋼線を
浸漬することによりめっきする方法である。しかし、こ
れらの方法では、めっき時に伸線加工により強化された
鋼線は軟化し、目標強度が得られない。On the other hand, in order to improve the corrosion resistance of the steel wire,
Various Zn-Al alloy platings have been developed in place of conventional Zn plating. For example, Japanese Patent Publication No. 55-26702, Zn-Al, Japanese Patent Publication No. 54-33223, Zn-Al-Mg, Japanese Patent Publication No. 57-500475, Zn-Al-Misch Metal, JP-A No. 56-112
No. 452 discloses Zn-Al-Na and the like. These are all methods of plating by dipping a steel wire in a molten alloy plating bath (about 450 ° C.) as in the conventional hot-dip Zn plating method. However, with these methods, the steel wire reinforced by the wire drawing process during plating softens, and the target strength cannot be obtained.
【０００５】ケーブル施工上、ＰＷＳワイヤには高い直
線性が要求されているにもかかわらず、従来、溶融めっ
き後に矯正加工を施すことはできなかった。それは、矯
正加工により鋼線の耐クリープ性が劣化し、架設後のケ
ーブルの常温クリープが増大するためである。これを防
止する手段としては、矯正後のめっき鋼線を２５０℃以
上でブルーイングすることが考えられる。しかし、Ｚｎ
めっき鋼線を２００℃以上の高温にさらすことは、脆い
Ｚｎ−Ｆｅ合金層を発達させ、その結果、めっき密着性
および耐食性が著しく劣化するため、この方法は実際に
は行なわれていない。Although a PWS wire is required to have a high linearity in cable construction, it has not been possible to carry out straightening processing after hot dipping in the past. This is because the straightening process deteriorates the creep resistance of the steel wire and increases the room temperature creep of the cable after installation. As a means for preventing this, it is considered that the plated steel wire after straightening is blued at 250 ° C. or higher. However, Zn
This method has not been practiced since exposing the plated steel wire to a high temperature of 200 ° C. or higher causes a brittle Zn—Fe alloy layer to develop, resulting in a significant deterioration in plating adhesion and corrosion resistance.
【０００６】[0006]
【発明が解決しようとする課題】以上述べたように、従
来の技術では、耐食性、直線性、ならびに耐クリープ性
に優れた高強度溶融めっき鋼線を製造することは不可能
であった。本発明の目的は、上記従来法の問題点を解決
することにより、従来より高強度のＰＷＳワイヤの製造
方法を提供することにある。As described above, it has been impossible to manufacture a high-strength hot-dip galvanized steel wire excellent in corrosion resistance, linearity, and creep resistance by the conventional techniques. It is an object of the present invention to provide a method of manufacturing a PWS wire having a higher strength than conventional methods by solving the problems of the conventional methods.
【０００７】[0007]
【課題を解決するための手段】本発明は、重量比でＣ：
０．７５〜１．０％、Ｓｉ：０．１５〜１．３％、Ｍ
ｎ：０．３〜１．０％、必要に応じて、Ｃｒ：０．１〜
１．０％、Ｖ：０．０２〜０．３０％の１種ないし２
種、さらに、Ａｌ，Ｔｉの１種ないし２種をそれぞれ
０．１％以下含有し、残余をＦｅおよび不可避的不純物
からなる鋼線を、重量比でＡｌ：２〜１２％、Ｓｉ：
０．０１〜０．０７％含有する合金浴を用いて溶融めっ
きしたのち矯正し、その後、２５０〜３７０℃でブルー
イングすることを特徴とする吊構造用高強度鋼線の製造
方法である。The present invention provides a weight ratio of C:
0.75-1.0%, Si: 0.15-1.3%, M
n: 0.3 to 1.0%, if necessary, Cr: 0.1 to
1.0%, V: 0.02 to 0.30% of 1 to 2
Steel wire containing 0.1% or less of each of Al, Ti and 1 or 2 of Al and Ti, and the balance of Fe and unavoidable impurities, Al: 2 to 12% by weight, Si:
A method for producing a high-strength steel wire for a hanging structure, comprising hot-dip-plating using an alloy bath containing 0.01 to 0.07 %, straightening, and then bluing at 250 to 370 ° C.
【０００８】以下に、本発明を詳細に説明する。はじめ
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、０．７５％以上とする。一方、Ｃ含有率が１．０％
を超えた場合、初析セメンタイトの発生防止に特別な配
慮を要するため、Ｃ含有率の上限は１．０％とする。The present invention will be described in detail below. First, the reasons for limiting the components of the present invention will be described. C is an effective and economical element for increasing strength and is one of the most important elements of the present invention. As the C content increases, the strength after patenting and the amount of work hardening during wire drawing increase. Therefore, in order to obtain a high-strength steel wire by wire drawing, a higher C content is advantageous, and in the present invention, it is 0.75% or more. On the other hand, the C content is 1.0%
If it exceeds 1.0, special consideration is required to prevent the occurrence of pro-eutectoid cementite, so the upper limit of the C content is 1.0%.
【０００９】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。また、フェライト中の
Ｓｉは伸線後の溶融亜鉛めっきやブルーイング工程にお
ける鋼線の強度低下を低減させる効果を有するため、高
強度鋼線の製造には不可欠な元素である。しかし、１．
３％を超えると、めっき後の矯正工程において鋼線の延
性が低下するため、１．３％を上限とする。Si is added as a deoxidizer in an amount of 0.15% or more. On the other hand, Si dissolves in ferrite as an alloying element and exhibits a remarkable solid solution strengthening action. Further, Si in the ferrite has an effect of reducing the strength reduction of the steel wire in the hot dip galvanizing after the wire drawing and the bluing process, and is an essential element for the production of the high strength steel wire. However, 1.
If it exceeds 3%, the ductility of the steel wire deteriorates in the straightening step after plating, so the upper limit is 1.3%.
【００１０】Ｍｎも脱酸剤として０．３％以上添加す
る。また、Ｍｎは焼入性向上効果が大きいため、線径が
大きい場合には、Ｍｎ含有率を上げることにより、断面
内の均一性を高めることが可能であり、伸線後の鋼線の
延性向上に有効である。しかし、１．０％を超えると中
心偏析部にマルテンサイトが生成し、伸線加工性が劣化
するため１．０％を上限とする。Mn is also added as a deoxidizing agent in an amount of 0.3% or more. Further, since Mn has a great effect of improving the hardenability, it is possible to improve the uniformity in the cross section by increasing the Mn content ratio when the wire diameter is large, and the ductility of the steel wire after drawing is increased. It is effective for improvement. However, if it exceeds 1.0%, martensite is generated in the center segregated portion and the wire drawability is deteriorated, so 1.0% is made the upper limit.
【００１１】Ｃｒは、パーライトのラメラー間隔を低減
し、線材の強度と伸線加工性を向上させるため、必要に
応じて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。In order to reduce the lamellar spacing of pearlite and improve the strength and wire drawability of the wire, Cr is added in an amount of 0.1% or more, if necessary. If it is less than 0.1%, the effect is not sufficient. On the other hand, if it exceeds 1.0%, the time required for transformation becomes long, the equipment becomes large, or the production efficiency is lowered. The upper limit.
【００１２】Ｖは、Ｍｎと同様、焼入性を向上させるた
め、線径が大きい場合の強化には効果的である。また、
炭窒化物を形成して析出硬化によりパーライトを強化す
る。この目的のために必要に応じて０．０２％以上添加
する。しかし、Ｖ添加によりパーライト変態が遅延し、
マルテンサイトやベイナイトが生成しやすくなるため、
また、Ｖ炭窒化物の析出硬化作用が飽和するため、０．
３％を上限とする。[0012] V, like Mn, improves the hardenability and is therefore effective for strengthening when the wire diameter is large. Also,
It forms carbonitrides and strengthens pearlite by precipitation hardening. For this purpose, 0.02% or more is added if necessary. However, the addition of V delays the pearlite transformation,
Since martensite and bainite are easily generated,
Further, since the precipitation hardening action of V carbonitride is saturated,
The upper limit is 3%.
【００１３】オーステナイト域で高速かつ高減面率の線
材圧延した後、直ちに冷却する場合には、再加熱パテン
ティングの場合に比べて、オーステナイト結晶粒は細か
くなる傾向を有す。しかし、線材の絞り値や鋼線の延性
をより一層向上させたい場合には、必要に応じてＡｌ，
Ｔｉの１種ないし２種以上を０．１％以下添加する。こ
れらの元素はいずれも炭化物や窒化物を生成しやすく、
このため、オーステナイト粒を細粒化し、線材の延性を
向上する効果が強い。しかし、０．１％を超えて添加し
ても、その効果は飽和するのみならず、非金属介在物が
増加するため、０．１％を上限とする。When the wire rod is rolled at a high speed and a high area reduction rate in the austenite region and then immediately cooled, the austenite crystal grains tend to be finer than in the case of reheating patenting. However, if it is desired to further improve the drawing value of the wire rod and the ductility of the steel wire, Al, if necessary,
One or more kinds of Ti are added in an amount of 0.1% or less. All of these elements easily generate carbides and nitrides,
Therefore, the effect of making the austenite grains finer and improving the ductility of the wire is strong. However, even if added over 0.1%, the effect is not only saturated, but also nonmetallic inclusions increase, so 0.1% is made the upper limit.
【００１４】次に、溶融Ｚｎめっき浴組成の限定理由に
ついて述べる。Ｚｎ−Ａｌ合金の耐食性はＡｌ濃度に依
存し、Ａｌ濃度の高い方が良好な耐食性を示す。従っ
て、十分な耐食性向上効果を得るためには２％以上含有
せしめる必要がある。一方、１２％を超えると添加効果
が飽和してくるうえ、融点上昇によりめっき温度が高く
なり、鋼線強度および捻回値の低下を招く。これより、
Ｚｎ−Ａｌ合金のＡｌ濃度の下限を２％、上限を１２％
とする。Next, the reasons for limiting the composition of the hot-dip Zn plating bath will be described. The corrosion resistance of the Zn-Al alloy depends on the Al concentration, and the higher the Al concentration, the better the corrosion resistance. Therefore, in order to obtain a sufficient effect of improving the corrosion resistance, it is necessary to contain 2% or more. On the other hand, if it exceeds 12%, the effect of addition is saturated, and the melting point rises, the plating temperature rises, and the steel wire strength and the twist value decrease. Than this,
The lower limit of the Al concentration of the Zn-Al alloy is 2%, and the upper limit thereof is 12%.
And
【００１５】Ｚｎ−Ａｌ合金浴中にＳｉを添加する目的
は、鋼製のめっき槽、鋼製シンカーロール、各種鋼製治
具類からのＦｅの溶出を抑制し、それにより、ドロスの
発生を防止することにある。従って、Ｓｉ添加により不
めっき等のめっき欠陥が減少し、めっき鋼線の耐赤錆発
生特性が著しく向上する。Ｓｉ含有量は、０．０１％未
満では上述の効果が認められず、一方、０．０７％を超
えて添加しても合金浴中に溶解しない。その結果、Ｓｉ
添加量は０．０１〜０．０７％とする。The purpose of adding Si to the Zn-Al alloy bath is to suppress the elution of Fe from the steel plating bath, the steel sinker rolls, and various steel jigs, thereby preventing the generation of dross. To prevent. Therefore, by adding Si, plating defects such as non-plating are reduced, and the red rust resistance characteristic of the plated steel wire is significantly improved. Si content is non-0.01%
In not observed effects described above fully, while not soluble in the alloy bath even if added over 0.07%. As a result, Si
The addition amount is 0.01 to 0.07 %.
【００１６】めっき後の鋼線には矯正加工を施す。矯正
の目的は、めっき鋼線の直線性を向上させること、およ
び、以下に述べるブルーイングとの複合効果によりＰＷ
Ｓ鋼線のクリープ値を低減させることである。矯正は、
通常のローラー型矯正機ないしは回転こま式矯正機を用
いて行なう。Straightening is applied to the steel wire after plating. The purpose of straightening is to improve the linearity of the plated steel wire, and to combine PW with the brewing effect described below.
It is to reduce the creep value of S steel wire. Correction
It is carried out by using a normal roller type straightening machine or a rotary top type straightening machine.
【００１７】矯正後の鋼線にはブルーイングを施す。ブ
ルーイングの目的は、矯正により導入された転位を固定
してＰＷＳ鋼線の降伏強度を高めること、および、クリ
ープひずみを減らすことである。ブルーイング温度は、
２５０℃未満では転位の固定が不十分であり、３００〜
３５０℃が好ましい。一方、３７０℃を超えるとめっき
層が軟化し、３８２℃以上ではめっき層の一部が融解す
る。従って、ブルーイング温度の下限は２５０℃、上限
は３７０℃とする。The steel wire after straightening is subjected to bluing. The purpose of bluing is to fix dislocations introduced by straightening to increase the yield strength of PWS steel wire and to reduce creep strain. The brewing temperature is
If the temperature is less than 250 ° C., the dislocation is insufficiently fixed,
350 ° C is preferred. On the other hand, when the temperature exceeds 370 ° C, the plating layer softens, and when the temperature is 382 ° C or higher, part of the plating layer melts. Therefore, the lower limit of the bluing temperature is 250 ° C and the upper limit is 370 ° C.
【００１８】なお、本発明法のＡｌ濃度範囲のＺｎ−Ａ
ｌ合金を使用して溶融めっきを行なった場合、通常の溶
融Ｚｎめっきの場合とは異なり、Ｚｎ−Ｆｅ合金層の発
達はみられず、また、めっき表面光沢もほとんど変化し
ない。本発明法により製造された鋼線が、溶融Ｚｎめっ
き鋼線に比べて良好な耐食性を示す理由は、耐食性に優
れためっき組成であることに加え、上述したように、め
っき層の熱的安定性が高いことによる。Zn-A in the Al concentration range of the method of the present invention is used.
When hot dip plating is performed using the 1-alloy, unlike the normal hot dip Zn plating, no Zn-Fe alloy layer is developed and the plating surface gloss is hardly changed. The reason why the steel wire produced by the method of the present invention exhibits good corrosion resistance as compared with the hot-dip galvanized steel wire is that, in addition to having a plating composition with excellent corrosion resistance, as described above, the thermal stability of the plating layer is stable. It is due to its high quality.
【００１９】[0019]
【実施例】以下に、実施例として、直径５mm、引張強さ
２００kgf/mm2 級および２２０kgf/mm2 級の高張力ＰＷ
Ｓ鋼線の製造効果を示す。表１に示す化学成分の鋼より
製造された直径１３mmの線材をパテンティング後伸線し
直径４．９６mmの鋼線とした。これを酸洗、溶融Ｚｎめ
っきしたのち矯正し、その後、流動層炉を用いてブルー
イングを行なった。めっき付着量はいずれも３００〜３
２０ｇ／ｍ2 である。[Examples] As examples, high tension PWs having a diameter of 5 mm and a tensile strength of 200 kgf / mm 2 grade and 220 kgf / mm 2 grade are given below.
The manufacturing effect of S steel wire is shown. A wire rod having a diameter of 13 mm manufactured from steel having the chemical composition shown in Table 1 was drawn after patenting to obtain a steel wire having a diameter of 4.96 mm. This was pickled, hot-dipped Zn was plated, then straightened, and then bluing was performed using a fluidized bed furnace. The amount of plating is 300 to 3
It is 20 g / m 2 .
【００２０】ＰＷＳ鋼線の評価方法のうち、クリープひ
ずみの測定は次の条件で行なった。
応力＝鋼線の実引張強さ×０．６０
温度＝３５℃
時間＝５００ｈAmong the evaluation methods for PWS steel wire, the creep strain was measured under the following conditions. Stress = Actual tensile strength of steel wire x 0.60 Temperature = 35 ° C Time = 500h
【００２１】また、耐食性の評価は、ＪＩＳ Ｚ２３７
１に規定された塩水噴霧試験により行ない、赤錆発生時
間を溶融Ｚｎめっき鋼線と比較した。結果を下記の
（１）式で定義する耐食性倍率として定量化した。The corrosion resistance is evaluated according to JIS Z237.
The salt spray test specified in 1 was conducted to compare the red rust generation time with the hot dip galvanized steel wire. The result was quantified as the corrosion resistance magnification defined by the following formula (1).
【数１】 [Equation 1]
【００２２】目標とする強度レベルは、ＣｒあるいはＶ
の添加されていないもの（Ａ，Ｂ，Ｆ群）は２００kgf/
mm2 級、添加されているもの（Ｃ，Ｄ，Ｅ，Ｇ群）は２
２０kgf/mm2 級である。目標とする延性は、捻回値（１
００ｄ）で２０回以上、また、耐食性は耐食性倍率で３
以上である。The target strength level is Cr or V.
200kgf / without addition of (A, B, F groups)
mm 2 grade, with 2 added (C, D, E, G groups)
It is 20 kgf / mm 2 grade. The target ductility is the twist value (1
00d) 20 times or more, and the corrosion resistance is 3 in terms of corrosion resistance ratio.
That is all.
【００２３】[0023]
【表１】 [Table 1]
【００２４】[0024]
【表２】 [Table 2]
【００２５】[0025]
【表３】 [Table 3]
【００２６】表１で、Ａ群はＣ含有量、Ｂ群はＳｉ含有
量、Ｃ群はＣｒ含有量、Ｄ群はＶ含有量の影響を示した
ものである。Ｅ−１はＣｒおよびＶの両元素が添加され
ている。Ａ−１はＣ量不足のため目標強度に到達してい
ない。一方、Ａ−６は初析セメンタイトが発生したた
め、鋼線の捻回値が大幅に低下した。同様に、Ｂ群で、
Ｓｉを１．４３％含有するＢ−４は、鋼線の捻回値が低
い。Ｃｒ含有量が１％を超えるＣ−６は、パテンティン
グ材の中心偏析部に少量のマルテンサイトが生成したた
め、鋼線の捻回値が著しく劣化した。Ｄ群でＶを０．３
８％含有するＤ−４の捻回値が低いのも同様の理由によ
る。In Table 1, the effects of the C content in the A group, the Si content in the B group, the Cr content in the C group, and the V content in the D group are shown. E-1 is added with both Cr and V elements. A-1 does not reach the target strength because the amount of C is insufficient. On the other hand, in A-6, proeutectoid cementite was generated, so that the twist value of the steel wire was significantly reduced. Similarly, in group B,
B-4 containing 1.43% Si has a low twist value of the steel wire. With C-6 having a Cr content of more than 1%, a small amount of martensite was generated in the central segregation portion of the patenting material, so that the twist value of the steel wire was significantly deteriorated. V in group D is 0.3
The reason why the twist value of D-4 containing 8% is low is also due to the same reason.
【００２７】Ｆ群はＺｎめっき浴中のＡｌ濃度の影響を
示したものである。Ｆ−１は通常のＺｎめっきである。
Ｆ−２は、Ａｌ濃度が２％未満であるため、耐食性倍率
が３に達していない。Ａｌ濃度の上昇により、はじめ耐
食性は向上するが、やがて飽和する傾向を示す。しか
し、Ｆ−５は、Ａｌ濃度が最も高く、めっき温度が５０
０℃に達したため、鋼線強度が目標値以下となり、さら
に捻回特性も劣化した。Ｄ−５は、Ｄ−１をＳｉを含有
しないめっき浴でめっきしたものであり、耐食性倍率が
溶融Ｚｎめっきの３倍に達していない。Ａ〜Ｇ群の各試
料で、本発明法のＡｌおよびＳｉ濃度範囲でめっきされ
たものは、いずれも溶融Ｚｎめっきの３倍以上という優
れた耐食性を示す。Ｇ群はブルーイング温度の影響を示
したものである。ブルーイング温度が２５０℃未満のＧ
−１は捻回値が低く、かつ、クリープひずみも大きい。Group F shows the influence of Al concentration in the Zn plating bath. F-1 is normal Zn plating.
Since F-2 has an Al concentration of less than 2%, the corrosion resistance magnification does not reach 3. Although the corrosion resistance is improved initially as the Al concentration increases, it tends to saturate. However, F-5 has the highest Al concentration and the plating temperature is 50
Since the temperature reached 0 ° C, the strength of the steel wire fell below the target value, and the twisting characteristics were further deteriorated. D-5 is obtained by plating D-1 with a plating bath containing no Si, and the corrosion resistance ratio does not reach 3 times that of hot-dip Zn plating. Each of the samples of groups A to G plated in the Al and Si concentration ranges of the method of the present invention exhibits excellent corrosion resistance, which is 3 times or more that of hot-dip Zn plating. Group G shows the influence of the brewing temperature. G with a brewing temperature of less than 250 ° C
-1 has a low twist value and a large creep strain.
【００２８】矯正の効果は、ローラー型矯正機を使用し
た場合についてはＡ−２とＡ−３、Ａ−４とＡ−５に、
また、回転こま型矯正機を使用した場合についてはＣ−
２とＣ−３、Ｃ−４とＣ−５に比較して示した。いずれ
の矯正機を使用しても、本発明法である矯正後ブルーイ
ングを付加する方法によれば、ＰＷＳ鋼線のクリープひ
ずみは顕著に低下するのみならず、直線性も大幅に改善
される。The effect of straightening is as follows: A-2 and A-3, A-4 and A-5 when using a roller type straightening machine.
Also, when using a rotary top type straightener, C-
2 and C-3, and C-4 and C-5. Whichever straightening machine is used, the method of adding bluing after straightening, which is the method of the present invention, not only significantly reduces the creep strain of the PWS steel wire, but also significantly improves the linearity. .
【００２９】[0029]
【発明の効果】以上の説明から明らかなように、本発明
によれば、耐食性、直線性、ならびに耐クリープ性に優
れた、引張強さ２００kgf/mm2 級および２２０kgf/mm2
級の吊構造用高強度鋼線（ＰＷＳ鋼線）の製造が可能で
ある。As is clear from the above description, according to the present invention, the tensile strength of 200 kgf / mm 2 grade and 220 kgf / mm 2 which are excellent in corrosion resistance, linearity, and creep resistance.
It is possible to manufacture high-strength steel wire for suspension structure (PWS steel wire).
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｃ２３Ｃ 2/28 Ｃ２３Ｃ 2/28 8/18 8/18 (58)調査した分野(Int.Cl.7，ＤＢ名) C23C 2/38 C21D 9/52 103 C22C 38/00 301 C22C 38/04 C22C 2/06 C22C 2/28 C22C 8/18 C22C 1/02 ─────────────────────────────────────────────────── ─── Continued Front Page (51) Int.Cl. 7 Identification Code FI C23C 2/28 C23C 2/28 8/18 8/18 (58) Fields investigated (Int.Cl. 7 , DB name) C23C 2 / 38 C21D 9/52 103 C22C 38/00 301 C22C 38/04 C22C 2/06 C22C 2/28 C22C 8/18 C22C 1/02
Claims (2)
て溶融めっきしたのち矯正し、その後、２５０〜３７０
℃でブルーイングすることを特徴とする吊構造用高強度
鋼線の製造方法。1. A weight ratio of C: 0.75 to 1.0%, Si: 0.15 to 1.3%, Mn: 0.3 to 1.0%, and the balance Fe and unavoidable impurities. A steel wire is Al: 2 to 12% by weight, Si: 0.01 to 0.07 %, and the rest is hot-dipped with an alloy bath consisting of Zn and unavoidable impurities, and then straightened. 370
A method for producing a high-strength steel wire for a suspended structure, which comprises bluing at ℃.
線を、 重量比で Ａｌ：２〜１２％、 Ｓｉ：０．０１〜０．０７％、 残余をＺｎおよび不可避的不純物からなる合金浴を用い
て溶融めっきしたのち矯正し、その後、２５０〜３７０
℃でブルーイングすることを特徴とする吊構造用高強度
鋼線の製造方法。2. A weight ratio of C: 0.75-1.0%, Si: 0.15-1.3%, Mn: 0.3-1.0%, and Cr: 0.1-1. 0.0%, V: 0.02 to 0.30% of 1 type or 2 types, and further, 1 or 2 types of Al and Ti, each containing 0.1% or less, the balance being Fe and unavoidable impurities. Steel wire consisting of: Al: 2 to 12% by weight, Si: 0.01 to 0.07 %, the rest being hot-dipped with an alloy bath consisting of Zn and unavoidable impurities, and then straightened, 250-370
A method for producing a high-strength steel wire for a suspended structure, which comprises bluing at ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02150393A JP3370368B2 (en) | 1993-02-09 | 1993-02-09 | Manufacturing method of high strength steel wire for suspended structure |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02150393A JP3370368B2 (en) | 1993-02-09 | 1993-02-09 | Manufacturing method of high strength steel wire for suspended structure |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06235054A JPH06235054A (en) | 1994-08-23 |
| JP3370368B2 true JP3370368B2 (en) | 2003-01-27 |
Family
ID=12056777
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP02150393A Expired - Fee Related JP3370368B2 (en) | 1993-02-09 | 1993-02-09 | Manufacturing method of high strength steel wire for suspended structure |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3370368B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102137949A (en) * | 2009-06-25 | 2011-07-27 | 新日本制铁株式会社 | High-strength Zn-Al coated steel wire for bridges excellent in corrosion resistance and fatigue properties and manufacturing method thereof |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101124052B1 (en) | 2007-01-31 | 2012-03-23 | 신닛뽄세이테쯔 카부시키카이샤 | Plated steel wire for pws excelling in torsion property and process for producing the same |
| JP4782247B2 (en) * | 2009-06-29 | 2011-09-28 | 新日本製鐵株式会社 | Zn-Al plated iron wire and method for producing the same |
| JP6237419B2 (en) * | 2014-03-31 | 2017-11-29 | 新日鐵住金株式会社 | Method for producing extra fine brass plated steel wire |
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1993
- 1993-02-09 JP JP02150393A patent/JP3370368B2/en not_active Expired - Fee Related
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102137949A (en) * | 2009-06-25 | 2011-07-27 | 新日本制铁株式会社 | High-strength Zn-Al coated steel wire for bridges excellent in corrosion resistance and fatigue properties and manufacturing method thereof |
| CN102137949B (en) * | 2009-06-25 | 2013-09-11 | 新日铁住金株式会社 | High-strength Zn-Al-plated steel wire for bridges which has excellent corrosion resistance and fatigue properties, and process for production thereof |
| EP2447389A4 (en) * | 2009-06-25 | 2016-08-17 | Nippon Steel & Sumitomo Metal Corp | HIGH-STRENGTH, BRIDGE-ALUMINUM, ZINC PLATED STEEL CABLE WITH EXCELLENT CORROSION RESISTANCE AND EXCELLENT FATIGUE CHARACTERISTICS, AND METHOD OF MANUFACTURING THE SAME |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH06235054A (en) | 1994-08-23 |
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