JPS62228431A - Manufacture of wire rod for long-sized high tension steel wire - Google Patents
Manufacture of wire rod for long-sized high tension steel wireInfo
- Publication number
- JPS62228431A JPS62228431A JP24404885A JP24404885A JPS62228431A JP S62228431 A JPS62228431 A JP S62228431A JP 24404885 A JP24404885 A JP 24404885A JP 24404885 A JP24404885 A JP 24404885A JP S62228431 A JPS62228431 A JP S62228431A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- wire rod
- strength
- long
- ceq
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 17
- 239000010959 steel Substances 0.000 title claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 238000001816 cooling Methods 0.000 claims abstract description 21
- 238000003466 welding Methods 0.000 claims abstract description 14
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 10
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 238000005098 hot rolling Methods 0.000 claims abstract 2
- 239000000203 mixture Substances 0.000 abstract description 12
- 229910052719 titanium Inorganic materials 0.000 abstract description 5
- 229910052796 boron Inorganic materials 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 229910052758 niobium Inorganic materials 0.000 abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 abstract description 3
- 238000010438 heat treatment Methods 0.000 description 23
- 238000000034 method Methods 0.000 description 15
- 239000000463 material Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 7
- 230000001788 irregular Effects 0.000 description 7
- 229910000734 martensite Inorganic materials 0.000 description 7
- 239000013307 optical fiber Substances 0.000 description 7
- 238000005336 cracking Methods 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 239000010953 base metal Substances 0.000 description 3
- 230000006698 induction Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 235000019362 perlite Nutrition 0.000 description 1
- 239000010451 perlite Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は長尺高張力ｍｓ用用材材製造方法に関するもの
である。DETAILED DESCRIPTION OF THE INVENTION (Industrial Field of Application) The present invention relates to a method for manufacturing a long high-tensile strength MS material.
（従来の技術）
光ファイバーは、その低損失、細径、大容量、経済性な
どの優れた特性を活して、海底ケーブルに導入すること
が試みられているが、例えば特公昭５９−７３６１号公
報では、光フアイバーケーブルとして第１図に示すよう
に、断面の形状が互いに等しく扇形の３本の金属材料異
形線（以下異形線という）が組合わされて、中心部に少
くとも１本の光ファイバーを収容する耐圧パイプが提案
されている。(Prior Art) Optical fibers have been attempted to be introduced into submarine cables by taking advantage of their excellent characteristics such as low loss, small diameter, large capacity, and economic efficiency. In the publication, as shown in Fig. 1, an optical fiber cable is constructed by combining three irregularly shaped metal wires (hereinafter referred to as irregular wires) with equal fan-shaped cross-sections, and at least one optical fiber in the center. A pressure-resistant pipe has been proposed that accommodates.
この構造では、光フアイバー心線１０を中心に置き、回
りから断面扇形の異形線２０を連続的に合わせながら、
一本の円筒状の耐圧層を形成するものである。この耐圧
層材料は深海の海水圧（例えば８０００ｍの深海ではＳ
ＯＯ気圧）に耐え得る。In this structure, an optical fiber core wire 10 is placed at the center, and irregular wires 20 having a fan-shaped cross section are continuously aligned from the surroundings.
It forms a single cylindrical pressure-resistant layer. This pressure-resistant layer material is made of seawater pressure in the deep sea (for example, S
Can withstand 00 atmospheric pressure).
一方、海底ケーブルは障害を考慮して接続函の最適設置
間隔が定められているか、現在約５０〜１００ Ｋｍ毎
に接続函を設置するのが経済的とされている。しかしな
がら異形線用素材である線材の製造について検討してみ
ると、現用鋳造設備及び加熱炉の能力の制約から、大単
重化を図ってみても線材の単長は３０，０００ｍに限定
される。On the other hand, for submarine cables, the optimum installation interval for connecting boxes is determined in consideration of failures, and it is currently considered economical to install connecting boxes every 50 to 100 km. However, when we consider the production of wire rods, which are materials for irregularly shaped wires, we find that even if we try to increase the unit weight, the single length of the wire rods is limited to 30,000 m due to the limitations of the current casting equipment and heating furnace capacity. .
従って、長距離の海底ケーブルの耐圧パイプ用素材とし
ての線材には、前記の扇形の異形線をうる冷間加工性と
、長尺化のための溶接性とを同時に満足させることが望
まれる。Therefore, it is desired that wire rods used as materials for pressure-resistant pipes of long-distance submarine cables simultaneously satisfy the above-mentioned cold workability for producing fan-shaped deformed wires and weldability for lengthening the wires.
そこでこのような加工性と溶接性とを同時に満足させ得
るような鋼材としては、例えば特公昭５９−２２７７４
号公報ではＴｉ、Ｂ を含有し、ＣｅｑＯ１５５％以
下の鋼を制御圧延して、５５ Ｋｙｆ／ｍｊ以上の引張
強さを有する溶接性及び加工性の優れた線材が提案され
ている。又特公昭５９−２９６４８号公報では溶接性の
すぐれた高強度鉄筋材が提案されている。Therefore, as a steel material that can satisfy such workability and weldability at the same time, for example, Japanese Patent Publication No. 59-22774
The publication proposes a wire rod with excellent weldability and workability, which has a tensile strength of 55 Kyf/mj or more and has a tensile strength of 55 Kyf/mj or more, which is produced by controlled rolling of steel containing Ti and B 2 and CeqO of 155% or less. Furthermore, Japanese Patent Publication No. 59-29648 proposes a high-strength reinforcing bar material with excellent weldability.
しかしながらこれらの鋼材は、それらを冷間加工して得
られる鋼線の強度が低く、海底ケーブルの耐圧パイプ用
の異形線には供し得ない。However, the strength of the steel wire obtained by cold working these steel materials is low, and it cannot be used as a deformed wire for pressure-resistant pipes of submarine cables.
（元側が解決しようとする問題点）
本発明は、溶接性及び冷間加工性に優れた長尺高張力鋼
線用の線材の製造方法を提供するものである。(Problems to be Solved by Original Party) The present invention provides a method for manufacturing a wire rod for a long high-tensile steel wire that has excellent weldability and cold workability.
（問題点を解決するための手段作用）
重量係でＣ０，３０〜ｏ、６５％、Ｓｉ１．０％以下、
Ｍｎ ０．３〜１．５％、Ｃｒ１．２％以下でＭｎ十Ｃ
ｒ０．３〜１．５ ％、及びＩ Ｏ，００２〜０．１％
、Ｔｉ０．００２〜０．１％、Ｎｂ Ｏ，００１−０，
３％、ＶＯ，ＯＯ１〜０．３％、Ｂｏ、０００５〜０．
１％の１種または２種以上を合計０．０００５〜０．３
％、残部Ｆｅ及び不可避不純物から成ると共に、Ｃｅｑ
＝−（Ｍｎ＋Ｃｒ）≧０．５７％を満足する鋼塊を熱
間圧延し、続いて該線材を溶接して長尺線材とし、該溶
接部をオーステナイト域に加熱保持し、続いて３〜２０
℃／ｓｅａで冷却して、微細なフェライト・パーライ
ト組織とすることを特徴とする長尺高張力鋼線用線材の
製造方法である。(Means and actions to solve the problem) Weight: C0, 30~0, 65%, Si: 1.0% or less,
Mn 0.3 to 1.5%, Cr 1.2% or less
r0.3-1.5%, and IO,002-0.1%
, Ti0.002-0.1%, NbO,001-0,
3%, VO, OO1-0.3%, Bo, 0005-0.
1% of one or more types in total 0.0005 to 0.3
%, the balance consists of Fe and unavoidable impurities, and Ceq
A steel ingot that satisfies =-(Mn+Cr)≧0.57% is hot-rolled, then the wire rod is welded to form a long wire rod, the welded part is heated and maintained in the austenite region, and then
This is a method for producing a long high-tensile steel wire rod, which is characterized by cooling at a temperature of .degree. C./sea to form a fine ferrite-pearlite structure.
以下本発明について詳細に説明する。The present invention will be explained in detail below.
海底光フアイバー用ケーブルの耐圧パイプは、引張強さ
１２６ＫＢ／−以上、好ましくは１３０Ｋｙｆ／−以上
を要求される。鋼線の強度は、素材の強度と冷間加工量
によって決るが、本発明者らの検討によると、例えば第
１図に示した幾形線２゜を製造するには、冷間加工率を
８５％以下に抑えることが、加工割れの発生を抑制する
上で必要である。製品強度１２６ Ｋ５＋ｆ／−を８５
％以下の冷間加工率で得るためには、素材の線材には７
ｏＫｐｆ／ｍｊ以上の引張強さが必要である。A pressure-resistant pipe for a submarine optical fiber cable is required to have a tensile strength of 126 KB/- or more, preferably 130 Kyf/- or more. The strength of steel wire is determined by the strength of the material and the amount of cold working, but according to the studies of the present inventors, for example, in order to manufacture the 2° geometric wire shown in Figure 1, the cold working rate must be increased. It is necessary to suppress the occurrence of processing cracks to 85% or less. Product strength 126 K5+f/-85
In order to obtain a cold working rate of less than 7%, the wire material must be
A tensile strength of oKpf/mj or more is required.
父上記素材は溶接部の強度、靭性に優れることが求めら
れている。一般に溶接性はＣ量に比例して悪化の傾向に
あるが、引張強さ７ｏＫｙｔ／−以上を満たすために適
量のＣと可能な範囲で、ＭｎあるいはＭｎの一部をＣｒ
に置換して添加することが望ましい。The above materials are required to have excellent strength and toughness in the welded area. In general, weldability tends to deteriorate in proportion to the amount of C, but in order to satisfy the tensile strength of 7 oKyt/- or more, Mn or a part of Mn must be replaced with Cr in an appropriate amount of C and within the possible range.
It is desirable to add it by replacing it with .
このように本発明においては、強度、溶接性及び加工性
を満足するために、特定の成分元素を添加するものであ
るが、以下に成分元素の添加範囲を上記のように限定し
た理由を説明する。In this way, in the present invention, specific component elements are added in order to satisfy strength, weldability, and workability.The reason for limiting the range of addition of component elements as described above will be explained below. do.
Ｃは溶接性の点から低い方が望ましいが、０．３係未満
ではｔｏＫｙｔ／−以上の強度は得られない。From the viewpoint of weldability, it is desirable that C be lower, but if it is less than 0.3, a strength of toKyt/- or more cannot be obtained.
一方、０□６５チ超では溶接部の靭性、加工性が劣化す
るので、０．３０％〜０．６５％とする。On the other hand, if it exceeds 0□65 inches, the toughness and workability of the welded part will deteriorate, so it should be set at 0.30% to 0.65%.
Ｓｌ はその固溶体硬化作用によって線材を強化する
ために添加されるが、１％を超えると靭性を劣化させる
ので１％を上限とした。Sl is added to strengthen the wire through its solid solution hardening effect, but if it exceeds 1%, the toughness deteriorates, so the upper limit was set at 1%.
Ｍｎ は溶接性への影響が少なく、強度を増加させる
元素であり、可能な範囲で添加することが望ましい。Ｍ
ｎ ０．３％未満ではＳを硫化物として固定することが
出来ず、また７ ０ ＫＢ／−以上の線材の強度を得る
こともできない。一方１．５チ超では線材の焼入性が高
くなりすぎて、溶接部に熱処理後マルテンサイトが発生
し、加工性を著しく劣化させることがあるので、０．３
％〜１．５係に添加範囲を限定した。Mn is an element that has little effect on weldability and increases strength, and is preferably added to the extent possible. M
If n is less than 0.3%, S cannot be fixed as a sulfide, and a wire strength of 70 KB/- or more cannot be obtained. On the other hand, if it exceeds 1.5 inch, the hardenability of the wire becomes too high, and martensite may occur in the welded part after heat treatment, which may significantly deteriorate workability.
The addition range was limited to 1.5% to 1.5%.
ＣｒはＭｎと全く同じ作用を持つ元素で、Ｍｎの一部と
置換して添刀口することが出来るが、ＭｎとＣｒの合計
量が１．５係を超えると、溶接部に熱処理後マルテンサ
イトが発生するので、Ｃｒ１．２％以下、Ｍｎ −１−
Ｃｒ １．５係以下に添加量を限定した。Cr is an element that has exactly the same effect as Mn, and can be added by substituting a part of Mn, but if the total amount of Mn and Cr exceeds 1.5, martensite will form in the weld after heat treatment. is generated, so Cr is 1.2% or less, Mn -1-
The amount added was limited to 1.5 parts or less of Cr.
ＡＡ、 Ｔｉ 、 Ｎｂ、 Ｖ、 Ｂはいずれもオース
テナイト粒変の調整のだめに１種または２種以上添加さ
れるが、ＡＩ！ｏ、ｏｏ２％未満、Ｔｉ０．００２チ未
満、ＮｂＯ，００１１未満、ＶＯ，００１１未満、ＢＯ
，０００５係未満で且つ１種または２種以上の合計が０
．０００５％未満では細粒化されないし、ＭＯ８１係超
、Ｔｉ０．１％超、Ｎｂ０．３％超、ｖ ０．３ ％超
、Ｂ ０．１ ％超で且つ１種または２種以上の合計が
０．３係超では、細粒化効果が飽和するばかりでなく、
これらの元素の窒化物による脆化作用が顕著になるので
、Ａ１０．００２〜０．１％、Ｔｉｅ、００２〜０．１
％、ＮｂＯ，ＯＯ１〜０．３％、Ｖｏ、００１〜０，３
多、８０．０００５〜０．１％で且つこれらの１種また
は２種以上の合計を０．０００５〜０．３％に限定した
。One or more of AA, Ti, Nb, V, and B are added to adjust austenite grain deformation, but AI! o, oo less than 2%, Ti less than 0.002, NbO, less than 0011, VO, less than 0011, BO
, less than 0005 and the total of one or more types is 0
．． If the content is less than 0.0005%, the particles will not be refined, and if the content is more than MO81, Ti0.1%, Nb0.3%, V0.3%, B0.1% or more, and the total of one or more of them is When the coefficient exceeds 0.3, not only the grain refining effect is saturated, but also
Since the embrittlement effect due to nitrides of these elements becomes significant, A10.002~0.1%, Tie, 002~0.1%
%, NbO, OO1-0.3%, Vo, 001-0,3
The total content of one or more of these was limited to 0.0005 to 0.3%.
ｐ、ｓはいずれも不純物としてみられるが、靭性の点か
らそれぞれ０．０３％以下にすることが望ましい。また
Ｎは時効脆化を抑制するために０，０１チ以下に抑える
ことが望ましい。Both p and s are seen as impurities, but from the viewpoint of toughness, it is desirable to limit each to 0.03% or less. Further, in order to suppress aging embrittlement, it is desirable to suppress N to 0.01 inch or less.
線材の強度はＣｅｑ ＝ Ｃ＋ ｇ （Ｍｎ十Ｃｒ ）
と、線材のオーステナイト域からの冷却速度によって決
り、Ｃｅｑが高いほど、また冷却速度が高いほど強度は
増加するが、本発明者らの検討によると、Ｃｅｑが０．
５７％以上ないと、いかに高速で冷却しても７０Ｋｐｆ
／−以上の強度を有するフェライト・パーライト鋼線材
は得られないことが明らかになった。これはＣｅｑがｏ
、５７％より低い線材を強度を上げるために高速冷却す
ると、加工性に致命的なマルテンサイトが現われるため
である。The strength of the wire is Ceq = C + g (Mn + Cr)
This is determined by the cooling rate from the austenite region of the wire rod, and the higher the Ceq and the higher the cooling rate, the higher the strength, but according to the studies of the present inventors, when Ceq is 0.
If it is not 57% or more, no matter how fast you cool it, it will be 70Kpf.
It has become clear that a ferrite-pearlite steel wire rod having a strength of /- or more cannot be obtained. This means Ceq is o
, 57%. If the wire rod is cooled at high speed in order to increase its strength, martensite will appear, which is fatal to the workability.
本発明の異形線用線材は、常法により線材圧延されて調
整冷却された後、溶接されて長尺線材とされ、更に溶接
部を熱処理して整粒された微細なフェライト・パーライ
ト組織とされ、更に冷間伸線または冷間圧延により所要
サイズとされる。The wire rod for deformed wires of the present invention is rolled by a conventional method, adjusted and cooled, and then welded into a long wire rod, and the welded part is further heat-treated to form a fine ferrite-pearlite structure. , and further formed into the required size by cold wire drawing or cold rolling.
線材の溶接は強加圧アップセット方式、ＴＩＧ方式ある
いはレーザ一方式等を用い、格別限定されないが、例え
ば強加圧アップセット方式は、最初比較的低電流密度（
ん７５ Ａ／ｍｊ ）で通電を開始する。継手が軟化し
、初期加圧力にて変形を受けだすと同時に通電を停止し
、いわゆる強加圧力（〜５０ Ｋｆ／ｒｔｕｊ ）
を加える。あとは加圧力と軟化部が追出されていった後
の抗力とのバランスで停止すると良い。Wire rod welding uses a strong pressure upset method, a TIG method, a single laser method, etc., and is not particularly limited. For example, the strong pressure upset method uses a relatively low current density (
75 A/mj). As soon as the joint softens and begins to deform under the initial pressure, the current supply is stopped and the so-called strong pressure (~50 Kf/rtuj) is applied.
Add. After that, it is best to stop with a balance between the pressurizing force and the drag force after the softened part is expelled.
ここで溶接部は衝合部とその近傍の熱影響部はＡ１点以
上に加熱された後急冷される。従って溶接ままでは、溶
接部はビッカース硬度が６００以上のマルテンサイト組
織となるので、著しく延性に欠ける。そこで線材から異
形線への加工性を向上させるために、溶接部をオーステ
ナイト域に加熱冷却する熱処理によって、母材と同等の
強度を有するフェライト・パーライト組織にすることが
必要となる。Here, in the welded part, the abutting part and the heat affected zone in the vicinity thereof are heated to a point above A1 and then rapidly cooled. Therefore, in the as-welded state, the welded part becomes a martensitic structure with a Vickers hardness of 600 or more, and is extremely lacking in ductility. Therefore, in order to improve the workability of wire rods into deformed wires, it is necessary to heat-treat the welded part to heat and cool it to an austenite region to create a ferrite-pearlite structure that has the same strength as the base metal.
即ち、本発明者らは、溶接部を母材と同等の７０Ｋｙｆ
／−以上の強度を有するフェライト・パーライト組織に
するための熱処理条件を検討した。その結果、溶接部を
オーステナイト域に加熱後、冷却するときの冷却速度の
選定が重要で、７０Ｋｐｆ／ｍＡ以上の強度を有するフ
ェライト・パーライト組織にするためには、３〜ｂ
却する必要があることが明らかになった。That is, the present inventors applied a welding temperature of 70 Kyf, which is equivalent to that of the base metal.
The heat treatment conditions for creating a ferrite/pearlite structure with a strength of /- or more were investigated. As a result, it is important to select the cooling rate when cooling the welded part after heating it to the austenite region.In order to create a ferrite-pearlite structure with a strength of 70 Kpf/mA or more, it is necessary to It became clear.
こ肚は冷却速度が３℃／ｓｅｃ未満では７ｏＫｐｆ／ｍ
ｊ以上の強度を得ることが出来ないためであり、一方２
０℃／ｓｅｃを超えると、再びマルテンサイト組織が現
われ加工性を劣化させるためである。冷却速度をこのよ
うな範囲に制御する手段は特に限定しないが、通電加熱
あるいは高周波加熱によって、電流量を制御しながら低
減させる手段、衝風冷却する手段などが良い。When the cooling rate is less than 3℃/sec, the cooling rate is 7oKpf/m.
This is because it is not possible to obtain a strength greater than j; on the other hand, 2
This is because when the temperature exceeds 0° C./sec, a martensitic structure appears again, degrading workability. The means for controlling the cooling rate within this range is not particularly limited, but suitable means include means for reducing the amount of current while controlling it by electrical heating or high-frequency heating, means for blast cooling, and the like.
後熱処理後の組織はほぼ母材と同じになり、硬度の差も
あまりない。溶接会合部ではわずかにフェライト量が多
いが、異形線に成形後はほとんど母材部との差異はない
。The structure after post-heat treatment is almost the same as that of the base material, and there is not much difference in hardness. The amount of ferrite is slightly higher in the weld joint, but after forming into a deformed wire, there is almost no difference from the base metal.
本発明の線材は最終りダクションが８０多以上に及ぶダ
イス引抜と、ロール乎圧延とを受けて異形線とする場合
が多いので、冷間加工性が要求される。このため本発明
の線材の組織は、全長にわたり整粒されたフェライト・
パーライト組織でなければならない。Since the wire rod of the present invention is often subjected to die drawing with a final reduction of 80 or more and roll rolling to form a deformed wire, cold workability is required. For this reason, the structure of the wire rod of the present invention is composed of ferrite grains that are grained throughout the entire length.
Must be perlite texture.
光フアイバー異形線は例えば７■φ線材をダイス引抜し
て４．３Ｕとし、ロールで平圧延して２．３朋厚の断面
矩形状線材とする。ついで扇形にするためダイス引抜を
行い、第１図に示すように内径ａ ＝ ３． Ｏｇ、外
径ｂ ＝ ６．０１２３、厚みｔ、＝１゜５朋の異形線
２０をうろことができる。The optical fiber deformed wire is, for example, a 7 dia. wire drawn through a die to form a wire rod of 4.3 U, and rolled flat with rolls to form a wire rod having a rectangular cross section with a thickness of 2.3 mm. Next, the die is drawn to form a fan shape, and as shown in FIG. 1, the inner diameter a = 3. Og, outer diameter b = 6.0123, thickness t, = 1° 5 mm.
なお、本発明はホースの外装などの長尺の高張力鋼線用
の線材の製造にも有効である。Note that the present invention is also effective in manufacturing wire rods for long high-tensile steel wires such as hose exteriors.
次に実施例をあげて本発明の効果を更に具体的に説明す
る。Next, the effects of the present invention will be explained in more detail with reference to Examples.
（実施例）
第１表に線材の組成、Ｃｅｑ、寸法、線材を溶接した手
段、溶接後その溶接部に加えた熱処理条件、線材を、第
１図に示した形状の内径３１３、外径６、０ 藺、厚み
１．５Ｕの異形線２０に加工したときの加工性及び異形
線の強度を併記した。この内磁１、３．４．５．７．８
．９．１０ が本発明例であり、他は比較例である。(Example) Table 1 shows the wire rod composition, Ceq, dimensions, the means by which the wire was welded, the heat treatment conditions applied to the welded part after welding, and the wire rod in the shape shown in Fig. 1 with an inner diameter of 313 and an outer diameter of 6. , 0. The workability and strength of the irregular wire when processed into the irregular wire 20 with a thickness of 1.5 U are also shown. This inner magnet 1, 3.4.5.7.8
．． 9.10 is an example of the present invention, and the others are comparative examples.
１ｍｌは本発明組成を満足し、Ｃｅｑ Ｏ，５９％、７
、５１１３の径で、強度８１ ＫＢ／ｍｊの線材をＴｒ
Ｇ溶接し、更に溶接部を８７０℃に４０秒高岡波方式で
加熱後８℃／ｓｅｃの速度で冷却し、引続き異形線に加
工した場合の結果で、加工中継線トラブルもなく、また
異形線は１３２ Ｋｐｆ／−の強度を示した。1ml satisfies the composition of the present invention, Ceq O, 59%, 7
, a wire rod with a diameter of 5113 and a strength of 81 KB/mj is Tr
G welding, the welded part was further heated to 870℃ for 40 seconds using the Takaoka wave method, and then cooled at a rate of 8℃/sec, and then processed into an irregularly shaped wire.There was no problem with the processing relay wire, and the irregularly shaped wire was showed an intensity of 132 Kpf/-.
一方間２は、組成、線径、強度及び線材の溶接方法はＮ
ａ ］、と同じであるが、溶接部の熱処理において加熱
後の冷却速度が２℃／ｓｅｃと小さかったために、溶接
部の強度が不足し、従って異形線強度が１２６Ｋｙｒ：
／−に達していない。On the other hand, for 2, the composition, wire diameter, strength, and wire welding method are N.
a], but because the cooling rate after heating during the heat treatment of the weld was as low as 2°C/sec, the strength of the weld was insufficient, and the deformed wire strength was 126 Kyr:
/- has not been reached.
Ｉ＠３は本発明組成で且つｃｅｑ ｏ、６２％、８．７
ｒｌ。I@3 has the composition of the present invention and ceq o, 62%, 8.7
rl.
の径で７ ｓ ＫＰｆ／−の強度を有する線材を、強加
圧アップセット方式で溶接し、更に溶接部を９００℃に
３０秒高岡波方式で加熱後、８℃／ ｓｅｃの冷却速度
で冷却し、その後異形線に加工した結果を示すもので、
断線中割れを生ずることもなく、１３７に９ｆ／ｙｊの
異形線が製造された。Wire rods with a diameter of , which shows the result of processing into irregularly shaped wires.
A deformed wire of 9 f/yj was manufactured in 137 without any cracking during wire breakage.
随４は本発明組成を満足し、且つｏ、６４％のＣｅｑと
８８ Ｋ９ｆ／−の強度を有する７、 ６１１３の線材
を、同じく強加圧アップセット方式で溶接し、溶接部を
８５０℃に１分直接通電で加熱後、１１℃／ ｓｅｃの
冷却速度で溶接して異形線に加工したときの結果で、断
線事故もなく、１３８ Ｋｐｆ／−の強度を有する異形
線が得られた。No. 4 is a wire rod of 7.6113 which satisfies the composition of the present invention and has a Ceq of 64% and a strength of 88K9f/-, and is welded using the same strong pressure upset method, and the welded part is heated to 850℃ for 1 hour. After heating by direct energization for 1 minute, welding was performed at a cooling rate of 11° C./sec to form a deformed wire, and a deformed wire with a strength of 138 Kpf/- was obtained without any disconnection accidents.
Ｎｆｌ ５は同じく本発明組成からなり、且つＣｅｑＯ
３６８％、６．８ツの径で、８５Ｋｐｆ／−の強度を有
する線材をレーザ一方式で溶接し、溶接部を通電加熱方
式で、８４０℃に４５秒加熱後、６℃／ｓｅｃの冷却速
度で冷却したのち、異形加工したもので、無事１２０
Ｋ９ｆ／−の異形線が得られた。Nfl 5 also consists of the composition of the present invention and contains CeqO
A wire rod with a diameter of 368%, 6.8 mm, and a strength of 85 Kpf/- was welded using a single laser method, and the welded part was heated to 840 °C for 45 seconds using an electric current heating method, followed by a cooling rate of 6 °C/sec. After cooling it in
A deformed line of K9f/- was obtained.
は６は随５と全く同じ組成、線径、強度を有し、溶接も
同じくレーザ一方式で行われたが、溶接後の熱処理で、
冷却速度を２３℃／ ｓｅｃまで上げたために、熱処理
実施個所にマルテンサイトが現われ、加工性が劣化した
例である。No. 6 had exactly the same composition, wire diameter, and strength as No. 5, and welding was also performed using the same laser method, but in the heat treatment after welding,
This is an example where the cooling rate was increased to 23°C/sec, and martensite appeared in the heat-treated areas, resulting in poor workability.
Ｎ［１７は本発明組成から成り、Ｃｅｑｏ、５５％、９
．０藷の径で、７１Ｋｙｔ／−の強度の線材を強加圧ア
ップセット方式で溶接し、更に溶接部を高周波誘導加熱
で９２０℃に２０秒加熱後、７℃／ ｓｅｃで冷却し、
異形線に加工したもので、割れの発生もなく１３ｓＫｐ
ｆ／−の強度を有する異形線が得られた。N [17 consists of the composition of the present invention, Ceqo, 55%, 9
．． Wire rods with a diameter of 0.5 mm and a strength of 71 Kyt/- were welded using a strong pressure upset method, and the welded part was heated to 920 °C for 20 seconds by high-frequency induction heating, and then cooled at 7 °C / sec.
Processed into irregularly shaped wire, 13sKp without cracking
A profiled wire with an intensity of f/- was obtained.
更に随８は本発明組成から成り、且つＣｅｑ Ｏ，７２
％、７．４１の径で９３ＫＰｆ／−の線材をフラッシュ
バット溶接し、溶接部を通電加熱方式で８４０℃×４０
秒加熱後、１２℃／ ｓｅｃで冷却して、その後異形線
に加工したもので、途中割れが生ずることもなく、ｌ
ｓ ｏ ＫＨ／−の強度の異形線を得ることができた。Furthermore, No. 8 consists of the composition of the present invention, and Ceq O, 72
%, a diameter of 7.41 and a wire rod of 93KPf/- was flash butt welded, and the welded part was heated at 840℃ x 40
After heating for seconds, cooling at 12℃/sec, and then processing into irregularly shaped wire, there is no cracking during the process, and the l
It was possible to obtain an irregular line with an intensity of s o KH/-.
闇９は本発明組成を満足し、且つＣｅｑ Ｏ，６０％、
８．２．の径で８２にグｆ／−の強度の線材をレーザー
溶接し、溶接部を高周波誘導加熱で８８０℃に３０秒加
熱後、１８℃／ Ｓｅｃで冷却して、その後異形線に加
工したもので、割れを発生することなく加工でき、１４
０ ＫＳ’ｆ／ｒＩｊの異形線が得られた。Darkness 9 satisfies the composition of the present invention, and contains Ceq O, 60%,
8.2. A wire with a diameter of 82 mm and a strength of 82 mm/- is laser welded, the welded part is heated to 880℃ for 30 seconds by high frequency induction heating, cooled at 18℃/sec, and then processed into a deformed wire. , can be processed without cracking, 14
An irregular line of 0 KS'f/rIj was obtained.
またＮｌ１１０は同じく本発明組成から成り、且つＣｅ
ｑ ０．６３％、６．４１の径で５ｓＫｐｆ／−の線材
を強加圧アップセット方式で溶接し、溶接部を高周波誘
導加熱で８５０℃に７０秒加熱後、１５℃、／ｓｅｃの
冷却速度で冷却し、その後異形線加工した場合の結果で
、１３４ ＫＰｆ／ｍｊ の鋼線が得られた。In addition, Nl110 also has the composition of the present invention, and has Ce
q 0.63%, a wire rod with a diameter of 6.41 and a diameter of 5sKpf/- was welded using a strong pressure upset method, and the welded part was heated to 850℃ for 70 seconds using high-frequency induction heating, and then the cooling rate was 15℃/sec. When the wire was cooled and then processed into a modified wire, a steel wire of 134 KPf/mj was obtained.
随１１〜２０は比較例で、忠１１はＭｎが本発明の下限
を下回っているために、１２６ Ｋｙｆ／−の異形線強
度に到達しなかった例、随１２はＳｌが本発明の上限を
上回ると共に、溶接後の熱処理の冷速も本発明の上限を
上回ったために、加工性が著しく劣化した例、随１３は
Ｃが本発明の下限を下回っているために、１２６Ｋｐｆ
／−の製品強度に到達しなかった例、ｌ＠１４と１５は
それぞれＭとＮｂが本発明の上限を超えているために、
多食の窒化物が析出して加工性が劣化した例、随１６は
ＣとＣｒ が共に本発明の上限を超えているために、
溶接部に熱処理後マルテンサイトが現われ、加工性が劣
化した例、随１７はＭｎとＣｒは単独では本発明内にあ
るが、その合計量が１．５係を超え、またＴ１ とＢ
も本発明の上限を超えているために加工性が劣化した例
、Ｎ［１１ＢはＣ，Ｍｎ、Ｃｒ単独では本発明内にある
が、Ｃｅｑが本発明の下限を下回り、且つまた溶接後の
熱処理の冷速も本発明の下限を下回っているために、製
品強度が１２６ Ｋｙ ｆ ／ｍｊに達しなかった例、
醜１９はＭｎ、Ｓｉ、Ｖがいずれも本発明の上限を超え
、またｐ、ｓも０．０３％を超え、更には溶接後の熱処
理の冷速も２０℃／ｓｅｃを超えているために加工性が
劣化した例、随２０はＡｌｌ、 Ｔｉ 、 Ｎｂ 、
Ｂ単独では本発明内にあるが、その合計量が本発明の上
限を超え、またＮも０．０１２０％も含有されていたた
めに、加工性が劣化した例を示す。Nos. 11 to 20 are comparative examples, and No. 11 is an example in which the irregular wire strength of 126 Kyf/- was not reached because Mn was below the lower limit of the present invention, and No. 12 was an example in which Sl exceeded the upper limit of the present invention. At the same time, the cooling rate of the heat treatment after welding also exceeded the upper limit of the present invention, resulting in significant deterioration in workability.
The examples where the product strength of /- was not reached, l@14 and 15, are because M and Nb exceed the upper limit of the present invention, respectively.
In Example 16, where machinability deteriorated due to the precipitation of highly erodible nitrides, both C and Cr exceeded the upper limits of the present invention.
In Example 17, where martensite appeared in the weld after heat treatment and the workability deteriorated, Mn and Cr are within the scope of the present invention individually, but their total amount exceeds a factor of 1.5, and T1 and B
An example in which workability deteriorated because N[11B exceeds the upper limit of the present invention, C, Mn, and Cr alone are within the scope of the present invention, but Ceq is below the lower limit of the present invention, and also after welding An example where the product strength did not reach 126 Ky f /mj because the cooling rate of the heat treatment was also below the lower limit of the present invention,
Ugly 19 is because Mn, Si, and V all exceed the upper limit of the present invention, p and s also exceed 0.03%, and furthermore, the cooling rate of heat treatment after welding exceeds 20 ° C / sec. Examples of deteriorated workability, No. 20 are All, Ti, Nb,
Although B alone is within the scope of the present invention, the total amount thereof exceeds the upper limit of the present invention, and since 0.0120% of N was also contained, the workability was deteriorated.
（発明の効果）
以上の実施例からも明らかなように、本発明は炭素鋼の
成分を特定して、線材のアズロールの引張強さｔｏＫ９
ｒ／−以上を得て、溶接によって長尺線材とし、溶接部
の熱処理によって全長に亘り整粒された微細なフェライ
ト・パーライト組織を得るので、海底ケーブル用異形線
の製造条件に適応する線材を容易に製造し得て、その工
業的効果は犬である。(Effects of the Invention) As is clear from the above examples, the present invention specifies the components of carbon steel and increases the tensile strength toK9 of the wire rod Azurol.
r/- or more, a long wire is made by welding, and a fine ferrite/pearlite structure that is grained over the entire length is obtained by heat treatment of the welded part, so it is possible to create a wire that is suitable for the manufacturing conditions of deformed wires for submarine cables. It is easy to manufacture and its industrial effectiveness is outstanding.
第３図は公知の異形線の断面図である。 １０・・光ファイバー心線、 ２０・・・異形線。 FIG. 3 is a sectional view of a known deformed wire. 10... Optical fiber core wire, 20... Deformed wire.
Claims (1)
Ｍｎ０．３〜１．５％、Ｃｒ１．２％以下で、Ｍｎ＋Ｃ
ｒ０．３〜１．５％、及びＡｌ０．００２〜０．１％、
Ｔｉ０．００２〜０．１％、Ｎｂ０．００１〜０．３％
、Ｖ０．００１〜０．３％、Ｂ０．０００５〜０．１％
の１種または２種以上を、合計０．０００５〜０．３％
、残部Ｆｅ及び不可避不純物から成ると共に、Ｃｅｑ＝
Ｃ＋１／５（Ｍｎ＋Ｃｒ）≧０．５７％を満足する鋼塊
を熱間圧延し、続いて該線材を溶接して長尺線材とし、
該溶接部をオーステナイト域に加熱保持し、続いて３〜
２０℃／ｓｅｃで冷却して、微細なフェライト・パーラ
イト組織とすることを特徴とする長尺高張力鋼線用線材
の製造方法。C0.30-0.65%, Si 1.0% or less in weight%,
Mn 0.3-1.5%, Cr 1.2% or less, Mn+C
r0.3-1.5%, and Al0.002-0.1%,
Ti0.002-0.1%, Nb0.001-0.3%
, V0.001-0.3%, B0.0005-0.1%
One or more of the following, totaling 0.0005 to 0.3%
, the balance consists of Fe and unavoidable impurities, and Ceq=
Hot rolling a steel ingot satisfying C+1/5(Mn+Cr)≧0.57%, then welding the wire rod to make a long wire rod,
The welded part is heated and maintained in the austenite region, and then 3~
A method for producing a long high-tensile steel wire rod, which comprises cooling at 20° C./sec to obtain a fine ferrite-pearlite structure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24404885A JPS62228431A (en) | 1985-11-01 | 1985-11-01 | Manufacture of wire rod for long-sized high tension steel wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24404885A JPS62228431A (en) | 1985-11-01 | 1985-11-01 | Manufacture of wire rod for long-sized high tension steel wire |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62228431A true JPS62228431A (en) | 1987-10-07 |
| JPH0454728B2 JPH0454728B2 (en) | 1992-09-01 |
Family
ID=17112946
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP24404885A Granted JPS62228431A (en) | 1985-11-01 | 1985-11-01 | Manufacture of wire rod for long-sized high tension steel wire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62228431A (en) |
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| KR100340643B1 (en) * | 1997-07-02 | 2002-07-18 | 이구택 | Manufacture method of wire rod for welding rod |
| WO2008044859A1 (en) * | 2006-10-11 | 2008-04-17 | Posco | Steel wire rod for high strength and high toughness spring having excellent cold workability, method for producing the same and method for producing spring by using the same |
| JP2009527638A (en) * | 2005-12-27 | 2009-07-30 | ポスコ | Steel wire rod excellent in cold workability and hardenability, and manufacturing method thereof |
| US7732733B2 (en) * | 2005-01-26 | 2010-06-08 | Nippon Welding Rod Co., Ltd. | Ferritic stainless steel welding wire and manufacturing method thereof |
| US20130133789A1 (en) * | 2010-08-17 | 2013-05-30 | Makoto Okonogi | Steel wire of special steel and wire rod of special steel |
| WO2014054756A1 (en) | 2012-10-04 | 2014-04-10 | 新日鐵住金株式会社 | Shaped steel wire for undersea-cable protecting tube, manufacturing method therefor, and pressure-resistant layer |
| EP2765213A4 (en) * | 2011-10-07 | 2016-03-30 | Kobe Steel Ltd | Steel wire for bolt, bolt, and manufacturing processes therefor |
| CN110453145A (en) * | 2019-08-20 | 2019-11-15 | 南京钢铁股份有限公司 | High-strength quake-proof reinforcing steel bar and rolling mill practice |
-
1985
- 1985-11-01 JP JP24404885A patent/JPS62228431A/en active Granted
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| KR100340643B1 (en) * | 1997-07-02 | 2002-07-18 | 이구택 | Manufacture method of wire rod for welding rod |
| US7732733B2 (en) * | 2005-01-26 | 2010-06-08 | Nippon Welding Rod Co., Ltd. | Ferritic stainless steel welding wire and manufacturing method thereof |
| JP2009527638A (en) * | 2005-12-27 | 2009-07-30 | ポスコ | Steel wire rod excellent in cold workability and hardenability, and manufacturing method thereof |
| WO2008044859A1 (en) * | 2006-10-11 | 2008-04-17 | Posco | Steel wire rod for high strength and high toughness spring having excellent cold workability, method for producing the same and method for producing spring by using the same |
| US8734599B2 (en) | 2006-10-11 | 2014-05-27 | Posco | Steel wire rod for high strength and high toughness spring having excellent cold workability, method for producing the same and method for producing spring by using the same |
| US20130133789A1 (en) * | 2010-08-17 | 2013-05-30 | Makoto Okonogi | Steel wire of special steel and wire rod of special steel |
| US10704118B2 (en) * | 2010-08-17 | 2020-07-07 | Nippon Steel Corporation | Steel wire and wire rod |
| US11203797B2 (en) | 2010-08-17 | 2021-12-21 | Nippon Steel Corporation | Steel wire and wire rod |
| EP2765213A4 (en) * | 2011-10-07 | 2016-03-30 | Kobe Steel Ltd | Steel wire for bolt, bolt, and manufacturing processes therefor |
| WO2014054756A1 (en) | 2012-10-04 | 2014-04-10 | 新日鐵住金株式会社 | Shaped steel wire for undersea-cable protecting tube, manufacturing method therefor, and pressure-resistant layer |
| 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 |
| CN110453145A (en) * | 2019-08-20 | 2019-11-15 | 南京钢铁股份有限公司 | High-strength quake-proof reinforcing steel bar and rolling mill practice |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0454728B2 (en) | 1992-09-01 |
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