JPS62166093A - Low alloy steel wire having excellent drawability - Google Patents
Low alloy steel wire having excellent drawabilityInfo
- Publication number
- JPS62166093A JPS62166093A JP518686A JP518686A JPS62166093A JP S62166093 A JPS62166093 A JP S62166093A JP 518686 A JP518686 A JP 518686A JP 518686 A JP518686 A JP 518686A JP S62166093 A JPS62166093 A JP S62166093A
- Authority
- JP
- Japan
- Prior art keywords
- alloy steel
- low alloy
- wire
- steel wire
- content
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 33
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 21
- 238000005096 rolling process Methods 0.000 abstract description 7
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 238000010438 heat treatment Methods 0.000 abstract description 6
- 229910045601 alloy Inorganic materials 0.000 abstract description 4
- 239000000956 alloy Substances 0.000 abstract description 4
- 238000001816 cooling Methods 0.000 description 15
- 229910000831 Steel Inorganic materials 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 239000002184 metal Substances 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 8
- 239000010959 steel Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 230000000694 effects Effects 0.000 description 5
- 238000003466 welding Methods 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 238000005491 wire drawing Methods 0.000 description 3
- 229910006639 Si—Mn Inorganic materials 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 229910002092 carbon dioxide Inorganic materials 0.000 description 2
- 239000001569 carbon dioxide Substances 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 238000010583 slow cooling Methods 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000007847 structural defect Effects 0.000 description 1
Landscapes
- Metal Extraction Processes (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は５１−Ｍｎ系、５ｉ−）４ｎ−Ｔｉ系低合金鋼
線材に関し、特に炭酸ガスアーク溶接棒用ワイヤなどに
使用される５１−Ｍｎ系、５１−Ｍｎ−Ｔｉ系低炭素ｗ
４線材に関し、また上記線材の伸線加工性の改善に関す
る。Detailed Description of the Invention [Field of Industrial Application] The present invention relates to 51-Mn series, 5i-)4n-Ti series low alloy steel wire rods, particularly 51-Mn series used for wires for carbon dioxide arc welding rods. system, 51-Mn-Ti low carbon w
4 wire rod, and also relates to improving the wire drawability of the wire rod.
炭酸ガスアーク溶接棒用ワイヤなどに使用される従来の
低合金鋼線材の組成は、Ｃが０．０３〜０．１４重量％
（以下１％は重量％とする） 、Ｓｉが０．５０〜１．
２０％、Ｍｎが１．０〜２．０％で、必要に応じて０．
０１〜０゜２５％のＴｉ、 ０．０１〜０．０５％のＡ
旦を含み、残部がＦｅおよび不可避的に含まれる不純物
からなるものである。The composition of conventional low-alloy steel wire rods used for carbon dioxide arc welding rods is 0.03 to 0.14% by weight of C.
(Hereinafter, 1% is defined as weight %), Si is 0.50 to 1.
20%, Mn is 1.0 to 2.0%, and if necessary 0.
01~0°25% Ti, 0.01~0.05% A
The remainder consists of Fe and unavoidably contained impurities.
上記のような従来の低合金鋼線材は、熱間圧延された後
、０．５〜１５°Ｃ／ｓｅｃの冷却速度で冷却された場
合、ｉ）島状マルテンサイト、アシュキラーフェライト
組織の発生、ｉｉ） Ｔｉ化合物の析出による強度レベ
ルの上昇とそのバラツキの増加、という組織的欠陥を有
し、伸線性の劣化、機械的性質の不均一などの聞届を生
じている。このため、従来は、通常の圧延ではそのまま
伸線して最終製品とすることはできず、伸線加工性、機
械的性質の均一性などを確保するために線材もしくは中
間仕上り線において軟化焼鈍処理が必要であった。When the conventional low-alloy steel wire rod as described above is cooled at a cooling rate of 0.5 to 15°C/sec after being hot rolled, i) the formation of island-like martensite and Ashkiller ferrite structures; , ii) It has structural defects such as an increase in the strength level and an increase in its dispersion due to the precipitation of Ti compounds, and there are reports of deterioration of wire drawability and non-uniformity of mechanical properties. For this reason, in the past, wire rods or intermediate finished wires were subjected to softening annealing in order to ensure wire drawing workability and uniformity of mechanical properties. was necessary.
また、最近、制御圧延、制御冷却（徐冷）技術を応用し
て材質の均一化を図ろうとする二三の試みがある（例え
ば、アール・アンド・デー神戸製鋼技報、第３５巻、第
２号（１９８５年４月）、第５２頁〜第５４頁）、また
一部の試みとして鋼片の低温圧延、熱間圧延材の徐冷法
の採用などにより伸線加工性の改善、材質の均一化を図
ったものが報告されているが、伸線加工性のうえで必須
である。島状マルテンサイト含有率（面精率で示す、以
下同様とする）を２．０％以下に抑えることは完全には
達成されておらず、また熱間圧延の負荷を大きくし生産
性を大きく阻害する点などがあり、焼鈍処理の省略まで
に至っていないのが実情である。Recently, there have been several attempts to make the material uniform by applying controlled rolling and controlled cooling (slow cooling) technologies (for example, R&D Kobe Steel Technical Report, Vol. 35, Vol. No. 2 (April 1985, pp. 52-54), and some attempts have been made to improve wire drawability and make the material uniform by low-temperature rolling of steel slabs and slow cooling of hot-rolled materials. Although there have been reports of cases in which this method has been improved, it is essential in terms of wire drawability. It has not been completely achieved to suppress the island martensite content (indicated by surface accuracy, the same shall apply hereinafter) to 2.0% or less, and it is necessary to increase the load of hot rolling and increase productivity. The reality is that the annealing process has not yet been omitted due to some obstacles.
〔発明が解決しようとする問題点〕
本発明は、上記従来技術の問題点を解消し、熱処理なし
に細径まで伸線し得る低合金鋼線材の提供を目的とする
ものである。[Problems to be Solved by the Invention] It is an object of the present invention to solve the problems of the prior art described above and to provide a low alloy steel wire rod that can be drawn to a small diameter without heat treatment.
上記目的を達成するため１本発明の伸線加工性の優れた
低合金鋼線材は、ｉ ） ０．５０ 〜１．２０％のＳ
ｉおよび１，００〜２．００％のＭｎを含有し且つＣ量
が０．０２％以下で残部が実質的にＦｅであり、島状マ
ルテンサイトの含有率を１．０％以下として、あるいは
、ｉｉ） ０．５Ｑ 〜１．２０％のＳｉ、１，００
〜２．００％ノＭｎ８よび０．０１〜０．２５％のＴｉ
を含有し且つＣ量が０．０１％以下、Ｎ量が０．００５
％以下で残部が実質的にＦｅであり、島状マルテンサイ
トの含有率を１．０％以下とするものである。In order to achieve the above objects, the low alloy steel wire rod of the present invention with excellent wire drawability is: i) 0.50 to 1.20% S
i and 1,00 to 2.00% of Mn, and the amount of C is 0.02% or less and the remainder is substantially Fe, and the content of island martensite is 1.0% or less, or , ii) 0.5Q ~ 1.20% Si, 1,00
~2.00% Mn8 and 0.01-0.25% Ti
and the amount of C is 0.01% or less and the amount of N is 0.005
% or less, the remainder is substantially Fe, and the content of island martensite is 1.0% or less.
本発明の低合金鋼線材は、組成を極低炭素化し、島状マ
ルテンサイト含有率を伸線加工性の良好な１％以下にコ
ントロールした組織とすることによって、熱処理なしに
細径まで伸線することを可能にしている。伸線性を良好
とするためには、島状マルテンサイトの含有率を１．０
％以下にすることが必要なのである。通常の圧延時の冷
却速度でも島状マルテンサイトの含有率を１．０％以下
に抑えるためには、線材中のＣ量を前記の値以下にする
ことが必要である。The low-alloy steel wire rod of the present invention has an ultra-low carbon composition and a structure in which the content of island martensite is controlled to 1% or less, which has good wire drawability, so that it can be drawn to a small diameter without heat treatment. making it possible to do so. In order to improve wire drawability, the content of island martensite should be 1.0.
It is necessary to keep it below %. In order to suppress the content of island martensite to 1.0% or less even at a cooling rate during normal rolling, it is necessary to reduce the amount of C in the wire to the above-mentioned value or less.
島状マルテンサイトの面積率が増加すれば、そのマルテ
ンサイトを起点としてカッピー断線の生じる確率が高く
なり、伸線加工性を著しく低下せしめる０組成を極低炭
素化すると、マルテンサイトの硬さが下り、またその含
有率も低下し、マルテンサイトの含有率が１％以下であ
れば伸線限界も１．ｈｍφ以下となって優れた伸線性が
得られる。If the area ratio of island-shaped martensite increases, the probability of cuppy wire breakage occurring from the martensite increases, and if the zero composition, which significantly reduces wire drawability, is made to have an extremely low carbon content, the hardness of martensite increases. The martensite content also decreases, and if the martensite content is 1% or less, the wire drawing limit is 1. hmφ or less, and excellent wire drawability can be obtained.
本発明の低合金鋼線材における各元素の含有量を前記の
ように定めた理由を以下に述べる。The reason why the content of each element in the low alloy steel wire of the present invention is determined as described above will be described below.
Ｃは本発明を特徴づける元素で、５１−Ｍ！１鋼では０
．０２％以下であれば、またＳｉ −Ｋｎ −Ｔｉ＃ｌ
テは０．０１％以下であれば通常の圧延時の冷却速度で
も、島状マルテンサイトの含有率を１％以下に抑えるこ
とが可能となる。C is an element that characterizes the present invention, and is 51-M! 0 for 1 steel
．． 02% or less, Si -Kn -Ti#l
If Te is 0.01% or less, the content of island martensite can be suppressed to 1% or less even at a normal cooling rate during rolling.
Ｓｉは、強力な脱酸元素であり、不純物介在物量を減じ
て溶接金属の強度を高める為には０．５０％以上必要で
あるが、多すぎるとフェライトを形成しσ脆化が起こり
易く溶接金属の靭性が低下するので１．２０％以下に抑
える必要がある。Si is a strong deoxidizing element, and 0.50% or more is necessary to reduce the amount of impurity inclusions and increase the strength of weld metal, but if it is too large, ferrite will form and σ embrittlement will easily occur. Since the toughness of the metal decreases, it is necessary to suppress it to 1.20% or less.
Ｍ ｎは、Ｓｉと同様脱酸効果を有すると共に溶接金属
の強度向上と高温割れ感受性を抑制する作用があり、こ
の作用発揮のためには１．０％以上必要であるが、多す
ぎると溶接金属の延びが劣化する傾向があるので２．０
％以下に抑える必要がある。Like Si, Mn has a deoxidizing effect and also has the effect of improving the strength of the weld metal and suppressing hot cracking susceptibility, and in order to exert this effect, 1.0% or more is required, but if it is too large, welding 2.0 because the elongation of metal tends to deteriorate.
It is necessary to keep it below %.
Ｔｉは、溶接時の入熱増加にともなう溶接金属の強度、
靭性低下の防止および高電流域における溶接アークの軟
質化などのために選択的に必要であり、このために微細
な炭化物を形成して析出硬化を図る作用を得るには０，
０１％以上に好ましくは０．０５％以上必要であるが、
０．２５％を越えると前記した析出硬化による強度レベ
ルが増加してワイヤの製造に伸線性の劣化を招くととも
に、溶接金属のクリープ破断強さを逆に低下させてしま
う。Ti increases the strength of weld metal due to increase in heat input during welding,
It is selectively necessary to prevent a decrease in toughness and to soften the welding arc in a high current range, and for this purpose, 0,
0.01% or more, preferably 0.05% or more is required,
If it exceeds 0.25%, the strength level due to the precipitation hardening described above will increase, leading to deterioration in wire drawability in the manufacture of wire, and conversely decreasing the creep rupture strength of the weld metal.
Ｎは、５１−Ｍｎ−Ｔｉ鋼において０．００５％を越え
るとＴｉＮまたはＴｉＣＮの型で析出硬化し、線材の強
度上昇につながるので０．００５％以下とした。N was set to 0.005% or less in 51-Mn-Ti steel because if it exceeds 0.005%, precipitation hardening occurs in the TiN or TiCN mold, leading to an increase in the strength of the wire rod.
本発明は、従来技術とは異なり、全く圧延上の負荷の増
大なしに、完全に熱処理を省略できる低合金鋼線材の提
供を可能としたものである。The present invention, unlike the prior art, makes it possible to provide a low-alloy steel wire rod that can completely omit heat treatment without increasing the rolling load at all.
（実施例１）
Ｓｉ−Ｍｎ系低合金鋼線材の熱間圧延後の、線材冷却速
度（９００°Ｃと ５００°との間の平均冷却速度）と
ビッカース硬さとの関係を調べた。その結果を第１図に
示す０曲線１は本実施例の場合で、Ｃが０．０１％、Ｓ
ｉが０．８７％、Ｍｎが１．７０％、Ｔｉが０．００２
％で残部が実質的にＦｅの組成を有するものである。比
較のため、従来の５ｉ−１１ｎ系低合金鋼についても調
べ、曲線２，３に示した。(Example 1) The relationship between the wire cooling rate (average cooling rate between 900°C and 500°C) and Vickers hardness after hot rolling of Si-Mn based low alloy steel wire was investigated. The 0 curve 1 shown in FIG. 1 is the case of this example, where C is 0.01% and S
i is 0.87%, Mn is 1.70%, Ti is 0.002
%, and the remainder has a composition of substantially Fe. For comparison, conventional 5i-11n low alloy steel was also investigated and shown in curves 2 and 3.
曲線２はＣが０．０３％、Ｓｉが０．７７％、Ｍｎが１
．５８％、Ｔｉが０．００２％の場合、曲線３はＣが０
．０８％、Ｓｉが ０．７７％、にｎが １．６４％、
Ｔｉが ０．００２％の場合で、いずれも従来例である
。Curve 2 is C 0.03%, Si 0.77%, Mn 1
．． 58% and Ti is 0.002%, curve 3 shows C as 0.
．． 08%, Si 0.77%, Ni 1.64%,
The case where Ti is 0.002% is a conventional example.
曲線１に示される本実施例の５１−Ｍｎ系低合金鋼は冷
却速度に関係なく低い硬さを示しているが、曲線２，３
に示される従来の材料では冷却速度の上昇に従って硬さ
が増加している。したがって、本実施例の線材は従来の
ものよりも伸線加工性がすぐれていると言える。The 51-Mn-based low alloy steel of this example shown in curve 1 shows low hardness regardless of the cooling rate, but curves 2 and 3 show low hardness regardless of the cooling rate.
In the conventional material shown in , the hardness increases as the cooling rate increases. Therefore, it can be said that the wire rod of this example has better wire drawability than the conventional wire rod.
（実施例２）
実施例１と同様の実験を５ｉ−１４ｎ−Ｔｉ系低合金ｗ
４線材について行なった。その結果を第２図に示す０曲
線４は本実施例の場合で、Ｃが０．０１％、Ｓｉが０．
８４％、Ｍｎが１．７３％、Ｔｉが０．１７％、Ｎが０
．００４％で残部が実質的にＦｅの組成を有するもので
ある。比較のため、従来のＳｉ−にｎ−Ｔｉ系低合金鋼
についても調べ１曲線５に示した１曲線５はＣが０．０
６％、Ｓｉが ０．８４％、Ｍｎが １．６４％、Ｔｉ
が０．１８％、Ｎが０．００７％の場合である。また、
曲線６は本発明の ５１−Ｍｎ−Ｔｉ系低合金鋼線材よ
りもＣＭかや−多く ０．０２％の場合で、Ｓｉは ０
．８３％、Ｍｎは １．８０％、Ｔｉは ０．１３％、
Ｎは０．００５％である。(Example 2) The same experiment as in Example 1 was conducted using a 5i-14n-Ti based low alloy w.
The test was conducted on 4 wire rods. The zero curve 4 shown in FIG. 2 is the case of this example, where C is 0.01% and Si is 0.01%.
84%, Mn 1.73%, Ti 0.17%, N 0
．． 0.004%, with the remainder being substantially Fe. For comparison, we also investigated conventional Si- and n-Ti based low alloy steels, and curve 1 shown in curve 5 shows that C is 0.0.
6%, Si 0.84%, Mn 1.64%, Ti
is 0.18% and N is 0.007%. Also,
Curve 6 is the case where the CM is slightly more than the 51-Mn-Ti low alloy steel wire of the present invention by 0.02%, and the Si is 0.
．． 83%, Mn 1.80%, Ti 0.13%,
N is 0.005%.
実施例１の場合と同様に、曲ａ４に示される本実施例の
５１−Ｍｎ−Ｔｉ系低合金鋼線材は冷却速度に関係なく
低い硬さを示しているが、曲線５に示される従来の材料
ならびに曲線６に示されるＣ量が０．０２％の材料では
冷却速度の上昇に従って、硬さが増加している。したが
って、本実施例の線材は他のものよりも伸線加工性がす
ぐれていると言える。As in the case of Example 1, the 51-Mn-Ti low alloy steel wire of this example shown by curve a4 shows low hardness regardless of the cooling rate, but the conventional 51-Mn-Ti low alloy steel wire shown by curve In the material and the material with a C content of 0.02% shown in curve 6, the hardness increases as the cooling rate increases. Therefore, it can be said that the wire rod of this example has better wire drawability than other wire rods.
（実施例３）
第１表に示す組成の低合金鋼線材を同表に示すｌ０４０
°Ｃ前後の温度からｌＯ°Ｏ／ｓの冷却速度で冷却し、
引張り強さ、絞り、島状マルテンサイト面積率を測定す
るとともに、どの位細い線径にまで伸線できるか調べた
。(Example 3) A low alloy steel wire rod having a composition shown in Table 1 was used as l040 shown in the same table.
Cooling from a temperature around °C at a cooling rate of 1O °O/s,
In addition to measuring the tensile strength, area of area, and island martensite area, we investigated how thin the wire diameter could be.
その結果を組成とともに第１表に示した。χは測定値の
平均値、σＣはバラツキを示す、伸線限界は１２°のダ
イスと２５°のダイスを用いて調べた。鋼Ａ、Ｂは従来
の低合金鋼、鋼Ｃは炭素量が０．０２％のＳｉ −Ｍｎ
−Ｔｉ系低合金鋼、鋼りは本実施例の５１−Ｍｎ系低合
金鋼、鋼Ｅは本実施例の５１−Ｍｎ−Ｔｉ系低合金鋼で
ある。The results are shown in Table 1 along with the composition. χ indicates the average value of the measured values, σC indicates the variation, and the wire drawing limit was investigated using a 12° die and a 25° die. Steels A and B are conventional low alloy steels, and steel C is Si-Mn with a carbon content of 0.02%.
-Ti-based low-alloy steel, steel is the 51-Mn-based low-alloy steel of this example, and steel E is the 51-Mn-Ti-based low-alloy steel of this example.
第１表から明らかなように１本実施例の線材は、従来の
材料ならびＣｌが０．０２％の５１−Ｍｎ−Ｔｉ系低合
金鋼線材に比較して、引張強さが低くそのバラツキも小
さい上に、絞り値も高い値を示している。さらに、本実
施例の線材のみが、金属組織における島状マルテンサイ
トの面積率が１％以下であり、その結果、伸線限界の線
径も他よりも細く良好である。したがって、第１表のデ
ータからも、本発明の線材は、他に比較して機械的性質
の均一性ならびに伸線性のすぐれていることが明らかで
ある。As is clear from Table 1, the wire rod of this example has lower tensile strength and less variation than conventional materials and 51-Mn-Ti low alloy steel wire rods with a Cl content of 0.02%. Not only is it small, but it also has a high aperture value. Furthermore, only the wire of this example has an area ratio of island-like martensite in the metal structure of 1% or less, and as a result, the wire diameter at the drawing limit is smaller and better than the others. Therefore, it is clear from the data in Table 1 that the wire rod of the present invention has excellent uniformity of mechanical properties and wire drawability compared to other wire rods.
（実施例４）
Ｓｉ−）ｌｎ系低合金鋼ならびに５ｉ−Ｌｎ−Ｔｉ系低
合金鋼について、径が５．５ ｍ＋ａの圧延材の金属組
織を調べた。実験は本発明の線材および従来の線材を用
いて行なった。４００倍の倍率の全屈組織顕微鏡写真を
第３図に示す。第３図から明らかなように、本実施例に
おける低合金鋼線材はフェライト相のみであり、従来の
低合金鋼線材はアシュギラーフエライト、島状マルテン
サイトが認められる。したがって、金属組織的見地から
も、本発明の低合金鋼線材は優れた伸線加工性と機械的
性質の均一性を期待できる。(Example 4) The metallographic structures of rolled materials having a diameter of 5.5 m+a were investigated for Si-)ln-based low alloy steel and 5i-Ln-Ti-based low alloy steel. Experiments were conducted using the wire of the present invention and a conventional wire. A full flexural tissue micrograph at 400x magnification is shown in Figure 3. As is clear from FIG. 3, the low alloy steel wire in this example has only a ferrite phase, whereas the conventional low alloy steel wire has Ashgiller ferrite and island martensite. Therefore, also from the viewpoint of metallographic structure, the low alloy steel wire rod of the present invention can be expected to have excellent wire drawability and uniformity of mechanical properties.
本発明の低合金鋼線材は、改善された全屈組織を有し、
通常圧延のみで容易に優れた伸線加工性が得られ、熱処
理を省略できる。The low alloy steel wire rod of the present invention has an improved total bending structure,
Excellent wire drawability can be easily obtained just by ordinary rolling, and heat treatment can be omitted.
第１図は５１−Ｍｎ系低合金鋼線材の冷却速度と硬さと
の関係を示すグラフ、第２図は５ｉ−１１ｎ−Ｔｉ系低
合金鋼線材の冷却速度と硬さとの関係を示すグラフ、第
３図は５１−Ｍｎ系および５１−Ｍｎ−Ｔｉ系低合金鋼
線材の金属組織を示す顕微鏡写真である。
■・・・・・・・・本発明の一実施例における線材の場
合、２，３・・・・・・・・従来の線材の場合、４・・
・・・・・・本発明の他の実施例における線材の場合、
５・・・・・・・・従来の線材の場合、６・・・・・・
・・本発明における組成と異なる組成の線材の場合。FIG. 1 is a graph showing the relationship between the cooling rate and hardness of a 51-Mn-based low alloy steel wire, and FIG. 2 is a graph showing the relationship between the cooling rate and hardness of a 5i-11n-Ti-based low alloy steel wire. FIG. 3 is a micrograph showing the metal structure of 51-Mn-based and 51-Mn-Ti-based low alloy steel wire rods. ■...In the case of the wire rod according to one embodiment of the present invention, 2, 3......In the case of the conventional wire rod, 4...
......In the case of the wire rod in other embodiments of the present invention,
5... In the case of conventional wire rods, 6...
...In the case of a wire rod having a composition different from that in the present invention.
Claims (2)
〜２．００重量％のＭｎを含有し且つＣ量が０．０２重
量％以下で残部が実質的にＦｅであり、島状マルテンサ
イトの含有率が１．０％以下であることを特徴とする伸
線加工性の優れた低合金鋼線材。(1) 0.50-1.20% by weight of Si and 1.00% by weight
It is characterized by containing ~2.00% by weight of Mn, the amount of C being 0.02% by weight or less, the balance being substantially Fe, and the content of island martensite being 1.0% or less. A low alloy steel wire rod with excellent wire drawability.
．００重量％のＭｎおよび０．０１〜０．２５重量％の
Ｔｉを含有し且つＣ量が０．０１重量％以下、Ｎ量が０
．００５重量％以下で残部が実質的にＦｅであり、島状
マルテンサイトの含有率が１．０％以下であることを特
徴とする伸線加工性の優れた低合金鋼線材。(2) 0.50-1.20 wt% Si, 1.00-2
．． 00% by weight of Mn and 0.01 to 0.25% by weight of Ti, the amount of C is 0.01% by weight or less, and the amount of N is 0
．． A low alloy steel wire rod with excellent wire drawability, characterized in that the balance is substantially Fe at 0.05% by weight or less, and the content of island martensite is 1.0% or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP518686A JPS62166093A (en) | 1986-01-14 | 1986-01-14 | Low alloy steel wire having excellent drawability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP518686A JPS62166093A (en) | 1986-01-14 | 1986-01-14 | Low alloy steel wire having excellent drawability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62166093A true JPS62166093A (en) | 1987-07-22 |
Family
ID=11604196
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP518686A Pending JPS62166093A (en) | 1986-01-14 | 1986-01-14 | Low alloy steel wire having excellent drawability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62166093A (en) |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS589792A (en) * | 1981-07-10 | 1983-01-20 | Kobe Steel Ltd | Low fume wire for gas shielded arc welding |
-
1986
- 1986-01-14 JP JP518686A patent/JPS62166093A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS589792A (en) * | 1981-07-10 | 1983-01-20 | Kobe Steel Ltd | Low fume wire for gas shielded arc welding |
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