JPS583919A - Manufacture of steel wire rod - Google Patents
Manufacture of steel wire rodInfo
- Publication number
- JPS583919A JPS583919A JP10124481A JP10124481A JPS583919A JP S583919 A JPS583919 A JP S583919A JP 10124481 A JP10124481 A JP 10124481A JP 10124481 A JP10124481 A JP 10124481A JP S583919 A JPS583919 A JP S583919A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- steel wire
- wire rod
- weight
- rolling
- 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
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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (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)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
この発明は、伸線時における耐折損性に優れた鋼線材の
製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for producing a steel wire rod with excellent breakage resistance during wire drawing.
鋼線材には、低炭素鋼線材がら中・高炭素鋼線材、さら
には合金鋼線材に至るまで数多くのものがあるが、これ
らの鋼線材は、多くの場合、鋼塊または横片を熱間圧延
した後球状化焼なましを行なうことにより製造される。There are many types of steel wire rods, ranging from low carbon steel wire rods to medium and high carbon steel wire rods, and even alloy steel wire rods. It is manufactured by rolling and then annealing it into a spheroid.
そして、この鋼線材を線引加工により伸線して鋼線とす
るのが普通である。ところが、上記伸線工程において、
熱間圧延や線材の運搬中などにおいて生じた微少な表面
疵を起点として折損を生ずることがあり、このような折
損の発生は伸線工程での能率を著しく低下させるものと
なっていた。そこで従来、上記表面疵に対する改善策と
して、表面疵を渦流探傷法などの検査手段によって全長
にわたって検査したり、表面溶剤や表面皮むきなどによ
って表面疵を除去したりするなどの対策が椎されること
が多いが、微少な表面疵については完全に除去すること
は困難である。また、このような対策を施した場合には
、表面疵を発見した際に伸線作業を一時的に中断させた
り、表面溶剤などによって歩留りが低下したりするなど
、鋼＠製造コストが上昇するという問題を有していた。Then, this steel wire rod is usually drawn into a steel wire by a wire drawing process. However, in the above wire drawing process,
Breakage can occur due to minute surface flaws that occur during hot rolling or during transportation of the wire rod, and the occurrence of such breakage significantly reduces efficiency in the wire drawing process. Conventionally, countermeasures against the above-mentioned surface flaws have been taken, such as inspecting the surface flaws over the entire length using inspection methods such as eddy current testing, and removing surface flaws using surface solvents, surface peeling, etc. However, it is difficult to completely remove minute surface flaws. Additionally, if such measures are taken, steel manufacturing costs will increase due to temporary suspension of wire drawing work when surface flaws are discovered, and yield reduction due to surface solvents, etc. There was a problem.
そのため、表面疵の程度が同じであっても伸線時に折損
を生じがたい鋼線材の開発も望まれていたが、従来より
この種の問題に対する研究はあまり行なわれておらず、
表面疵の存在下で伸線時の折損発生を低減する方法はあ
まり提案ちれていない。Therefore, there has been a desire to develop a steel wire rod that is less likely to break during wire drawing even if the degree of surface flaws is the same, but there has been little research into this type of problem.
There have not been many proposals for methods for reducing the occurrence of wire breakage during wire drawing in the presence of surface flaws.
そこで、本発明者らは、鋼線材の靭性を高めることによ
って伸線時の折損発生を低減することに着目して種々の
実験研究を積み重ねた結果、この種の鋼線材の靭性は、
第１図および第２図に示すようなプレスノツチ曲げ試験
による破断たわみを測定することによって評価できるこ
とを確認し、破断たわみのより大きな鋼線材を開発する
ことを目的としてさらに実験を積み重ね、この発明を完
成するに至った。なお、第１図および第２図において、
１は試験片、２は抑圧具、６は支え、４は試験片１に形
成した切欠部である。Therefore, the present inventors focused on reducing the occurrence of breakage during wire drawing by increasing the toughness of the steel wire rod, and as a result of various experimental studies, the toughness of this type of steel wire rod is as follows.
It was confirmed that the evaluation could be made by measuring the fracture deflection by the press notch bending test as shown in Figures 1 and 2, and further experiments were carried out with the aim of developing a steel wire rod with a larger fracture deflection. It was completed. In addition, in Fig. 1 and Fig. 2,
1 is a test piece, 2 is a suppressor, 6 is a support, and 4 is a notch formed in the test piece 1.
この発明は、上述した従来の問題点に着目してなされた
もので、上記の如く、破断たわみのより大きな鋼線材を
開発し、この鋼線材を伸線して鋼線とする伸線工程での
折損発生を低減できるようにすることを目的としている
。This invention was made by focusing on the above-mentioned conventional problems, and as described above, a steel wire rod with a larger breaking deflection was developed, and a wire drawing process for drawing this steel wire rod into a steel wire was made. The purpose is to reduce the occurrence of breakage.
この発明は、Ｃ： ０．４〜１．５重量％、Ｓｔ ：
０．１〜０．４重量％、Ｍｎ：０．１〜１．５重量％を
基本組成とし、さらに必要に応じて適宜の合金成分を含
む鋼を用いて熱間圧延により鋼線材を製造するに際し、
６００℃以上Ａｒ３変態点以下の温度で減面率３０％以
上の圧延を行ない、その後通常の方法で球状化部なまし
を行なうようにしたことを特徴としている。This invention contains C: 0.4 to 1.5% by weight, St:
A steel wire rod is produced by hot rolling using steel having a basic composition of 0.1 to 0.4% by weight, Mn: 0.1 to 1.5% by weight, and further containing appropriate alloy components as necessary. On this occasion,
It is characterized in that it is rolled with an area reduction of 30% or more at a temperature of 600° C. or higher and lower than the Ar3 transformation point, and then the spheroidized portion is smoothed by a conventional method.
この発明に係る鋼線材は、Ｃ：帆４〜１．５重量％、ｓ
ｉ ： ｏ、ｉ 〜０．４重量％、Ｍｎ ： ０．１〜
１．５重量％を基本組成とし、さらに必要に応じて適宜
の合金元素を添加含有するものであり、たとえば普通炭
素鋼線材（硬鋼線材、ばね鋼線材、冷間圧造用炭素鋼線
材等を含む）や、合金鋼線材（ばね鋼線材、耐熱鋼線材
、鉄クロム電熱線材等を含む）などがある。The steel wire rod according to the present invention has C: sail 4 to 1.5% by weight, s
i: o, i ~0.4% by weight, Mn: 0.1~
The basic composition is 1.5% by weight, and additionally contains appropriate alloying elements as necessary.For example, ordinary carbon steel wire rod (hard steel wire rod, spring steel wire rod, carbon steel wire rod for cold heading, etc.) ) and alloy steel wire rods (including spring steel wire rods, heat-resistant steel wire rods, iron-chromium heating wire rods, etc.).
上記化学成分のうち、Ｃはその含有量が０．４重ｔ％未
満では鋼線としての必要な強度が期待できず、また、１
．５重量％を越えると網状セメンタイトが多く生成して
靭性を著しく損うため、０．４〜１．５重吋係とした。Among the above chemical components, if the content of C is less than 0.4% by weight, the necessary strength as a steel wire cannot be expected;
．． If it exceeds 5% by weight, a large amount of reticular cementite will be produced and the toughness will be significantly impaired, so the content is set at 0.4 to 1.5% by weight.
また、Ｓｉは製鋼作業において脱酸を十分に行なって欠
陥のない鋼を得るためには０．１重敵襲以上き有させる
ことが必要である。しかし、帆４重量％を越えても脱酸
効果は飽和状態となるので、脱酸を目的とするためのＳ
ｉ含有量は、鋼の基本成分として、Ｏ０１〜０．４重量
％とした。In addition, in order to sufficiently deoxidize and obtain defect-free steel in steel manufacturing operations, it is necessary to have a Si content of 0.1 or more. However, even if the content exceeds 4% by weight, the deoxidizing effect reaches saturation, so S
The i content was O01 to 0.4% by weight as a basic component of the steel.
Ｍｎは鋼の焼入性を向上させ、強度ならびに靭性を向上
させるのに有効な元素であるが、０．１重量％未満では
その効果が得られない。また、■。５重量％ｅ越えると
造塊時の偏析によって強度にむらを生ずるおそれがある
ので、鋼の基本成分としてＯ０１〜１．５重量％とした
。Mn is an element effective in improving the hardenability of steel and improving its strength and toughness, but if it is less than 0.1% by weight, this effect cannot be obtained. Also ■. If it exceeds 5% by weight, there is a risk of uneven strength due to segregation during agglomeration, so the basic component of the steel is set to 1 to 1.5% by weight.
上記基本成分のほか、必要に応じて、Ｓｉ、Ｃｕ。In addition to the above basic components, Si and Cu may be added as necessary.
Ｎｉ 、 Ｃｒ 、 Ｍｏ 、 Ｗ 、 Ｃｏ 、 Ａ
ｔ、 Ｖ 、 Ｎｂ 、 Ｔｉ 。Ni, Cr, Mo, W, Co, A
t, V, Nb, Ti.
Ｚｒ ｌ Ｂ等の１種または２種以上を含有させること
もできる。It is also possible to contain one or more types of Zr l B and the like.
これらのうち、Ｓｌは鋼の焼もどし軟化抵抗性および耐
へたり性を増加させるために有効な元素であり、とくに
ばね鋼線材の場合には脱酸に必要な量を越えて含有させ
ることが望ましい。しかし、含有量が多すぎると著しく
脆くなるので、その上限を３重量％とするのが良い。Among these, Sl is an effective element for increasing the tempering softening resistance and settling resistance of steel, and especially in the case of spring steel wire rods, it should not be contained in an amount exceeding the amount required for deoxidation. desirable. However, if the content is too large, it becomes extremely brittle, so it is preferable to set the upper limit to 3% by weight.
Ｃｕは適量含有されている場合に析出硬化によって鋼の
強度を増すが、多すぎると熱間加工性を著しく害するの
で、その上限を０．５重量％とするのが良い。When Cu is contained in an appropriate amount, it increases the strength of the steel through precipitation hardening, but if it is too large, it significantly impairs hot workability, so the upper limit is preferably 0.5% by weight.
Ｎｉは鋼の靭性向上に役立つ元素であるが、多すぎると
オーステナイトが安定となり、耐力の不足をきたすので
、その上限を３重量％とするのが良い。Ni is an element that helps improve the toughness of steel, but if it is present too much, austenite becomes unstable and yield strength is insufficient, so the upper limit is preferably 3% by weight.
Ｃｒは鋼の焼入性および強度を高めるのに有効な元素で
あるが、多すぎると鋼を脆化させ、熱間加工性を悪化す
るので、その上限ｔｌ−２重１１％とするのが良い。Cr is an effective element for increasing the hardenability and strength of steel, but too much Cr makes the steel brittle and impairs hot workability, so the upper limit of tl-2 weight is 11%. good.
ＭＯは鋼の焼入性と強度を高めるのに有効な元素である
が、その効果は１．５重量％を越えると飽和状態となり
、それ以上含有させるとかえって鋼の熱間加工性を害す
るので、その上限全１．５重量饅とするのが良い。MO is an effective element for increasing the hardenability and strength of steel, but its effect reaches a saturated state when it exceeds 1.5% by weight, and containing more than that actually impairs the hot workability of steel. It is best to set the upper limit to a total of 1.5 weight rice cakes.
Ｗは鋼の強度を高めるのに有効な元素であるが、多すぎ
るとかえって熱間加工性を害するので、その上限を１．
５重量％とするのが良い。W is an effective element for increasing the strength of steel, but too much W impairs hot workability, so the upper limit is set at 1.
The content is preferably 5% by weight.
ＣＯは鋼の焼もどし軟化抵抗性を増大するのに有効な元
素であるが、２重量％を越えるとその効果は飽和状態と
なるので、その上限を２重１％とするのが良い。CO is an effective element for increasing the temper softening resistance of steel, but if it exceeds 2% by weight, its effect reaches a saturated state, so it is preferable to set the upper limit to 1% by weight.
さらに、ＡｔおよびＶ 、 Ｎｂ 、 Ｔｉ 、 Ｚｒ
は、圧延過程において結晶粒を微細化し、Ａｒ３変態で
生成するパーライトが微細化することにより、圧延後の
球状北都なましにおいて球状化を促進するのに有効な元
素である。このとき、Ａｔ含有量が多すぎるとアルミナ
系の大型介在物が形成されることによって疲労強度が低
下するので、その上限を０．０３重量％とするのが良い
。また、Ｖ 、 Ｎｂ 、 Ｔｉ 。Furthermore, At and V, Nb, Ti, Zr
is an effective element for promoting spheroidization in spherical Hokuto annealing after rolling by refining crystal grains in the rolling process and refining pearlite produced by Ar3 transformation. At this time, if the At content is too large, large alumina-based inclusions will be formed, resulting in a decrease in fatigue strength, so the upper limit is preferably set to 0.03% by weight. Also, V, Nb, Ti.
ｚｒを含有させる場合には上記した効果が飽和する範囲
内で含有させるのが良く、シたがって、Ｖ。When containing zr, it is preferable to contain it within a range in which the above-mentioned effects are saturated; therefore, V.
Ｎｂ 、 Ｔｉ 、 Ｚｒの上限を各々帆１重量％とし
、Ｖ十Ｎｂ ＋Ｔｉ ＋ Ｚｒ ＜０゜３重量％と規制
するのが良い。It is preferable to set the upper limits of Nb, Ti, and Zr to 1% by weight each, and to regulate the content to be 1% by weight (V+Nb+Ti+Zr<0°3% by weight).
次に、上記基本組成および必要に応じて適宜の添加元素
を含む鋼を用いて熱間圧延により鋼線材を製造するに際
しては、前記熱間圧延の一部または全部において、６０
０℃以上Ａｒ、変態点以下の温度で減面率３０％以上の
圧延を行ない、その後通常の方法により球状北都なまし
を行なう。Next, when manufacturing a steel wire rod by hot rolling using the steel containing the above basic composition and appropriate additive elements as necessary, 60%
Rolling is performed with an area reduction of 30% or more at a temperature of 0° C. or more in Ar and below the transformation point, and then spherical Hokuto annealing is performed by a conventional method.
ここで、鋼の熱間圧延の一部または全部において、６０
０℃以上Ａｒ３変態点以下の温度での圧延を行なうのは
、Ａｒ３変態点以下の温度で圧延を行なうことによって
、Ａｒ３変態で生じたパーライト中の炭化物を破壊し、
その後の球状北都なましにおいて球状化を促進させるよ
うにするためである。Here, in some or all of the hot rolling of steel, 60
The reason for rolling at a temperature of 0°C or higher and lower than the Ar3 transformation point is that by rolling at a temperature lower than the Ar3 transformation point, the carbides in the pearlite produced by the Ar3 transformation are destroyed;
This is to promote spheroidization in the subsequent rounding of the spherical Hokuto.
しかし、圧延温間が６θＯ℃よりも低くなると、圧延抵
抗が過大になるので、鋼組織を微細化するための熱間圧
延を６００℃以上Ａｒ、変態点以下の温度で行なう。な
お、このとき、減面率が３０チより小さいと、上記炭化
物を破壊する作用が十分に得られないので、減面率を３
０％以上とする。However, if the rolling temperature is lower than 6θO°C, the rolling resistance becomes excessive, so hot rolling for refining the steel structure is carried out at a temperature of 600°C or more in Ar and a temperature below the transformation point. At this time, if the area reduction rate is less than 30 inches, the effect of destroying the carbide cannot be obtained sufficiently, so the area reduction rate is set to 30 inches.
0% or more.
以下、実施例により説明する。Examples will be explained below.
〔実施例 １〕
表１に示す化学成分の鋼を高周波誘導炉によって溶製し
たのち造塊し、これらの鋼塊を同じく表１に示す加熱温
度に０口熱した後線材圧延を開始し、次いで仕上圧延工
程における温度および減面率を表１に示す値に調整し、
その後空冷して直径１３供の線素材を製造した。次に得
られた線素材に対し、７５０℃Ｘ ６ ｈｒの条件で球
状北都々ましを行なって鋼線材を製造した。次いで、各
線材から第１図および第２図に示す試験片１を切り出し
た。[Example 1] Steel having the chemical composition shown in Table 1 was melted in a high-frequency induction furnace and then formed into an ingot. After heating these steel ingots to the heating temperature also shown in Table 1, wire rod rolling was started, Next, the temperature and area reduction rate in the finish rolling process were adjusted to the values shown in Table 1,
Thereafter, it was air cooled to produce a wire material with a diameter of 13mm. Next, the obtained wire material was subjected to spherical drilling under the conditions of 750° C. for 6 hours to produce a steel wire material. Next, test pieces 1 shown in FIGS. 1 and 2 were cut out from each wire.
このときの試験片１の寸法は、直径（Ｄ）が７糟、長さ
１００瓢であり、切欠部４のθ＝６０°、Ｈ＝０．２調
、Ｒ＝Ｏ００２震であって、Ｌ＝８０−に設定して押圧
具２によるプレスノツチ曲げ試１１ｉ１ｒ行なった。こ
の結果を同じく表１に示す。The dimensions of the test piece 1 at this time are 7 mm in diameter (D), 100 mm in length, θ of the notch 4 = 60°, H = 0.2 scale, R = O002 scale, and L =80-, and a press notch bending test 11i1r was performed using the pressing tool 2. The results are also shown in Table 1.
表１において、供試材Ａ１〜４のように、加熱温度が１
１００℃以上でかつ仕上圧延温度がＡｒ３変態点（表１
の供試材のＡｒ３変態点は約７２０℃）よりも高い場合
には、仕上圧延減面率を３０％以上としたときでも、圧
延による組織の微細化を十分に行なうことができず、そ
の後の球状化部なましにおいて球状化が十分になされな
いので、破断たわみ量は小さい値となっている。また、
供試材Ａ５のように、圧延仕北温度ｋＡｒ３変態点以下
としても、仕上圧延減面率が１０％と小さい場合には、
Ａｒ３変態で生じた炭化物を十分に破壊することができ
ず、その後の球状化部な１しにおいて球状化が十分にな
されないので、破断たわみ量は小さい値となっている。In Table 1, as in sample materials A1 to A4, the heating temperature is 1.
100℃ or higher and the finish rolling temperature is Ar3 transformation point (Table 1
If the Ar3 transformation point of the sample material is higher than approximately 720°C, even if the finish rolling reduction rate is 30% or more, the structure cannot be refined sufficiently by rolling, and the subsequent In the rounding of the spheroidized part, the spheroidization is not sufficiently achieved, so the amount of deflection at break is a small value. Also,
Even if the rolling finish temperature kAr3 is below the transformation point, as in sample material A5, if the finish rolling area reduction is as small as 10%,
The amount of deflection at break is a small value because the carbide produced by the Ar3 transformation cannot be sufficiently destroyed and the subsequent spheroidization is not achieved in the spheroidized portion.
これに対して、供試材Ａ６のように、仕上圧延減面率を
３０係と大きくとった場合には、組織の微細化効果が十
分であってその陵の球状化部なましにおける組織の球状
化が良好であり、破断たわみ量を大きくすることができ
、靭性の改善をはかることができる。さらに、供試材屋
７，８のように、鋼中にＮｂ 、 Ｖを含む場合には、
これを含まない場合に比べてより組織の微細化をはかる
ことができ、破断たわみ量をより増大させることができ
る。On the other hand, when the finish rolling area reduction rate is as large as 30 factors, as in sample A6, the effect of refining the structure is sufficient, and the structure in the smoothing of the spheroidized part of the ridge is Spheroidization is good, the amount of deflection at break can be increased, and toughness can be improved. Furthermore, when Nb and V are included in the steel, as in sample materials 7 and 8,
Compared to the case where this is not included, the structure can be made finer and the amount of deflection at break can be further increased.
〔実施例 ２〕
表２に示す化学成分の鋼を実施例１の場合と同様に溶製
・造塊し、各鋼塊を同じく表２に示す加熱温度に加熱し
た後圧延を開始し、次いで仕上圧延工程における温度お
よび減面率を表２に示す値に各々調整し、その後空冷し
て直径１３欄の線素材を製造した。次に得られた線素材
に対し、７５０℃Ｘ ６ ｈｒの条件で球状化貌なまし
を行なって鋼線材を製造した。次いで、実施例１と同様
に試験片１を作成してプレスノツチ曲げ試験を行なった
。[Example 2] Steel having the chemical composition shown in Table 2 was melted and made into ingots in the same manner as in Example 1, and after each steel ingot was heated to the heating temperature also shown in Table 2, rolling was started. The temperature and area reduction rate in the finish rolling process were adjusted to the values shown in Table 2, and then air-cooled to produce a wire material with a diameter of 13 columns. Next, the obtained wire material was subjected to spheroidizing annealing at 750° C. for 6 hours to produce a steel wire material. Next, a test piece 1 was prepared in the same manner as in Example 1, and a press notch bending test was conducted.
この結果を同じく表２に示す。なお、表２に示す表２に
示すように、Ｓｌを約２重量％含有するばね鋼線材につ
いても上記表１に示す実施例１の場合とほぼ同様の結果
を得た。このほか、Ｃｒ。The results are also shown in Table 2. As shown in Table 2, almost the same results as in Example 1 shown in Table 1 above were obtained for the spring steel wire rod containing about 2% by weight of Sl. In addition, Cr.
Ｂを含む鋼線材についても実験したが、同様に良好な結
果が得られた。Experiments were also conducted using steel wire rods containing B, and similarly good results were obtained.
以ヒ説明してきたように、この発明によれば、Ｃ： ０
．４〜１．５重ｔ％、Ｓｉ ： ０．１〜０．４重量％
、Ｍｎ ： ０．１〜１．５重量％を基本組成とする鋼
を用いて熱間圧延により鋼線材を製造するに際し、前記
熱間圧延の一部または全部において、６００℃以上Ａｒ
、変態点以下の温度で減面率３０％以上の圧延を行ない
、その後球状北都なましを行なうようにしたから、Ａｒ
３変態で生じたラメラ状の炭化物を圧延によって良好に
破壊し、その後の球状化部なましにおける球状化を十分
に促進させて鋼線材の靭性を著しく高め、鋼線材の破断
たわみ量を大きくすることが可能であり、破断たわみ綾
の増大によって伸線時における折損の発生を低減するこ
とができるという非常にすぐれた効果を有する。As explained below, according to this invention, C: 0
．． 4 to 1.5 wt%, Si: 0.1 to 0.4 wt%
, Mn: When manufacturing a steel wire rod by hot rolling using steel having a basic composition of 0.1 to 1.5% by weight, Ar
, the Ar
The lamellar carbide produced by the 3-transformation is effectively destroyed by rolling, and the subsequent annealing of the spheroidized part sufficiently promotes spheroidization, thereby significantly increasing the toughness of the steel wire and increasing the amount of fracture deflection of the steel wire. This has the very excellent effect of reducing the occurrence of breakage during wire drawing by increasing the deflection at break.
第１図および第２図は鋼線材の靭性評価に用いたプレス
ノツチ曲げ試験方法の実施状況を示す説明図および試験
片の切欠部拡大説明図である。
特許出願人 大同特殊鋼株式会社
第１図FIGS. 1 and 2 are an explanatory diagram showing the implementation status of the press notch bending test method used for evaluating the toughness of steel wire rods, and an enlarged explanatory diagram of the notch of the test piece. Patent applicant: Daido Steel Co., Ltd. Figure 1
Claims (1)
〜帆４１０、Ｍｎ ： ０．１〜１．５重量％を基本組
成とする鋼を用いて熱間圧延により鋼線材を製造するに
際し、６００℃以上Ａｒ、ｌ変態点以下の温度で減面率
３０％以上の圧延を行ない、その後球状化焼なましを行
なうことを特徴とする鋼線材の製造方法。(1) C: 0.4-1.5% by weight, si: 0.1
~Sail 410, Mn: When manufacturing a steel wire rod by hot rolling using steel with a basic composition of 0.1 to 1.5% by weight, the area reduction rate at a temperature of 600°C or higher and Ar and l transformation points or lower 1. A method for producing a steel wire rod, which comprises rolling 30% or more and then spheroidizing annealing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10124481A JPS583919A (en) | 1981-07-01 | 1981-07-01 | Manufacture of steel wire rod |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10124481A JPS583919A (en) | 1981-07-01 | 1981-07-01 | Manufacture of steel wire rod |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS583919A true JPS583919A (en) | 1983-01-10 |
Family
ID=14295488
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10124481A Pending JPS583919A (en) | 1981-07-01 | 1981-07-01 | Manufacture of steel wire rod |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS583919A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5827926A (en) * | 1981-08-12 | 1983-02-18 | Nippon Steel Corp | Manufacture of wire rod having spheroidal structure |
| JPS59126721A (en) * | 1983-01-11 | 1984-07-21 | Kawasaki Steel Corp | Manufacture of steel material for rapid spheroidizing |
| US4604145A (en) * | 1984-01-13 | 1986-08-05 | Sumitomo Metal Industries, Ltd. | Process for production of steel bar or steel wire having an improved spheroidal structure of cementite |
-
1981
- 1981-07-01 JP JP10124481A patent/JPS583919A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5827926A (en) * | 1981-08-12 | 1983-02-18 | Nippon Steel Corp | Manufacture of wire rod having spheroidal structure |
| JPS59126721A (en) * | 1983-01-11 | 1984-07-21 | Kawasaki Steel Corp | Manufacture of steel material for rapid spheroidizing |
| US4604145A (en) * | 1984-01-13 | 1986-08-05 | Sumitomo Metal Industries, Ltd. | Process for production of steel bar or steel wire having an improved spheroidal structure of cementite |
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