JPS583929A - Manufacture of steel wire rod - Google Patents
Manufacture of steel wire rodInfo
- Publication number
- JPS583929A JPS583929A JP10124581A JP10124581A JPS583929A JP S583929 A JPS583929 A JP S583929A JP 10124581 A JP10124581 A JP 10124581A JP 10124581 A JP10124581 A JP 10124581A JP S583929 A JPS583929 A JP S583929A
- Authority
- JP
- Japan
- Prior art keywords
- steel wire
- steel
- wire rod
- weight
- rod
- 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
- 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】
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、低炭素鋼線材から中・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、鋼塊または鋼片を熱間圧延
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
疵全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剣されること
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、鋼線製造コストが上昇するという問題を有していた
。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
りこの桃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
はあまり提案されていない。Then, this steel wire rod is usually drawn into a steel wire by a wire drawing process. However, in the above wire drawing process,
Minute surface flaws that occur during hot rolling or during the transportation of wire rods can lead to breakage, and the occurrence of such breakage significantly reduces the efficiency of the wire drawing process. Conventionally, countermeasures against the above-mentioned surface flaws have been taken, such as inspecting the entire length using inspection methods such as eddy current flaw detection, and removing surface flaws using surface solvents, surface peeling, etc. However, it is difficult to completely remove minute surface flaws. In addition, if such measures are taken, steel wire manufacturing costs will be reduced because wire drawing operations will have to be temporarily interrupted when surface flaws are discovered, and yields will decrease due to surface solvents. It had the problem of rising. Therefore, there has been a desire to develop a steel wire rod that is less prone to breakage during wire drawing even if the degree of surface flaws is the same. Few methods have been proposed to reduce the occurrence of wire breakage during wire drawing in the presence of 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は抑圧其、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、−卜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 paying attention to the conventional problems mentioned above.As mentioned above, a steel wire rod with a larger breaking deflection was developed, and this steel wire rod was drawn into a steel wire. The purpose is to reduce the occurrence of breakage during the process.
この発明は、C: 0.4〜1.5ifチ、5l−0,
1〜0.4重量饅、Mn : 0.1〜1.5重量%を
基本組成とし、さらに必豊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、
前記熱間圧延における最終ロール通過後の鋼線素材の温
度および冷却速度を調節することによって、(この際必
要に応じて上記最終ロール通過後の鋼線素材を変態温7
1j以上に再加熱してその温度および冷却速度を調節す
ることによって、)当該鋼線素材の常温での金属組織を
面積率総和でフェライト+パーライトが90チ以下とな
るように調整し、その後球状北都な丼しを行なうように
したことを特徴としている。This invention provides C: 0.4 to 1.5if, 5l-0,
When manufacturing a steel wire rod by hot rolling using steel with a basic composition of 1 to 0.4 weight %, Mn: 0.1 to 1.5 weight %, and further containing appropriate alloy components according to demand. ,
By adjusting the temperature and cooling rate of the steel wire material after passing through the final roll in the hot rolling (at this time, if necessary, the steel wire material after passing through the final roll may be heated to a transformation temperature of 7.
By reheating to 1J or more and adjusting the temperature and cooling rate, the metal structure of the steel wire material at room temperature is adjusted so that the total area ratio of ferrite + pearlite is 90J or less, and then spherical It is unique in that it is made to resemble a bowl of rice from the northern capital.
この発明に係る鋼線材は、C: 0.4〜1.5重量%
、81 : 0.1〜0.4重量俤、Mn : 0.1
〜1.5重t%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 contains C: 0.4 to 1.5% by weight.
, 81: 0.1-0.4 weight, Mn: 0.1
The basic composition is ~1.5wt%, and further contains appropriate alloying elements as necessary, such as ordinary carbon steel wire rods (hard steel wire rods, spring steel wire rods, carbon steel wire rods 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重量%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重量%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 the content exceeds 5% by weight, a large amount of reticular cementite will be produced and the toughness will be significantly impaired, so the content was 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001重量%以上含有させる
ことが必要である。しかし、004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
Si含有量は、鋼の基本成分として、0.1〜0.4重
量%とした。Further, in order to sufficiently deoxidize and obtain defect-free steel in steel manufacturing operations, it is necessary to contain Si in an amount of 0.01% by weight or more. However, even if it exceeds 0.004% by weight, the deoxidizing effect reaches a saturated state, so the Si content for the purpose of deoxidizing is set to 0.1 to 0.4% by weight as a basic component of 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
その効果が得られたい。また、1.5重量%を越えると
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0.1〜1.5重量%とした
。Mn is an effective element for improving the hardenability of steel, as well as improving its strength and toughness, but the effect cannot be obtained if it is less than 0.1% by weight. Moreover, if it exceeds 1.5% by weight, there is a risk of uneven strength due to segregation during agglomeration, so the basic component of the steel is set at 0.1 to 1.5% by weight.
一ヒ紀基本成分のほか、必要に応じて、81.Cu。In addition to the basic ingredients, 81. Cu.
Ni 、 Cr r Mo 、 W 、(:o 、 A
t+ V * Nb + Ti 、 Zr tB等の1
種または2種以上を含有させることもできる。Ni, Cr Mo, W, (:o, A
t+V*Nb+Ti, Zr tB, etc. 1
A species or two or more species can also be included.
これらのうち、Siは鋼の焼もどし軟化抵抗性および耐
へたす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t%とするのが良い。Among these, Si is an effective element for increasing the tempering softening resistance and flattening resistance of steel, and especially in the case of spring steel wire rods, Si should be contained in an amount exceeding the amount required for deoxidation. is desirable. However, if the content is too large, it becomes extremely brittle, so it is preferable to set the upper limit to 3 weight t%.
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f%とするのが良い。When Cu is contained in an appropriate amount, it increases the strength of the steel by precipitation hardening, but if it is too large, it significantly impairs hot workability, so the upper limit is preferably set to 0.5% by weight.
N1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。N1 is an element that helps improve the toughness of steel, but if it is too large, austenite will become unstable and yield strength will be insufficient, so the upper limit should be 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、その上限を2重量%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 is preferably 2% by weight.
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、その上限を1.5重量%とするのが良い。Mo is an effective element for increasing the hardenability and strength of steel, but its effect reaches saturation when it exceeds 1.5% by weight, and if it is contained more than that, it will actually impair the hot workability of steel. , the upper limit is preferably 1.5% by weight.
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重量%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 saturation, so the upper limit is preferably 2% by weight.
さらに、kt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
球状化焼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゜033重量%するのが良い
。また、V、Nb。Furthermore, kt and V, Nb, Ti, Zr
is an effective element for promoting spheroidization in the spheroidizing annealing after rolling by refining crystal grains during 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 it is preferable to set the upper limit to 0.033% by weight. Also, V, Nb.
’[’t 、 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 、 Nb 、 Ti 、 Zrの上限を各々0.1
重量%とし、V+Nb+Ti +Zr<0.3重量%と
規制するのが良い。'['t, When containing Zr, it is best to contain it within a range where the above-mentioned effects are saturated; therefore,
The upper limits of V, Nb, Ti, and Zr are each set to 0.1
% by weight, and preferably regulates 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、前記熱間圧延における最終ロール通過後の鋼線
素材の温度および冷却速度を調節することによって、当
該鋼線素材の常温での金属組織を面積率総和でフェライ
ト士パーライトが90%以下となるように調整し、その
後球状北都なましを行なうようにしたのは、鋼線素材の
常温での金属組織が、面積率Wallにおいて、フェラ
イト士パーライトが90%以下で且つマルテンサイト、
ベイナイト、残留オーステナイトの1種または2種以上
が10%以上であるようにしたものに対して、次に球状
化焼なまし全行なうと、鋼線材の靭性を著しく改善する
ことができるようになるためである。このとき、フェラ
イト士パーライトが90%以上で且つマルテンサイト、
ベイナイト、残留オーステナイトの1種または2種以上
が10チ以下であると、上記靭性改善に対する効果はあ
まり見られない。また、熱間圧延における最終ロール通
過後の鋼線素材のm1fおよび冷却速度を調節して当該
鋼線素材の常温での金属組織を面積諸相でフェライト+
パーライト90チ以下とするに際して、必要に応じて前
記最終ロール通過後の鋼線素材をAca変態温変以上に
再加熱し、その後冷却速度を調節することもでき、同様
に球状化焼なまし後における鋼線材の靭性を著しく改善
することができる。Next, when producing a steel wire rod by hot rolling using steel containing the above basic composition and appropriate additive elements as necessary, the temperature and cooling of the steel wire material after passing through the final roll in the hot rolling and the cooling By adjusting the speed, the metal structure of the steel wire material at room temperature was adjusted so that the total area ratio of ferrite and pearlite was 90% or less, and then spherical Hokuto annealing was performed. The metal structure of the wire material at room temperature is 90% or less of ferrite and pearlite in the area ratio Wall, and martensite,
If one or more of bainite and retained austenite is contained in a proportion of 10% or more, then the toughness of the steel wire rod can be significantly improved by performing spheroidizing annealing. It's for a reason. At this time, ferrite pearlite is 90% or more, martensite,
When the amount of one or more of bainite and retained austenite is 10 or less, the above-mentioned effect on improving the toughness is not seen much. In addition, by adjusting the m1f and cooling rate of the steel wire material after passing through the final roll during hot rolling, the metal structure of the steel wire material at room temperature can be changed to ferrite +
In order to reduce the pearlite to 90 cm or less, if necessary, the steel wire material after passing through the final roll may be reheated to a temperature higher than the Aca transformation temperature, and then the cooling rate may be adjusted. The toughness of steel wire can be significantly improved.
次に、実施例について説明する。Next, examples will be described.
〔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
度に加熱した後圧延を開始し、次いで仕上圧延温度な表
1に示す如く設定して鋼線素材が最終ロールを通過した
のちの温度および冷却速度を調節し、各鋼線素材の常温
での金属組織が同じく表1に示す如くになるようにした
。次に得られた鋼線素材に対し、750℃X 6 hr
の条件で球状化焼なましを行なって鋼線材を製造した。[Example 1] Steel having the chemical composition shown in Table 1 is 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, rolling is started, and then finish rolling is carried out. The temperature was set as shown in Table 1, and the temperature and cooling rate after the steel wire material passed through the final roll were adjusted so that the metal structure of each steel wire material at room temperature became as shown in Table 1. did. Next, the obtained steel wire material was heated at 750℃ for 6 hours.
A steel wire rod was manufactured by performing spheroidizing annealing under the following conditions.
次いで、各鋼線材から第1図および第2図に示す試験片
1を切り出した。このときの試験片1の寸法は、直径(
I))が7浦、長さ100w+mであり、切欠部4のθ
=60°、H= 0.2 wn XR= 0.02 +
nmであって、L−8011III+に設定して抑圧具
2によるプレスノツチ曲げ試験を行なった。この結果を
同じく表1に示す。Next, test pieces 1 shown in FIGS. 1 and 2 were cut out from each steel wire rod. The dimensions of test piece 1 at this time are the diameter (
I)) is 7 ura, length 100w+m, and θ of notch 4
=60°, H=0.2 wn XR=0.02 +
nm, and was set to L-8011III+, and a press notch bending test was conducted using the suppressor 2. The results are also shown in Table 1.
表1において、供試材AIのように、最終ロールを通過
した後の鋼線素材の常温での金属組織がフェライト+パ
ーライト100 %である場合には、球状北都なまし後
の鋼線材の靭性がかなり低く、破断たわみ量も小さいも
のとなっている。また、供試材A2のように、最終ロー
ルを通過した後の鋼線素材の冷却速度を若干高めてフェ
ライト+パーライトの朧率総和を95%程度に少なくし
た場合には、破断たわみ量も若干増大しているが、この
程度の靭性では伸線時しこ折損を生ずるおそれが十分に
ある。これに対して、供試材53〜6のように、最終ロ
ールを通過した後の鋼線材の冷却速度をさらに高めてフ
ェライト+パーライトの面積率総和が90%以下となる
ようにし、マルテンサイト、ベイナイト、残留オーステ
ナイトの1種または2種以−トの面積率総和を相対的に
高め、その後球状北都なましを行なった場合には、破断
たわみ量もかなり多く、靭性にすぐれているものである
ため、伸線時に折損を生ずることがなくAる。さらに、
鋼中にNbまたはVを適量含有させたものでは、鋼線材
の靭性をさらに高めることができ、供試材A8の場合に
は本実施例におけるプレスノツチ曲げ試験において破断
を生じなかった。In Table 1, when the metal structure of the steel wire material at room temperature after passing through the final roll is 100% ferrite + pearlite, as in sample material AI, the toughness of the steel wire material after spherical Hokuto annealing is is quite low, and the amount of deflection at break is also small. In addition, when the cooling rate of the steel wire material after passing through the final roll is slightly increased to reduce the sum of the haze ratio of ferrite + pearlite to about 95%, as in sample material A2, the amount of fracture deflection is also slightly increased. However, with this level of toughness, there is a sufficient risk that breakage will occur during wire drawing. On the other hand, as in specimens 53 to 6, the cooling rate of the steel wire rod after passing through the final roll is further increased so that the total area ratio of ferrite + pearlite is 90% or less, and martensite, If the total area ratio of one or more types of bainite and retained austenite is relatively increased, and then spherical Hokuto annealing is performed, the amount of deflection at break is considerably large, resulting in excellent toughness. Therefore, no breakage occurs during wire drawing. moreover,
When the steel contains an appropriate amount of Nb or V, the toughness of the steel wire can be further improved, and in the case of sample material A8, no breakage occurred in the press notch bending test in this example.
〔実施例 2〕
表2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、次いで仕上圧延温度を表
2に示す如く設定して鋼線素材が最終1ゴールを通過し
たのちの温度および冷却速度を調節し、各鋼線素材の常
温での金属組織が同じく表2に示す如くになるようにし
た。次に得られた鋼線素材に対し、750℃X6hrの
条件で球状北都々ましを行なって鋼線材を製造した。[Example 2] Steel having the chemical composition shown in Table 2 was melted in a high-frequency induction furnace and then formed into ingots. After heating these steel ingots to the heating temperature also shown in Table 2, rolling was started, and then finish rolling was carried out. The temperature was set as shown in Table 2, and the temperature and cooling rate were adjusted after the steel wire material passed the final goal, so that the metal structure of each steel wire material at room temperature became as shown in Table 2. I made it. Next, the obtained steel wire material was subjected to spherical drilling under the conditions of 750° C. for 6 hours to produce a steel wire rod.
次いで各鋼線材から前記実施例1の場合と同じ試験片1
を作成してプレスノツチ曲げ試験を行なった。この結果
を同じく表2に示す。Next, the same test piece 1 as in Example 1 was prepared from each steel wire.
A press notch bending test was conducted using the press notch bending test. The results are also shown in Table 2.
表2に示すように、Siを約2重量係含有するばね鋼線
材についても前記実施例1の場合とほぼ同様の結果が得
られた。このほか、Cr、Bl: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。As shown in Table 2, almost the same results as in Example 1 were obtained for the spring steel wire containing about 2% Si by weight. In addition, experiments were also conducted on steel wire rods containing Cr and Bl, and similarly good results were obtained.
〔実施例 3〕
表3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3に示す加熱温
度に加熱した後圧延を開始し、次いで仕上圧延温度全表
3に示す如く設定して鋼線素材を最終ロールに通過させ
た後、各鋼線素材を同じく表3に示す再抽熱温IWに加
熱してその後の冷却速IWを調節し、各鋼線素材の常温
での金属組織が同じく表3に示す如くになるようにした
。次に得られた鋼線素材に苅して、750℃X 6 h
rの条件で球状北都々ましを行なって鋼線材を製造した
。次いで各鋼線材から前記実施例1の場合ど同じ試験片
1を作成してプレスノツチ曲げ試験を行なった。この結
果を同じく表3に示す。[Example 3] Steel having the chemical composition shown in Table 3 was melted in a high-frequency induction furnace and then formed into ingots. After heating these steel ingots to the heating temperature also shown in Table 3, rolling was started, and then finish rolling was carried out. After setting the temperature as shown in Table 3 and passing the steel wire material through the final roll, each steel wire material was heated to the re-extraction temperature IW also shown in Table 3, and the subsequent cooling rate IW was adjusted, The metal structure of each steel wire material at room temperature was made to be as shown in Table 3. Next, the obtained steel wire material was heated at 750°C for 6 hours.
A steel wire rod was manufactured by performing spherical cross-polishing under the conditions of r. Next, the same test piece 1 as in Example 1 was prepared from each steel wire and subjected to a press notch bending test. The results are also shown in Table 3.
表3に示すように、最終ロール通過後の鋼線素材をAO
3変態温度以上に再加熱した場合にも前記実施例とほぼ
同様の結果を得ることができた。As shown in Table 3, the steel wire material after passing through the final roll is
Even when the material was reheated to a temperature higher than 3 transformation temperature, almost the same results as in the above example could be obtained.
以上説明してきたように、この発明によれば、C: 0
.4〜1.5重付チ、st : o、t〜0゜4重量%
、Mn : O01〜1.5成葉%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、前記熱間圧延にお
ける最終ロール通過後の鋼線素材の温度および冷却速度
を調節することによって、この際必要に応じて上記最終
ロール通過後の鋼線素材を変態温度以上に再加熱してそ
の温度および冷却速度を調節することによって、当該鋼
線素材の常温での金属組織を面積率総和でフェライト+
パーライト90%以下となるようにし、その後通常の方
法によって球状北都なましを行なうようにしたから、球
状北都なまし後における鋼線材の靭性を著しく高めるこ
とができ、鋼線材の破断たわみ量をかなり増大させるこ
とが可能であり、破断たわみ量の増大によって伸線時に
おける折損の発生を著しく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 above, according to this invention, C: 0
.. 4 to 1.5 weight, st: o, t to 0° 4% by weight
, Mn: When manufacturing a steel wire rod by hot rolling using a steel having a basic composition of O01 to 1.5% and further containing appropriate alloy components as necessary, the final roll passing in the hot rolling By adjusting the temperature and cooling rate of the subsequent steel wire material, at this time, if necessary, by reheating the steel wire material after passing through the final roll above the transformation temperature and adjusting the temperature and cooling rate. , the metal structure of the steel wire material at room temperature is ferrite +
Since the pearlite content is 90% or less, and then spherical Hokuto annealing is performed using the usual method, the toughness of the steel wire rod after spherical Hokuto annealing can be significantly increased, and the amount of fracture deflection of the steel wire rod can be significantly reduced. It has the very excellent effect of significantly reducing the occurrence of breakage during wire drawing by increasing the amount of breakage deflection.
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.
Claims (1)
0.1〜0.4重量%、■二0.1〜1.5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、前記熱間圧延における最終ロール通過後
の鋼線素材の温度および冷却速度を調節することによっ
て当該鋼線素材の常温での金属組織を面積率総和でフェ
ライト+パーライトが90%以下となるように調整し、
その後球状化焼なましを行なうことf特徴とする鋼線材
の製造方法。(1) C: 0.4-1.5iiiL%, St:
When manufacturing a steel wire rod by hot rolling using steel having a basic composition of 0.1 to 0.4% by weight, By adjusting the temperature and cooling rate of the subsequent steel wire material, the metal structure of the steel wire material at room temperature is adjusted so that the total area ratio of ferrite + pearlite is 90% or less,
A method for producing a steel wire rod, characterized in that a spheroidizing annealing process is performed thereafter.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10124581A JPS583929A (en) | 1981-07-01 | 1981-07-01 | Manufacture of steel wire rod |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10124581A JPS583929A (en) | 1981-07-01 | 1981-07-01 | Manufacture of steel wire rod |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS583929A true JPS583929A (en) | 1983-01-10 |
Family
ID=14295515
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP10124581A Pending JPS583929A (en) | 1981-07-01 | 1981-07-01 | Manufacture of steel wire rod |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS583929A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100384629B1 (en) * | 1998-10-16 | 2003-08-19 | 주식회사 포스코 | A high strength wire-rod having superior wire drawability and a method therefor |
CN109963960A (en) * | 2016-10-28 | 2019-07-02 | 日本制铁株式会社 | Wire rod and its manufacturing method |
-
1981
- 1981-07-01 JP JP10124581A patent/JPS583929A/en active Pending
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100384629B1 (en) * | 1998-10-16 | 2003-08-19 | 주식회사 포스코 | A high strength wire-rod having superior wire drawability and a method therefor |
CN109963960A (en) * | 2016-10-28 | 2019-07-02 | 日本制铁株式会社 | Wire rod and its manufacturing method |
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