JPH0751736B2 - Rolled wire rod with excellent machinability and method for producing the same - Google Patents
Rolled wire rod with excellent machinability and method for producing the sameInfo
- Publication number
- JPH0751736B2 JPH0751736B2 JP16988288A JP16988288A JPH0751736B2 JP H0751736 B2 JPH0751736 B2 JP H0751736B2 JP 16988288 A JP16988288 A JP 16988288A JP 16988288 A JP16988288 A JP 16988288A JP H0751736 B2 JPH0751736 B2 JP H0751736B2
- Authority
- JP
- Japan
- Prior art keywords
- steel
- less
- wire rod
- machinability
- rolled wire
- 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.)
- Expired - Lifetime
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 13
- 229910000831 Steel Inorganic materials 0.000 claims description 80
- 239000010959 steel Substances 0.000 claims description 80
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 16
- 230000009466 transformation Effects 0.000 claims description 12
- 229910052717 sulfur Inorganic materials 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 8
- 229910052745 lead Inorganic materials 0.000 claims description 8
- 238000005096 rolling process Methods 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 6
- 238000005520 cutting process Methods 0.000 description 13
- 239000000463 material Substances 0.000 description 11
- 239000013078 crystal Substances 0.000 description 7
- 238000005498 polishing Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000004804 winding Methods 0.000 description 4
- 229910000915 Free machining steel Inorganic materials 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000003746 surface roughness Effects 0.000 description 3
- 238000010622 cold drawing Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052714 tellurium Inorganic materials 0.000 description 2
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 102200029231 rs11551768 Human genes 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)
Description
【発明の詳細な説明】 産業上の利用分野 本発明は、被削性にすぐれる圧延線材棒鋼及びその製造
方法に関する。Description: TECHNICAL FIELD The present invention relates to a rolled wire rod steel having excellent machinability and a method for producing the same.
従来の技術 磨棒用鋼として用いられる切削用圧延線材棒鋼は、引抜
加工後、自動車部品、建設機械部品、油圧機器部品、装
飾部品、電気部品、事務機器部品等、多岐にわたる部品
の製造に広く用いられている。かかる分野においては、
特に、近年、高精度化や製造費用の低減を目的として、
被削性にすぐれる鋼材が要望されている。Conventional technology Rolled steel rod steel for cutting, which is used as steel for polished rods, is widely used in the manufacture of various parts such as automobile parts, construction machine parts, hydraulic equipment parts, decorative parts, electric parts, office equipment parts after drawing. It is used. In this area,
Especially in recent years, for the purpose of high precision and reduction of manufacturing cost,
There is a demand for steel materials with excellent machinability.
従来、被削性を有する鋼材は、Ｓ、Pb、Ca、Bi、Te等の
所謂快削性付与元素を含有しており、例えば、SUM24V鋼
は、0.3％のＳと0.20％のPbを含有しており、S45CL鋼
は、0.2％のPbを含有している。また、例えば、特開昭5
9−118861号公報には、Pb、Bi、Te等を添加してなるフ
ェライト・パーライト組織を有する快削鋼が記載されて
いる。Conventionally, steel materials having machinability contain so-called free-machining-providing elements such as S, Pb, Ca, Bi, and Te. For example, SUM24V steel contains 0.3% S and 0.20% Pb. The S45CL steel contains 0.2% Pb. In addition, for example, Japanese Patent Laid-Open No.
Japanese Patent Laid-Open No. 9-118861 describes a free-cutting steel having a ferrite-pearlite structure formed by adding Pb, Bi, Te and the like.
しかしながら、このように、快削性元素を鋼に添加する
ことによつて、鋼の被削性を高めるときは、場合によつ
ては、鋼材の機械的性質が劣化して、用途が限られるこ
ととなつたり、或いは上記のような快削性元素を鋼に添
加するには、特別の手段を必要とし、また、添加する快
削性元素によつては、高価であるために、鋼材の製造費
用を著しく高めることとなる。However, when the machinability of the steel is increased by adding the free-cutting element to the steel in this way, the mechanical properties of the steel material deteriorate in some cases, and the application is limited. In addition, or in order to add the above-mentioned free-cutting elements to steel, special means is required, and the added free-cutting elements are expensive, so that This will significantly increase the manufacturing cost.
発明が解決しようとする課題 本発明者らは、磨棒用鋼として用いられる被削性にすぐ
れる従来の鋼材及びその製造における上記した種々の問
題を解決するために、圧延鋼材において、被削性に及ぼ
す熱処理組織と結晶粒度との関係について鋭意研究した
結果、従来、磨棒用鋼における結晶粒度番号は、通常、
８〜12程度であり、例えば、前記特開昭59−118861号公
報による快削鋼においては、結晶粒度番号が９以上であ
ることが必要とされているところ、本発明者らは、圧延
鋼材の結晶粒度番号を所定値以上に大きくすることによ
つて、特に前述したような快削性元素を鋼に添加するこ
となしに、被削性にすぐれる圧延線材棒鋼を得ることが
でき、特に、磨棒用鋼は、その切削時に圧延鋼材の結晶
粒が保持されるので、上記本発明による鋼材は、磨棒用
鋼としての用途に好適に用いることができることを見出
した。DISCLOSURE OF THE INVENTION Problems to be Solved by the Invention In order to solve the above-mentioned various problems in the conventional steel material used as a steel for a polishing rod and having excellent machinability, and the above-mentioned various problems, in the rolled steel material, As a result of diligent research on the relationship between the heat treatment structure and the grain size on the property, conventionally, the grain size number in the steel for the polishing rod is usually
It is about 8 to 12, and for example, in the free-cutting steel according to JP-A-59-118861, the grain size number is required to be 9 or more. By increasing the grain size number of the above to a predetermined value or more, it is possible to obtain a rolled wire rod steel excellent in machinability, in particular, without adding a free-cutting element as described above to steel, It has been found that the steel for a polishing rod retains the crystal grains of the rolled steel during cutting, and thus the steel according to the present invention can be suitably used for the application as a steel for a polishing rod.
更に、本発明者らは、快削性元素を含む快削鋼について
も、圧延鋼材の結晶粒度番号を所定値以上に大きくする
ことによつて、一層、被削性にすぐれる圧延線材棒鋼を
得ることができることを見出した。本発明は、かかる知
見に基づいてなされたものである。Further, the inventors of the present invention, even for free-cutting steel containing a free-cutting element, by increasing the grain size number of the rolled steel to a predetermined value or more, a rolled wire rod steel further excellent in machinability is obtained. Found that you can get. The present invention has been made based on such findings.
従つて、本発明は、一般には、被削性にすぐれる圧延線
材棒鋼及びその製造方法を提供することを目的とし、特
に、冷間引抜加工に供される被削性にすぐれる磨棒用鋼
を提供することを目的とする。Therefore, the present invention is generally intended to provide a rolled wire rod steel having excellent machinability and a method for producing the same, and particularly for a polishing rod having excellent machinability that is subjected to cold drawing. Intended to provide steel.
課題を解決するための手段 本発明による被削性にすぐれる圧延線材棒鋼は、重量％
で C 0.04〜0.55％、 Si 0.40％以下、 Mn 0.30〜２％、 S 0.040％以下、 残部鉄及び不可避的不純物よりなる圧延線材棒鋼であつ
て、結晶粒度番号が6.5以下であることを特徴とする。Means for Solving the Problems The rolled wire rod steel excellent in machinability according to the present invention has a weight%
And C 0.04 to 0.55%, Si 0.40% or less, Mn 0.30 to 2%, S 0.040% or less, and a rolled wire rod steel consisting of the balance iron and unavoidable impurities, characterized by having a grain size number of 6.5 or less. To do.
本発明による被削性にすぐれる圧延線材棒鋼は、上記元
素に加えて、 S 0.04〜0.4％、及び Pb 0.05〜0.4％ よりなる群から選ばれる少なくとも１種の元素を含有す
ることができる。The rolled wire rod steel having excellent machinability according to the present invention may contain at least one element selected from the group consisting of S 0.04 to 0.4% and Pb 0.05 to 0.4% in addition to the above elements.
本発明によるかかる被削性にすぐれる圧延線材棒鋼の製
造方法は、上記した化学成分を有する鋼片を （イ）圧延終了後、650〜1100℃の範囲の温度で巻き取
るか、又は （ロ）A3変態点からA1変態点を通過するときまでの平均
冷却速度を0.2℃／秒以下として、結晶粒度番号が6.5以
下である圧延線材棒鋼を得ることを特徴とする。The method for producing a rolled wire rod steel bar having excellent machinability according to the present invention is (1) after completion of rolling, rolling up a steel slab having the above-mentioned chemical composition at a temperature in the range of 650 to 1100 ° C, or (b) ) average cooling rate from a 3 transformation point until it passes through the a 1 transformation point as follows 0.2 ° C. / sec, the crystal grain size number is equal to or obtaining a rolled wire rod steel bar is 6.5 or less.
先ず、本発明による圧延線材棒鋼における化学成分の限
定理由について説明する。First, the reasons for limiting the chemical components in the rolled wire rod steel according to the present invention will be described.
Ｃは、本発明鋼に機械的強度を与えるための元素であつ
て、そのために少なくとも0.04％の添加を必要とする。
しかし、過多に添加するときは、鋼の硬度を適正な範囲
を越えて高くして、被削性を劣化させるのみならず、靭
性をも劣化させ、更には、本発明に従つて、鋼材の結晶
粒を大きくくしても、被削性を大幅に向上させることが
できないので、添加量の上限を0.55％とする。C is an element for imparting mechanical strength to the steel of the present invention, and for that purpose, addition of at least 0.04% is required.
However, when added in excess, the hardness of the steel is increased beyond the proper range to deteriorate not only machinability but also toughness, and further, according to the present invention, Even if the crystal grains are made large, the machinability cannot be significantly improved, so the upper limit of the addition amount is made 0.55%.
Siは、過多に添加するときは、硬度を適正な範囲を越え
て高くして、被削性や靭性を劣化させ、更には、前記し
たように、鋼材の結晶粒を大きくしても、被削性を大幅
に向上させることができないので、添加量の上限を0.40
％とする。When Si is excessively added, the hardness is increased beyond the appropriate range to deteriorate the machinability and toughness, and as described above, even if the crystal grains of the steel material are increased, Since the machinability cannot be significantly improved, the upper limit of the addition amount is 0.40.
%.
Mnは、脱酸作用と共に、MnSを形成して、FeSの生成を抑
制し、鋼の熱間加工性を改善し、更に、焼入れ性を向上
させて、鋼の強度と靭性を改善するために添加される。
しかし、Mnも、過多に添加するときは、鋼の硬度を不必
要に高くして、被削性を劣化させるのみならず、靭性を
も劣化させ、更に、本発明による被削性の改善効果を妨
げるので、添加量の上限を２％とする。Mn forms MnS together with deoxidizing action, suppresses FeS generation, improves hot workability of steel, and further improves hardenability to improve strength and toughness of steel. Is added.
However, when Mn is also added in an excessive amount, the hardness of the steel is unnecessarily increased to deteriorate not only the machinability but also the toughness, and further, the machinability improving effect of the present invention. Therefore, the upper limit of the added amount is set to 2%.
Ｓは、被削性を向上させる元素ではあるが、0.4％を越
えて過多に添加するときは、機械的強度の劣化が著し
く、前述したような部品の製造に用いることができな
い。本発明においては、快削性元素を添加せずして、被
削性にすぐれる圧延線材棒鋼とするときは、Ｓ量は0.04
0％以下とし、Ｓを快削性元素として添加するときは、
上記理由によつて、その添加量は、0.4％以下とする。S is an element that improves the machinability, but if it is added in excess of 0.4%, the mechanical strength is significantly deteriorated and it cannot be used for the production of the above-mentioned parts. In the present invention, when the rolled wire rod steel having excellent machinability is prepared without adding a free-machining element, the S content is 0.04.
When the content is 0% or less and S is added as a free-cutting element,
For the above reason, the added amount is 0.4% or less.
本発明による線材圧延棒鋼には、その被削性を一層改善
するために、上記したように、Ｓと共に、又は単独に
て、Pbを0.05〜0.4％の範囲で添加することができる。In order to further improve the machinability of the rolled wire rod steel according to the present invention, Pb can be added in the range of 0.05 to 0.4% together with S or alone as described above.
本発明による鋼は、上述したような化学成分を有すると
共に、その結晶粒度番号が6.5以下であることを必要と
する。本発明に従つて、結晶粒度番号を6.5以下とする
ことによつて、満足すべき被削性を得ることができる。The steel according to the present invention needs to have the chemical composition as described above and have a grain size number of 6.5 or less. According to the present invention, by setting the grain size number to 6.5 or less, satisfactory machinability can be obtained.
次に、本発明による上記被削性にすぐれる鋼材は、上記
した化学成分を有する鋼片を （イ）圧延終了後、650〜1100℃の範囲の温度で巻き取
るか、又は （ロ）A3変態点からA1変態点を通過するときまでの平均
冷却速度を0.2℃／秒以下として、結晶粒度番号を6.5以
下とすることによつて得ることができる。巻取温度が65
0℃よりも低いときは、過冷組織が生成し、被削性が劣
化するほか、圧延時に疵がつきやすい。他方、巻取温度
が1100℃を越えるときは、スケールが厚くなり、酸洗後
の製品の表面肌が悪くなる。Next, the steel material excellent in machinability according to the present invention is a steel slab having the above-mentioned chemical composition (a) after completion of rolling, is wound at a temperature in the range of 650 to 1100 ° C, or (b) A. It can be obtained by setting the average cooling rate from the 3 transformation point to the time of passing the A 1 transformation point to 0.2 ° C./sec or less and setting the grain size number to 6.5 or less. Winding temperature is 65
When the temperature is lower than 0 ° C, a supercooled structure is generated, machinability is deteriorated, and defects are likely to occur during rolling. On the other hand, when the winding temperature exceeds 1100 ° C, the scale becomes thick and the surface texture of the product after pickling deteriorates.
本発明によれば、上記した二つの方法の組合せを採用す
ることもできる。少なくとも上記いずれかの方法を用い
ないときは、結晶粒を大きく成長させることができず、
得られる鋼材において、結晶粒度番号が6.5を越えて、
結晶粒が微細になる結果、目的とするすぐれた被削性を
鋼材に付与することができない。According to the invention, it is also possible to employ a combination of the two methods mentioned above. If at least one of the above methods is not used, the crystal grains cannot be grown large,
In the obtained steel material, the grain size number exceeds 6.5,
As a result of the finer crystal grains, it is not possible to impart the desired machinability to the steel material.
発明の効果 以上のように、本発明による圧延線材棒鋼は、快削性付
与元素を実質的に含有せずして、高い被削性を有し、従
つて、前述した部品の製造における高精度化や製造費用
の低減に大きく寄与することができる。特に、本発明に
よる圧延線材棒鋼は、その切削時に圧延材の結晶粒が保
持される磨棒用鋼として好適に用いることができる。Effects of the Invention As described above, the rolled wire rod steel according to the present invention does not substantially contain the free-machinability imparting element and has a high machinability, and accordingly, has high precision in the production of the above-mentioned parts. It is possible to greatly contribute to reduction in manufacturing cost and manufacturing cost. In particular, the rolled wire rod steel according to the present invention can be suitably used as a steel for a polishing rod in which crystal grains of the rolled material are retained during cutting.
更に、本発明によれば、Ｓ及び／又はPbを快削性元素と
して添加すると共に、圧延鋼材の結晶粒度番号を所定値
以上とすることによつて、一層被削性にすぐれる圧延線
材棒鋼を得ることができる。Further, according to the present invention, by adding S and / or Pb as a free-cutting element and setting the grain size number of the rolled steel material to a predetermined value or more, a rolled wire rod steel having further excellent machinability Can be obtained.
実施例 以下に実施例を挙げて本発明を説明するが、本発明はこ
れら実施例により何ら限定されるものではない。EXAMPLES The present invention will be described below with reference to examples, but the present invention is not limited to these examples.
実施例１ C 0.08％、 Si 微量、 Mn 1.04％ P 0.075％ S 0.330％、 残部鉄及び不可避的不純物よりなるSUM22鋼片を第１表
に示す温度にて巻取り、第１表に示す結晶粒度番号を有
する25mm径圧延棒鋼を得た。Example 1 C 0.08%, Si trace amount, Mn 1.04% P 0.075% S 0.330%, SUM22 steel piece consisting of balance iron and unavoidable impurities was wound at the temperature shown in Table 1, and the grain size shown in Table 1 was obtained. A numbered 25 mm diameter rolled steel bar was obtained.
これら圧延棒鋼を22mm径に冷間引抜した後、自動盤を用
いて、第２表に示す切削条件にて切削加工を行ない、得
られた切削加工部品の仕上面粗さと工具の摩耗量によつ
て被削性を評価した。After cold-drawing these rolled steel bars to a diameter of 22 mm, they were machined under the cutting conditions shown in Table 2 using an automatic lathe, and the surface finish of the machined parts obtained and the amount of tool wear Then, machinability was evaluated.
結果を第１図及び第２図に示すように、巻取温度を950
℃以上として、結晶粒度番号を6.5以下とした本発明鋼
は、いずれも被削性にすぐれる。As shown in Fig. 1 and Fig. 2, the winding temperature was set to 950.
All of the steels of the present invention having a grain size number of 6.5 or less at a temperature of ℃ or higher have excellent machinability.
実施例２ C 0.15％、 Si 0.27％下、 Mn 0.45％、 P 0.020％、 S 0.025％、 残部鉄及び不可避的不純物よりなるS15C鋼片を第１表に
示すように、A3変態点からA1変態点を通過するときまで
の平均冷却速度を種々変えて、第１表に示す結晶粒度番
号を有する25mm径圧延棒鋼を得た。Example 2 As shown in Table 1, an S15C steel slab consisting of C 0.15%, Si 0.27%, Mn 0.45%, P 0.020%, S 0.025%, balance iron and inevitable impurities, was changed from A 3 transformation point to A By varying the average cooling rate until passing one transformation point, rolled steel bars with a diameter of 25 mm having the grain size numbers shown in Table 1 were obtained.
これら圧延棒鋼を実施例１と同様に22mm径に冷間引抜し
た後、第２表に示す切削条件にて切削加工を行なつて、
被削性を評価した。結果を第１図及び第２図に示す。A3
変態点からA1変態点を通過するときまでの平均冷却速度
を0.20℃／秒以下として、結晶粒度番号を6.5以下とし
た本発明鋼は、いずれも被削性にすぐれる。These rolled steel bars were cold drawn to a diameter of 22 mm in the same manner as in Example 1, and then cut under the cutting conditions shown in Table 2,
The machinability was evaluated. The results are shown in FIGS. 1 and 2. A 3
The steels of the present invention in which the average cooling rate from the transformation point to the time of passing the A 1 transformation point is 0.20 ° C./sec or less and the grain size number is 6.5 or less are all excellent in machinability.
実施例３ C 0.08％、 Si 微量、 Mn 1.05％、 P 0.080％、 S 0.320％、 Pb 0.26％、 残部鉄及び不可避的不純物よりなるSUM24L鋼片を第１表
に示す巻取温度にて巻取り、第１表に示 す結晶粒度番号を有する25mm径圧延棒鋼を得た。Example 3 A SUM24L steel piece consisting of C 0.08%, Si trace amount, Mn 1.05%, P 0.080%, S 0.320%, Pb 0.26%, balance iron and unavoidable impurities was wound at the winding temperature shown in Table 1. , Shown in Table 1 A 25 mm diameter rolled steel bar with a grain size number was obtained.
これら圧延棒鋼を実施例１と同様に22mm径に冷間引抜し
た後、第２表に示す切削条件にて切削加工を行なつて、
被削性を評価した。結果を第３図及び第４図に示す。本
発明鋼は、従来鋼に比べて、工具摩耗量が少なく、仕上
面あらさが良好である。These rolled steel bars were cold drawn to a diameter of 22 mm in the same manner as in Example 1, and then cut under the cutting conditions shown in Table 2,
The machinability was evaluated. The results are shown in FIGS. 3 and 4. The steel of the present invention has less tool wear than the conventional steel and has a good finished surface roughness.
第１図は、本発明鋼及び比較鋼の切削個数と仕上面粗さ
との関係を示すグラフ、第２図は、本発明鋼及び比較鋼
の切削個数と工具の摩耗量との関係を示すグラフ、第３
図は、本発明鋼及び比較鋼の切削個数と仕上面粗さとの
関係を示すグラフ、第４図は、本発明鋼及び比較鋼の切
削個数と工具の摩耗量との関係を示すグラフである。FIG. 1 is a graph showing the relationship between the number of cuts of the present invention steel and comparative steel and the finished surface roughness, and FIG. 2 is a graph showing the relationship between the number of cuts of the present invention steel and comparative steel and the wear amount of the tool. , Third
FIG. 4 is a graph showing the relationship between the number of cuts of the present invention steel and comparative steel and the finished surface roughness, and FIG. 4 is a graph showing the relationship between the number of cuts of the present invention steel and comparative steel and the wear amount of the tool. .
───────────────────────────────────────────────────── フロントページの続き (72)発明者 松山 博幸 兵庫県神戸市東灘区魚崎北町６丁目６―24 ―302 (56)参考文献 特開 昭55−122859（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Hiroyuki Matsuyama 6-24-24, Uozakikita-cho, Higashinada-ku, Kobe-shi, Hyogo (56) References JP-A-55-122859 (JP, A)
Claims (4)
て、結晶粒度番号が6.5以下であることを特徴とする被
削性にすぐれる圧延線材棒鋼。1. A rolled wire rod steel comprising, by weight, C 0.04 to 0.55%, Si 0.40% or less, Mn 0.30 to 2%, and S 0.040% or less, and the balance iron and unavoidable impurities. A rolled wire rod steel with excellent machinability, which is characterized by being 6.5 or less.
し、 残部鉄及び不可避的不純物よりなる圧延線材棒鋼であつ
て、結晶粒度番号が6.5以下であることを特徴とする被
削性にすぐれる圧延線材棒鋼。2. In weight%, (a) C 0.04 to 0.55%, Si 0.40% or less, and Mn 0.30 to 2% are contained, and (b) S 0.04 to 0.4% and Pb 0.05 to 0.4%. A rolled wire rod containing at least one element selected from the group consisting of balance iron and unavoidable impurities, and having a grain size number of 6.5 or less, which is excellent in machinability Steel bar.
るか、又は （ロ）A3変態点からA1変態点を通過するときまでの平均
冷却速度を0.2℃秒以下として、 結晶粒度番号が6.5以下である圧延線材棒鋼を得ること
を特徴とする被削性にすぐれる圧延線材棒鋼の製造方
法。3. A steel slab composed of C 0.04 to 0.55% by weight, Si 0.40% or less, Mn 0.30 to 2%, and S 0.040% or less by weight, and the balance iron and unavoidable impurities. Rolling at a temperature in the range of ~ 1100 ° C, or (b) Rolling with a grain size number of 6.5 or less with an average cooling rate of 0.2 ° C seconds or less from the A 3 transformation point to the time of passing the A 1 transformation point A method for producing a rolled wire rod steel having excellent machinability, which comprises obtaining a wire rod steel.
し、 残部鉄及び不可避的不純物よりなる鋼片を （イ）圧延終了後、650〜1100℃の範囲の温度で巻き取
るか、又は （ロ）A3変態点からA1変態点を通過するときまでの平均
冷却速度を0.2℃／秒以下として、 結晶粒度番号が6.5以下である圧延線材棒鋼を得ること
を特徴とする被削性にすぐれる圧延線材棒鋼の製造方
法。4. In weight%, (a) contains C 0.04 to 0.55%, Si 0.40% or less, and Mn 0.30 to 2%, and further comprises (b) S 0.04 to 0.4% and Pb 0.05 to 0.4%. A steel slab containing at least one element selected from the group consisting of the balance iron and unavoidable impurities (a) after rolling is wound at a temperature in the range of 650 to 1100 ° C, or (b) A Rolling with excellent machinability, characterized in that a rolled wire rod steel having a grain size number of 6.5 or less is obtained with an average cooling rate of 0.2 ° C / sec or less from the 3 transformation point to the time of passing the A 1 transformation point. Manufacturing method of wire rod.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16988288A JPH0751736B2 (en) | 1988-07-06 | 1988-07-06 | Rolled wire rod with excellent machinability and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16988288A JPH0751736B2 (en) | 1988-07-06 | 1988-07-06 | Rolled wire rod with excellent machinability and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0219443A JPH0219443A (en) | 1990-01-23 |
| JPH0751736B2 true JPH0751736B2 (en) | 1995-06-05 |
Family
ID=15894702
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16988288A Expired - Lifetime JPH0751736B2 (en) | 1988-07-06 | 1988-07-06 | Rolled wire rod with excellent machinability and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0751736B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100398390B1 (en) * | 1998-12-24 | 2003-12-18 | 주식회사 포스코 | A method of manufacturing wire having superior formability for steel fiber of concreate |
| JP3739958B2 (en) * | 1999-03-09 | 2006-01-25 | 新日本製鐵株式会社 | Steel with excellent machinability and its manufacturing method |
| JP4516203B2 (en) * | 1999-11-16 | 2010-08-04 | 株式会社神戸製鋼所 | Steel with excellent straightness after cold drawing |
| KR100435483B1 (en) * | 1999-12-28 | 2004-06-10 | 주식회사 포스코 | A method for manufacturing wire rod for train rail creep with no surface defect and superior surface decarborization |
-
1988
- 1988-07-06 JP JP16988288A patent/JPH0751736B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0219443A (en) | 1990-01-23 |
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