JPH0420966B2 - - Google Patents
Info
- Publication number
- JPH0420966B2 JPH0420966B2 JP62042710A JP4271087A JPH0420966B2 JP H0420966 B2 JPH0420966 B2 JP H0420966B2 JP 62042710 A JP62042710 A JP 62042710A JP 4271087 A JP4271087 A JP 4271087A JP H0420966 B2 JPH0420966 B2 JP H0420966B2
- Authority
- JP
- Japan
- Prior art keywords
- inclusions
- wire
- steel
- molten steel
- powder
- 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
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Treatment Of Steel In Its Molten State (AREA)
Description
（利用分野）
本発明はコードワイヤやピアノ線などに用いら
れる炭素鋼において伸線性のすぐれた高炭素線材
用鋼の製造方法に関するものである。
（発明の背景及び先行技術）
ラジアルタイヤに使用されるコードワイヤやピ
アノ線などの極細線は一般に高炭素キルド鋼を熱
間圧延して約5.5mmφ線材となし、これを間にパ
テンテイングを併用しながら数回の冷間引抜加工
（伸線加工）を施すことにより製造される。伸線
時の断線原因の一つに主として脱酸剤の添加によ
り鋼中にAl2O3、SiO2などの延性に乏しい非金属
介在物が生成し鋼の伸線性が阻害されることが挙
げられ、そのため脱酸生成物の形態を延性に悪影
響のないものにして介在物を無害化する方法が提
案され（特開昭50−71507号公報）、脱酸生成物を
スペサタイト組成にするために溶鋼脱酸用のSi、
Mn、Alの添加量を調整する方法がとられてき
た。この方法は、介在物の形態制御に着目した点
ですぐれたものであるが、Alを使用するため、
脱酸前の溶鋼中酸素などの製造条件のバラツキに
より伸線性に有害な硬質のAl2O3を伴つた介在物
を生成することがあり、非金属介在物の軟質化を
完全にすることができず介在物形態制御の精度の
点で問題を有している。
（発明の概要）
本発明はこのような問題を解決するために脱酸
により非金属介在物として生ずるAl2O3の生成を
防止するとともに非金属介在物を確実に軟質化す
ることを目的とするもので、Al2O3の起源である
脱酸用アルミニウムを全く使用せず、Si、Mnに
よる脱酸を行ない、かつ溶鋼中に存在する脱酸生
成物と十分に反応する量の低融点の粉体（熱間圧
延において延性を有するような組成の粉体）を投
入することによりAl2O3の生成を防止し、非金属
介在物を確実に軟質のものにコントロールできる
ことを見い出し本発明を完成させたものである。
すなわち、脱酸剤としてのAlを全く使用せず、
Mn／Siが1.7以上になるようにSi及びMnにて脱
酸されたＣ 0.25〜1.00％を含有する高炭素溶鋼
に、SiO2：30〜45％、CaO：30〜45％、Na2O：
10〜40％より成る粉体を、溶鋼トン当り200ｇ以
上投入することを特徴とするものである。
（詳細な説明）
本発明は前述の通り脱酸剤としてAlを全く使
用することなく、Si、Mnを使用して脱酸し、Ｃ
0.25〜1.00％、Mn／Si比1.7以上となるように
調整された高炭素鋼の溶鋼にSiO230〜45％、
CaO 30〜45％、Na2O 10〜40％より成る粉体
を、溶鋼中の非金属介在物を十分に反応する量で
ある溶鋼トン当り200ｇ以上を投入することによ
り伸線性に有害なAl2O3の生成を防止し、かつ非
金属介在物を再現性よく軟質（Si−Mn−Ca−
Na−Ｏ系）とするものであるが、次に本発明に
おいてＣ量とMn／Siを上述のように限定した理
由について説明する。
Ｃは成品の強度を確保するためには少くとも
0.25％が必要であるが、1.00％を超えると加工性
が悪化するために0.25〜1.00％とする。
Mn／Si比は1.7未満の場合には延伸困難なSiO2
系介在物が増加して伸線性を著しく阻害するので
1.7以上とする。
本発明はまたAlの添加を規制するとともに、
SiO2−CaO−SiO2より成る粉体を投入すること
により、非金属介在物の組成を再現性よくSi−
Mn−Na−Ｏにコントロールするものであるが、
SiO2−CaO二元系において融点の最も低い
SiO2／CaO＝１の組成を有するフラツクスに対
し、熱間圧延温度（1000〜1200℃）で十分な延性
を有する介在物ができるようにNa2Oを配合し
て、その配合率がNa2O10％以下では介在物の延
性効果がなく、またNa2O40％以上ではその効果
が飽和しコストアツプを招くだけとなることを知
見したので、本発明ではSiO2 30〜45％、CaO
30〜45％、Na2O 10〜40％より成る組成の粉体
を使用することにより、熱間圧延後長く伸長し、
冷間伸線加工において無害な介在物を得るもので
ある。
粉体の投入量は溶鋼トン当り200ｇ以上、望ま
しくは500ｇ以上としている。溶鋼中の脱酸生成
物は溶鋼トン当り50〜200ｇ程度生成されるため、
粉体が200ｇ未満であると脱酸生成物との反応量
が不足し、前記介在物が十分に生成されない。投
入量の上限は特に制限されないが、過剰の投入は
経済的に無駄であり、一般には5000ｇ以下とする
のが好ましい。
粉体の投入方法は上部より投入する方法以外
に、浸漬ランスを介してArガスのような不活性
ガスとともに溶鋼中に吹込んでもよく、むしろ後
者の方が反応時間を短縮するためには望ましい。
上部投入の場合には反応を促進するために不活性
ガスや電磁撹拌による溶鋼の撹拌を併用すること
が好ましい。
次に本発明の実施例を示して特徴を説明する。
70トン転炉で第１表に示した化学成分を有する
鋼を溶製し、不純物としてのAlの含有量の少な
いFe−Si及びFe−Mnを脱酸剤として投入後、出
鋼末期のスラグ流出を抑えるようにして出鋼し、
取鍋内に（粉体）40％CaO−30％SiO2−30％
Na2O（符号Ａ〜Ｅ、Ｌ〜Ｏ参照）の粉体及び
（粉体）45％CaO−45％SiO2−10％Na2Oの粉
体を第１表に示す各種の量で投入した。その後、
溶鋼中にArガスを300／minの流量で７分間吹
込み、溶鋼を撹拌した後、連続鋳造法にて鋳片を
鋳込んだ。なお、比較のために粉体を投入しない
場合についても同様に連続鋳造を行なつた。得ら
れた鋳片を熱間圧延して5.5mmφの線材を製造し、
この線材について顕微鏡観察により介在物検査を
実施した。検査は披測定面積44mm2で介在物幅が
3μｍ以上の非延性介在物の個数と3μｍ以下の延
性介在物の個数を数え、結果を第１表に示す。次
いでこの5.5mmφの線材を冷間加工により5.5mmφ
→2.6mmφ、鉛パテンテイング→1.3mmφ、鉛パテ
ンテイング→0.5mmφ→0.2mmφの工程で、0.2mmφ
に伸線した。この時の断線回数を断線指数（＝鋼
１トン伸線時の断線回数を、比較鋼の最大値を
100として表わした指数）として第１表に併せて
示す。
(Field of Application) The present invention relates to a method for producing high carbon wire rod steel with excellent wire drawability among carbon steels used for cord wires, piano wires, and the like. (Background of the invention and prior art) Ultrafine wires such as cord wires and piano wires used in radial tires are generally made by hot rolling high carbon killed steel into approximately 5.5mmφ wire rods, which are then patented in between. It is manufactured by performing cold drawing (wire drawing) several times. One of the causes of wire breakage during wire drawing is that non-metallic inclusions with poor ductility such as Al 2 O 3 and SiO 2 are formed in the steel due to the addition of deoxidizing agents, which inhibits the wire drawability of the steel. Therefore, a method was proposed to make the inclusions harmless by changing the form of the deoxidized product to one that does not have a negative effect on ductility (Japanese Patent Application Laid-open No. 71507/1983), and in order to make the deoxidized product have a spessartite composition. Si for deoxidizing molten steel,
A method has been used to adjust the amounts of Mn and Al added. This method is excellent in that it focuses on controlling the morphology of inclusions, but since it uses Al,
Due to variations in manufacturing conditions such as oxygen in molten steel before deoxidation, inclusions with hard Al 2 O 3 that are harmful to wire drawability may be generated, so it is difficult to completely soften nonmetallic inclusions. This poses a problem in terms of accuracy in controlling the shape of inclusions. (Summary of the Invention) In order to solve such problems, the present invention aims to prevent the formation of Al 2 O 3 that is generated as non-metallic inclusions by deoxidation, and to reliably soften the non-metallic inclusions. It does not use any deoxidizing aluminum, which is the source of Al 2 O 3 , and deoxidizes with Si and Mn, and has a low melting point that is sufficient to react with the deoxidation products present in molten steel. It was discovered that the formation of Al 2 O 3 can be prevented by adding powder (powder with a composition that is ductile during hot rolling), and that nonmetallic inclusions can be reliably controlled to be soft. It has been completed. In other words, without using any Al as a deoxidizing agent,
SiO2 : 30-45%, CaO: 30-45%, Na2O are added to high carbon molten steel containing 0.25-1.00% C which has been deoxidized with Si and Mn so that Mn/Si is 1.7 or more. :
It is characterized in that 200 g or more of powder consisting of 10 to 40% is added per ton of molten steel. (Detailed Description) As mentioned above, the present invention uses Si and Mn to deoxidize without using Al as a deoxidizing agent at all, and C
0.25-1.00%, 30-45% SiO 2 in high carbon steel molten steel adjusted to have an Mn/Si ratio of 1.7 or more.
By adding powder consisting of 30-45% CaO and 10-40% Na 2 O in an amount of 200 g or more per ton of molten steel, which is an amount that sufficiently reacts with non-metallic inclusions in molten steel, Al, which is harmful to wire drawability, is removed. 2 O 3 generation is prevented and nonmetallic inclusions are reproducibly softened (Si-Mn-Ca-
Next, the reason why the amount of C and Mn/Si are limited as described above in the present invention will be explained. C is at least required to ensure the strength of the finished product.
0.25% is necessary, but if it exceeds 1.00%, workability deteriorates, so it is set at 0.25 to 1.00%. SiO 2 is difficult to stretch when the Mn/Si ratio is less than 1.7.
Since system inclusions increase and significantly impede wire drawability,
Must be 1.7 or higher. The present invention also regulates the addition of Al, and
By introducing powder consisting of SiO 2 −CaO−SiO 2 , the composition of nonmetallic inclusions can be determined with good reproducibility.
Although it controls Mn-Na-O,
The lowest melting point in the SiO 2 −CaO binary system
Na 2 O is blended into the flux having a composition of SiO 2 /CaO = 1 so that inclusions with sufficient ductility are formed at the hot rolling temperature (1000 to 1200°C), and the blending ratio is Na 2 It was found that inclusions have no ductility effect when O is less than 10%, and that the effect is saturated when Na 2 O is more than 40%, which only increases costs.
By using a powder with a composition of 30-45% Na 2 O and 10-40% Na 2 O, it can be elongated long after hot rolling.
Harmless inclusions are obtained during cold wire drawing. The amount of powder to be added is 200 g or more, preferably 500 g or more per ton of molten steel. Since deoxidation products in molten steel are generated in the range of 50 to 200 g per ton of molten steel,
If the amount of powder is less than 200 g, the amount of reaction with the deoxidized product will be insufficient, and the inclusions will not be sufficiently produced. There is no particular upper limit to the amount to be added, but excessive amounts are economically wasteful, so it is generally preferable to limit the amount to 5,000 g or less. In addition to the method of introducing the powder from the top, it is also possible to inject the powder into the molten steel together with an inert gas such as Ar gas through an immersion lance, and the latter is preferable in order to shorten the reaction time. .
In the case of top charging, it is preferable to use inert gas or magnetic stirring to stir the molten steel in order to promote the reaction. Next, embodiments of the present invention will be shown and characteristics will be explained. After melting steel having the chemical composition shown in Table 1 in a 70-ton converter and adding Fe-Si and Fe-Mn, which have a low content of Al as impurities, as deoxidizers, the slag at the final stage of steel tapping is produced. Steel is tapped in a manner that suppresses outflow,
In the ladle (powder) 40%CaO−30% SiO2−30 %
Powder of Na 2 O (see symbols A to E, L to O) and (powder) powder of 45% CaO - 45% SiO 2 -10% Na 2 O were added in various amounts shown in Table 1. did. after that,
After stirring the molten steel by blowing Ar gas into the molten steel at a flow rate of 300/min for 7 minutes, slabs were cast using a continuous casting method. For comparison, continuous casting was also carried out in the same manner without the addition of powder. The obtained slab was hot rolled to produce a 5.5mmφ wire rod.
This wire was inspected for inclusions by microscopic observation. The inspection was performed on a measurement area of 44mm2 , and the width of the inclusion was
The number of non-ductile inclusions of 3 μm or more and the number of ductile inclusions of 3 μm or less were counted, and the results are shown in Table 1. Next, this 5.5mmφ wire rod is cold worked to 5.5mmφ
→2.6mmφ, lead patenting → 1.3mmφ, lead patenting → 0.5mmφ → 0.2mmφ process, 0.2mmφ
The wire was drawn. The number of wire breaks at this time is the wire breakage index (= the number of wire breaks when drawing 1 ton of steel, the maximum value of the comparative steel)
It is also shown in Table 1 as an index (expressed as 100).
【表】
第１表の結果から明らかなように本発明の方法
により粉体を溶鋼トン当り200ｇ以上投入すると、
非延性介在物の個数が著しく減少し延性介在物が
増加している。介在物の組成はSi−Mn−Ca−
Na−Ｏで、介在物が軟質に制御されているため、
熱間圧延により介在物の大部分が幅3μｍ未満の
微細な形態に延伸されている。この効果は投入量
が200ｇ／トン未満の場合には殆んど認められず、
粉体無添加の場合と同様に非延性介在物が多数生
成した。この非延性介在物の個数の結果は、伸線
加工での断線回数の結果に反映されており、本発
明鋼では断線指数は０〜25程度であるのに対し、
比較鋼では80以上と非常に高い結果を示した。
以上説明したように、本発明によると粉体の投
入という簡単な操作で、鋼の伸線性を阻害する非
延性の非金属介在物の生成を防ぐことができ、確
実に非金属介在物を延性組成のものにコントロー
ルできる。従つて伸線性のすぐれた高炭素線材用
鋼を再現性よく製造することができ、実操業に与
える利点は極めて大きいものである。[Table] As is clear from the results in Table 1, when 200 g or more of powder is added per ton of molten steel using the method of the present invention,
The number of non-ductile inclusions decreased significantly and the number of ductile inclusions increased. The composition of the inclusion is Si-Mn-Ca-
Because inclusions are controlled to be soft with Na-O,
By hot rolling, most of the inclusions are drawn into a fine shape with a width of less than 3 μm. This effect is hardly observed when the input amount is less than 200g/ton.
A large number of non-ductile inclusions were generated as in the case without powder addition. The result of the number of non-ductile inclusions is reflected in the result of the number of wire breaks during wire drawing, and while the wire breakage index of the steel of the present invention is about 0 to 25,
The comparison steel showed very high results of over 80. As explained above, according to the present invention, the formation of non-ductile non-metallic inclusions that inhibit the wire drawability of steel can be prevented by the simple operation of adding powder, and the non-metallic inclusions can be reliably made ductile. The composition can be controlled. Therefore, high-carbon wire steel with excellent wire drawability can be manufactured with good reproducibility, and the advantages in actual operation are extremely large.
Claims (1)
調整されたＣ 0.25〜1.00％を含有する高炭素溶
鋼にSiO2 30〜45％、CaO 30〜45％、Na2O 10
〜40％より成る粉体を溶鋼トン当り200ｇ以上を
投入することを特徴とする伸線性のすぐれた高炭
素線材用鋼の製造方法。1 High carbon molten steel containing 0.25 to 1.00% C that has been deoxidized with Si and Mn and adjusted to Mn/Si: 1.7 or more is mixed with 30 to 45% SiO 2 , 30 to 45% CaO, and 10 Na 2 O 10
1. A method for producing steel for high carbon wire rods with excellent wire drawability, characterized in that 200 g or more of powder consisting of ~40% is added per ton of molten steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62042710A JPS63210232A (en) | 1987-02-27 | 1987-02-27 | Manufacture of steel for high-carbon wire rod excellent in wiredrawability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62042710A JPS63210232A (en) | 1987-02-27 | 1987-02-27 | Manufacture of steel for high-carbon wire rod excellent in wiredrawability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63210232A JPS63210232A (en) | 1988-08-31 |
| JPH0420966B2 true JPH0420966B2 (en) | 1992-04-07 |
Family
ID=12643628
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62042710A Granted JPS63210232A (en) | 1987-02-27 | 1987-02-27 | Manufacture of steel for high-carbon wire rod excellent in wiredrawability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63210232A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005264335A (en) * | 2005-04-28 | 2005-09-29 | Sumitomo Metal Ind Ltd | Si deoxidized steel excellent in fatigue strength and method for producing the same |
-
1987
- 1987-02-27 JP JP62042710A patent/JPS63210232A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63210232A (en) | 1988-08-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2575827B2 (en) | Manufacturing method of ultra low carbon steel for continuous casting with excellent cleanliness | |
| WO2000077271A1 (en) | High carbon steel wire rod excellent in drawability and fatigue resistance after wire drawing | |
| JP3550924B2 (en) | Method for manufacturing high carbon steel wire and wire | |
| CN111500919A (en) | Production method of high cleanliness high titanium low carbon steel | |
| JPH10130714A (en) | Method for producing steel for wire rod excellent in drawability and cleanliness | |
| JP3319245B2 (en) | Method for producing highly clean austenitic stainless steel | |
| JP3536461B2 (en) | High carbon steel wire with excellent drawability and aging resistance | |
| RU2058994C1 (en) | Method of making semikilled steel, microalloyed by vanadium | |
| CN118291708A (en) | A method for smelting hydrogen pipeline steel | |
| CN118406842A (en) | Preparation method of rare earth ultra-low carbon steel for special material and rare earth ultra-low carbon steel | |
| JPH0420966B2 (en) | ||
| JPS6157372B2 (en) | ||
| JP3282865B2 (en) | Manufacturing method of high carbon steel for high strength ultra fine wire | |
| JPH07268440A (en) | Method of deoxidizing molten steel | |
| JP2009084672A (en) | Method for heating molten steel and method for producing rolled steel | |
| JP2976855B2 (en) | Method of deoxidizing molten steel | |
| JP7827229B1 (en) | Method for refining molten steel and method for producing steel | |
| JPS63262412A (en) | Method for cleaning molten steel | |
| JP3221812B2 (en) | Low oxygen steel smelting method | |
| JPH1068011A (en) | Method for producing oxide-dispersed steel | |
| KR950012406B1 (en) | Method of manufacturing carbon dioxide welding rod steel | |
| JPH04354853A (en) | Fe-ni alloy cold rolled sheet excellent in cleanliness and etching pierceability and its production | |
| CN118256683A (en) | Smelting method of molten steel with extremely low sulfur content and application thereof | |
| JPH05331523A (en) | Method for refining molten steel for bearing steel | |
| CN113667790A (en) | Production method of gas-shielded welding wire steel |