JPH0762171B2 - Method for producing austenitic stainless steel excellent in wire drawability and cold rollability - Google Patents
Method for producing austenitic stainless steel excellent in wire drawability and cold rollabilityInfo
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- JPH0762171B2 JPH0762171B2 JP1194366A JP19436689A JPH0762171B2 JP H0762171 B2 JPH0762171 B2 JP H0762171B2 JP 1194366 A JP1194366 A JP 1194366A JP 19436689 A JP19436689 A JP 19436689A JP H0762171 B2 JPH0762171 B2 JP H0762171B2
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- stainless steel
- austenitic stainless
- wire
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は伸線加工により超極細線とし、あるいは冷間圧
延により箔とするためのオーステナイト系ステンレス鋼
の製造方法に関するものである。TECHNICAL FIELD The present invention relates to a method for producing austenitic stainless steel for forming ultrafine wires by wire drawing or forming foil by cold rolling.
化学工業用フィルターあるいは繊維強化複合材料用原料
にオーステナイト系ステンレス鋼の超極細線が使用され
ている。その直径は50μｍφ以下であり、断面が真円形
で、かつ高耐食性のものが要求される。従来、断面が真
円形の超極細線は伸線加工によって製造されており、材
料には汎用のSUS304あるいはSUS316が使用されていた。Ultra fine wires of austenitic stainless steel are used as raw materials for filters for the chemical industry or fiber reinforced composite materials. Its diameter is 50 μmφ or less, and it is required to have a perfect circular cross section and high corrosion resistance. Conventionally, ultrafine wires with a perfect circular cross section have been manufactured by wire drawing, and general-purpose SUS304 or SUS316 was used as the material.
ところで、超極細線の製造に際しては、伸線加工が強度
の冷間加工であること、線が微小直径であることから基
本材質以外に非金属介在物が伸線加工性に大きく影響し
てくる。非金属介在物の多い、すなわち清浄度の悪い材
料では伸線途中で断線が生じ、所要の線径を得ることが
できないかあるいは製品歩留まりが低くなり製造上の大
きな問題点である。By the way, in the production of ultra-fine wire, non-metallic inclusions have a great influence on wire drawing workability in addition to the basic material because the wire drawing is a strong cold work and the wire has a small diameter. . A material having a large amount of non-metallic inclusions, that is, a material having poor cleanliness causes a wire breakage during wire drawing, which makes it impossible to obtain a desired wire diameter or lowers the product yield, which is a major problem in manufacturing.
また、近年、OA機器等各種電子機器用部品へのオーステ
ナイト系ステンレス箔の適用が急速に増加してきてい
る。これに伴い、材料の信頼性に対する要求は一段と厳
しくなってきている。Further, in recent years, the application of austenitic stainless steel foil to parts for various electronic devices such as office automation equipment has been rapidly increasing. Along with this, the demand for the reliability of materials has become more severe.
オーステナイト系ステンレス箔は冷間圧延によって製造
されるため、非金属介在物の存在は微小割れあるいは表
面疵等の欠陥を誘発すると共に、機械的性質あるいは疲
労特性の低下をも招くため大きな問題である。Since austenitic stainless steel foil is manufactured by cold rolling, the presence of non-metallic inclusions causes defects such as microcracks and surface defects, and also causes deterioration of mechanical properties or fatigue properties, which is a big problem. .
従って、有害な非金属介在物を積極的に低減する方策が
試みられ、この結果、溶解原料を厳しく管理するととも
に超高真空化あるいはESR等による多数回のリメルトに
よる製法がとられている。Therefore, a measure for actively reducing harmful non-metallic inclusions has been attempted, and as a result, the raw material for melting has been strictly controlled, and a production method has been adopted by performing remelting a number of times such as ultra-high vacuum or ESR.
しかしながらこれらの方法では生産性が低く、製造コス
トも高い等の欠点がある。However, these methods have drawbacks such as low productivity and high manufacturing cost.
最近、軽薄短小の趨勢の中で極細ステンレス線およびス
テンレス箔の需要がますます増大する中で伸線加工性な
らびに冷間圧延性に優れたオーステナイト系ステンレス
鋼が強く要求されている。Recently, amid growing demand for ultra-fine stainless wire and stainless foil in the trend of light, thin, short and small, austenitic stainless steel excellent in wire drawing workability and cold rolling property is strongly demanded.
本発明は、高歩留りで超極細線に伸線加工でき、また、
高歩留りで極薄箔に冷間圧延できる耐食性に優れたオー
ステナイト系ステンレス鋼を生産性良く製造することを
目的とする。The present invention is capable of drawing ultra-fine wires with high yield, and
It is an object of the present invention to produce an austenitic stainless steel excellent in corrosion resistance, which can be cold-rolled into an ultrathin foil with high yield and is excellent in productivity.
本発明に係わる伸線性ならびに冷間圧延性に優れたオー
ステナイト系ステンレス鋼の製造法は、重量％にて C:0.005〜0.10％,Si:0.2〜1.0％， Mn:0.2〜2.5％,P≦0.045％,S≦0.020％， Ni:6〜20％,Cr:15〜25％,N:0.01〜0.10％， Al:0.0005〜0.005％,Ca:0.0001〜0.002％， Mg:0.0001〜0.001％,O≦0.0025％ を含有し、さらに必要に応じてMo:0.5〜3.5％およびCu:
0.5〜3.5％の１種または２種を含有し、残部Feおよび不
可避的不純物からなるオーステナイト系ステンレス鋼の
熱間圧延素材を、1000℃以上1300℃以下の温度で10分以
上加熱した後熱間圧延することにより、熱間圧延材にお
ける非金属介在物の組成を、重量％にて、SiO2:20〜50
％,MnO:15〜60％,Al2O3:3〜15％,CaO:3〜25％,MgO:0.5
〜10％ とすることを特徴とする。The method for producing an austenitic stainless steel excellent in wire drawability and cold rolling property according to the present invention is C: 0.005 to 0.10%, Si: 0.2 to 1.0%, Mn: 0.2 to 2.5%, P ≦ in weight%. 0.045%, S ≤ 0.020%, Ni: 6 to 20%, Cr: 15 to 25%, N: 0.01 to 0.10%, Al: 0.0005 to 0.005%, Ca: 0.0001 to 0.002%, Mg: 0.0001 to 0.001%, O ≦ 0.0025%, and optionally Mo: 0.5-3.5% and Cu:
After hot-rolling an austenitic stainless steel hot-rolling material containing 0.5 to 3.5% of 1 or 2 and the balance Fe and unavoidable impurities at a temperature of 1000 ° C or more and 1300 ° C or less for 10 minutes or more, hot working By rolling, the composition of the non-metallic inclusions in the hot-rolled material, in% by weight, is SiO 2 : 20 to 50
%, MnO: 15~60%, Al 2 O 3: 3~15%, CaO: 3~25%, MgO: 0.5
It is characterized by being ~ 10%.
本発明における成分限定理由は次の通りである。The reasons for limiting the components in the present invention are as follows.
C,N:伸線あるいは冷間圧延（以下冷間加工と言う）時の
延・靭性の点からはC,Nは共に低い方が好ましい。しか
しながら、C,Nを低めることはオーステナイト相が不安
定となり、凝固時にδ相を生成すること、さらに伸線加
工時にマルテンサイ相を生成し、いずれにおいてもマト
リックスの加工性を低下する。また、C,Nを低めること
は精練時間の延長をきたし、製造コストのアップにな
る。従って、Ｃは0.005〜0.10％とし、Ｎは0.01〜0.10
％とした。C, N: From the viewpoint of ductility and toughness during wire drawing or cold rolling (hereinafter referred to as cold working), it is preferable that both C and N are low. However, lowering C and N makes the austenite phase unstable, producing a δ phase during solidification, and further producing a martensi phase during wire drawing, which reduces the workability of the matrix. In addition, lowering C and N leads to an increase in refining time and an increase in manufacturing cost. Therefore, C is 0.005 to 0.10% and N is 0.01 to 0.10.
%.
Si:Siは、介在物を冷間加工にて延伸・分断する組成に
調整するためには0.2％以上必要であるが、1.0％を越え
て多量に含有すると、SiO2系の硬質酸化物を形成し、冷
間加工性を低下する。よって、Si含有量は0.2〜1.0％と
した。Si: Si must be 0.2% or more in order to adjust the composition so that the inclusions are stretched / separated by cold working, but if it is contained in a large amount exceeding 1.0%, a hard oxide of SiO 2 system is formed. Formed, and deteriorates cold workability. Therefore, the Si content is set to 0.2 to 1.0%.
Mn:Mnは鋼中ＳとMnSを生成し、熱間加工性を改善する。
また、オーステナイト相を安定化し、冷間加工性を向上
する。これらの作用を有効ならしめるためには0.2％以
上が必要である。一方、必要量以上に含有量が高くなる
と固溶硬化により材料の靭性が低下する。よって、Mnの
上限は2.5％とした。Mn: Mn forms S and MnS in steel and improves hot workability.
It also stabilizes the austenite phase and improves cold workability. 0.2% or more is required to make these effects effective. On the other hand, when the content is higher than the necessary amount, the toughness of the material decreases due to solid solution hardening. Therefore, the upper limit of Mn is set to 2.5%.
S,P:S,Pは熱間加工性、伸線加工性のいずれの面からも
低い程好ましいものであるが、通常の原料から不可避的
に混入してくるので、Ｓ含有量は0.020％以下とし、Ｐ
含有量は0.045％以下とした。S, P: S, P is preferably as low as possible from both aspects of hot workability and wire drawing workability, but since it is inevitably mixed from ordinary raw materials, the S content is 0.020%. Below, P
The content was 0.045% or less.
Ni:Niは鋼のオーステナイト域を拡大し常温にて安定し
たオーステナイト組織とするのに必須であり、併せて、
鋼の延・靭性を向上させるためには６％以上は必要であ
る。一方、20％を越えて含有すると冷間加工時の強度不
足を来たし、伸線加工における断線率および冷間圧延に
おける箔の破断率が増加するばかりでなく、高価になっ
てしまう。よって、Ni含有量は６〜20％とした。Ni: Ni is indispensable for expanding the austenite region of steel and making the austenite structure stable at room temperature.
6% or more is necessary to improve the ductility and toughness of steel. On the other hand, if the content exceeds 20%, the strength during cold working becomes insufficient, and not only the breakage rate in wire drawing and the breakage rate of foil in cold rolling increase, but also the cost becomes high. Therefore, the Ni content is set to 6 to 20%.
Cr:Crは安定した耐食性を得るため、また冷間加工時の
加工発熱下での強度の確保のために15％以上が必要であ
る。一方、25％を越えるとδ相を形成し、熱間加工性を
低下させる。よって、Cr含有量は15〜25％とした。Cr: Cr is required to be 15% or more in order to obtain stable corrosion resistance and to secure the strength under heat generation during cold working. On the other hand, if it exceeds 25%, a δ phase is formed and the hot workability is deteriorated. Therefore, the Cr content is set to 15 to 25%.
Mo:Moは不可避的不純物として鋼中に0.4％以下含まれる
が、耐食性の確保と冷間加工時の加工発熱下での強度を
確保するため、0.5％以上を必要に応じて添付するが、
多量に含有することは熱間加工性の低下を来すとともに
高価になる。よって、Moは0.5〜3.5％とした。Mo: Mo is contained as 0.4% or less in steel as an unavoidable impurity, but 0.5% or more is attached as necessary to secure the corrosion resistance and the strength under the heat generated during processing during cold working.
If a large amount is contained, the hot workability is deteriorated and the cost becomes high. Therefore, Mo is set to 0.5 to 3.5%.
Cu:Cuは不可避的不純物として鋼中に0.4％以下含まれる
が、耐食性の確保と延性を向上させるため、0.5％以上
必要に応じて添付するが、多量に含有すると熱間加工性
が低下する。よってCuは0.5〜3.5％とした。Cu: Cu is contained as 0.4% or less in steel as an unavoidable impurity, but 0.5% or more is added as necessary to secure corrosion resistance and improve ductility, but if contained in a large amount, hot workability deteriorates . Therefore, Cu is set to 0.5 to 3.5%.
Al,Mg,Ca:これらはいずれも単独で存在すると鋼中に硬
質の酸化物系介在物を形成し、鋼の清浄性を悪くし、冷
間加工性を大幅に低下するため、高清浄性を確保するた
めには低い程好ましい。しかしこれらは溶解原料あるい
は耐火物から単独で不可避的に混入する恐れがある。従
って、本発明においては、Alを0.0005〜0.005％,Mgを0.
0001〜0.001％,Caを0.0005〜0.002％の範囲で複合添加
することにより、高清浄下とともに、冷間加工時に介在
物が延伸・分断され易くする。Al, Mg, Ca: If all of these are present alone, they form hard oxide inclusions in the steel, which deteriorates the cleanliness of the steel and significantly reduces cold workability. In order to ensure that, the lower the better. However, these may be unavoidably mixed alone from the molten raw material or the refractory. Therefore, in the present invention, Al is 0.0005 to 0.005%, Mg is 0.
By adding 0001 to 0.001% and Ca in the range of 0.0005 to 0.002% in a combined manner, the inclusions are easily stretched and divided during cold working as well as under high cleanliness.
上記組成に調整されたオーステナイト系ステンレス鋼の
熱間圧延素材を1000℃以上1300℃以下の温度で10分以上
加熱した後、熱間圧延することにより、熱間圧延材にお
ける介在物の組成を重量％にてSiO2:20〜50％,MnO:15〜
60％,Al2O3:3〜15％,CaO:3〜25％,MgO:0.5〜10％とす
る。介在物の組成がこの範囲をはずれると超極細線ある
いは箔への冷間加工時に介在物起因の断線あるいは破断
が生じるおそれがある。After heating the austenitic stainless steel hot-rolled material adjusted to the above composition at a temperature of 1000 ° C or more and 1300 ° C or less for 10 minutes or more, by hot rolling, the composition of inclusions in the hot-rolled material is weighted. % SiO 2 : 20-50%, MnO: 15〜
60%, Al 2 O 3 : 3 to 15%, CaO: 3 to 25%, MgO: 0.5 to 10%. If the composition of the inclusions deviates from this range, there is a risk of disconnection or breakage due to the inclusions during the cold working of the ultrafine wire or foil.
熱間圧延素材は、超極細線用としてはビレット、箔用と
してはスラブであり、いずれも連続鋳造されたもの、あ
るいは分塊圧延されたもののいずれでも良い。熱間圧延
材は、超極細線用としては線材、箔用としては熱間圧延
鋼帯である。The hot-rolled material is a billet for ultra-fine wires and a slab for foil, and both may be continuously cast or slab-rolled. The hot rolled material is a wire material for ultrafine wire and a hot rolled steel strip for foil.
本発明によって得られた線材あるいは熱間圧延鋼帯は、
マトリックスが延性および靭性に優れ、超極細線への伸
線加工あるいは箔への冷間圧延時に非金属介在物が延伸
し、かつ分断し易いので、断線あるいは破断が生じ難
い。The wire rod or hot rolled steel strip obtained by the present invention,
The matrix has excellent ductility and toughness, and non-metallic inclusions are stretched and easily split during wire drawing into ultrafine wires or cold rolling into foil, so that breakage or breakage is unlikely to occur.
実施例１ 第１表に本実施例に供したオーステナイト系ステンレス
鋼の化学成分を示した。Example 1 Table 1 shows the chemical composition of the austenitic stainless steel used in this example.
これらの鋼を真空溶解ならびに電子ビーム溶解法にて溶
製し、線材圧延用ビレットを製造した。These steels were melted by a vacuum melting method and an electron beam melting method to manufacture a billet for rolling a wire rod.
該ビレットをビレット加熱炉にて1100℃×60分加熱後、
線材圧延し、5.5mmφの線材とした。圧延された線材は
焼鈍および酸洗を行った後、一旦1.8mmφまで伸線した
後、光輝焼鈍を施し、さらに0.5mmφに伸線した。0.5mm
φに伸線された中間線を光輝焼鈍した後、極細線への伸
線加工に供した。After heating the billet in a billet heating furnace at 1100 ° C for 60 minutes,
The wire rod was rolled into a 5.5 mmφ wire rod. The rolled wire rod was annealed and pickled, then once drawn to 1.8 mmφ, then bright annealed and further drawn to 0.5 mmφ. 0.5 mm
After the intermediate wire drawn to φ was bright annealed, it was subjected to wire drawing processing into an ultrafine wire.
極細伸線は18〜20パス連続伸線になるように、平均減面
率８〜10％でダイススケジュールを設定し、線径20μｍ
φまで伸線して製造した。潤滑は市販の湿式潤滑油を用
いた。The ultra-thin wire drawing is set to a continuous wire drawing of 18 to 20 passes by setting the die schedule with an average surface reduction rate of 8 to 10% and a wire diameter of 20 μm.
It was drawn to φ and manufactured. A commercially available wet lubricating oil was used for lubrication.
伸線加工性は、重量55kgの0.5mmφ素線から線径20μｍ
φまで伸線し、最初の断線を生じた時に得られた20μｍ
φ線の重量で評価した。Wire drawing workability is 20μm from 0.5mmφ wire with a weight of 55kg
20μm obtained when the first wire break occurred after wire drawing up to φ
It was evaluated by the weight of the φ wire.
第２表は5.5mmφ線材における、酸化物系非金属介在物2
0ヶの平均組成ならびに３μｍ以上の大きさを有する酸
化物系非金属介在物の単位面積当りの個数と伸線加工性
の関係を示したものである。Table 2 shows oxide-based non-metallic inclusions in the 5.5mmφ wire. 2
It shows the relationship between the number of oxide-based non-metallic inclusions having a mean composition of 0 and a size of 3 μm or more per unit area and wire drawability.
〔Ｏ〕量を制限し、非金属介在物組成を調整した本発明
例（No.1〜No.16）は、３μｍ以上の大きさの酸化物系
非金属介在物の個数が少なく、１断線当りに得られる20
μｍφの極細ステンレス線の伸線量が圧倒的に多いこと
がわかる。これに対して、比較例のNo.17およびNo.21鋼
は〔Ｏ〕量が高いために、また、No.18〜No.20は非金属
介在物組成が調整されていないがために、さらに、No.2
2〜24は〔Ｏ〕量が高くかつ非金属介在物が調整されて
いないために、いずれも３μｍ以上の介在物個数が多
く、１断線当りの伸線量は低い。In the present invention examples (No. 1 to No. 16) in which the amount of [O] was limited and the composition of non-metallic inclusions was adjusted, the number of oxide-based non-metallic inclusions having a size of 3 μm or more was small, and one breakage occurred. 20 per hit
It can be seen that the drawing amount of the ultrafine stainless steel wire of μmφ is overwhelmingly large. On the other hand, the No. 17 and No. 21 steels of Comparative Examples have a high [O] amount, and the No. 18 to No. 20 steels have the non-metallic inclusion composition not adjusted, Furthermore, No.2
In Nos. 2 to 24, the amount of [O] was high and the non-metallic inclusions were not adjusted, so that the number of inclusions having a size of 3 μm or more was large and the wire extension amount per wire breakage was low.
実施例２ 第３表に、箔圧延に供した本実施例のオーステナイト系
ステンレス鋼の化学成分を示した。 Example 2 Table 3 shows the chemical composition of the austenitic stainless steel of this example that was subjected to foil rolling.
真空溶解法により溶製したスラブを1200℃×20分加熱
後、熱間圧延を行い、4mm厚のステンレス鋼帯とした。
該ステンレス鋼帯を素材として、50μｍ厚の箔圧延を行
い、得られたオーステナイト系ステンレス箔の表面欠陥
を調査した。The slab melted by the vacuum melting method was heated at 1200 ° C. for 20 minutes and then hot rolled to obtain a stainless steel strip having a thickness of 4 mm.
Using the stainless steel strip as a raw material, 50 μm thick foil was rolled, and the surface defects of the obtained austenitic stainless steel foil were investigated.
結果を第４表に示す。The results are shown in Table 4.
本発明例No.25は、表面欠陥が全く認められないのに対
して、比較例No.26には肉眼判定可能な割れが0.1個/m2
発生している。割れ部にはAl2O3濃度の高い酸化物系非
金属介在物が認められた。Inventive Example No. 25, surface defects are not observed at all, in Comparative Example No. 26 is visually recognizable cracks 0.1 / m 2
It has occurred. Oxide-based nonmetallic inclusions with high Al 2 O 3 concentration were found in the cracks.
〔発明の効果〕 以上説明したように、本発明により製造したオーステナ
イト系ステンレス鋼は、既存の技術で容易に、且つ安価
に製造できるため、オーステナイト系極細線においては
化学工業用各種フィルターを初め、複合材料用繊維原料
に適用でき、また、冷間加工性が極めて良好になるた
め、ステンレス箔用素材や複雑形状に加工される板材
等、広い分野に応用できるため、その産業上への貢献は
極めて大である。 [Effects of the Invention] As described above, the austenitic stainless steel produced according to the present invention can be easily and inexpensively produced by the existing technique, and therefore, in the austenitic extra fine wire, various filters for the chemical industry are started, Since it can be applied to fiber raw materials for composite materials and has extremely good cold workability, it can be applied to a wide range of fields such as stainless steel foil materials and plate materials processed into complex shapes. It is extremely large.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 竹内 英麿 山口県光市大字島田3434番地 新日本製鐵 株式会社光製鐵所内 (56)参考文献 特開 昭62−99436（ＪＰ，Ａ) 特開 昭62−124220（ＪＰ，Ａ) 特開 昭64−53704（ＪＰ，Ａ) 特開 平１−92342（ＪＰ，Ａ) 特開 平１−298115（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Hidemaru Takeuchi 3434 Shimada, Hikari City, Yamaguchi Prefecture, Nippon Steel Works, Ltd. Hikari Steel Works (56) References JP 62-99436 (JP, A) Special Kai 62-124220 (JP, A) JP 64-53704 (JP, A) JP 1-92342 (JP, A) JP 1-298115 (JP, A)
Claims (2)
％,Mn:0.2〜2.5％,P≦0.045％,S≦0.020％,Ni:6〜20％,
Cr:15〜25％,N:0.01〜0.05％,Al:0.0005〜0.005％,Ca:
0.0001〜0.002％,Mg:0.0001〜0.001％,O≦0.0025％を含
有し、残部Feおよび不可避的不純物からなるオーステナ
イト系ステンレス鋼の熱間圧延素材を、1000℃以上1300
℃以下の温度で10分以上加熱した後熱間圧延することに
より、熱間圧延材における非金属介在物の組成を、重量
％にて、SiO2:20〜50％,MnO:15〜60％,Al2O3:3〜15％,C
aO:3〜25％,MgO:0.5〜10％とすることを特徴とする伸線
性ならびに冷間圧延性に優れたオーステナイト系ステン
レス鋼の製造方法。1. C: 0.005 to 0.10% by weight%, Si: 0.2 to 1.0
%, Mn: 0.2 to 2.5%, P ≤ 0.045%, S ≤ 0.020%, Ni: 6 to 20%,
Cr: 15-25%, N: 0.01-0.05%, Al: 0.0005-0.005%, Ca:
Austenitic stainless steel hot-rolled material containing 0.0001 to 0.002%, Mg: 0.0001 to 0.001%, O ≤ 0.0025%, and balance Fe and unavoidable impurities.
The composition of the non-metallic inclusions in the hot-rolled material, in% by weight, is SiO 2 : 20-50%, MnO: 15-60% by hot rolling after heating at a temperature of ℃ or less for 10 minutes or more. , Al 2 O 3 : 3-15%, C
aO: 3 to 25%, MgO: 0.5 to 10%, a method for producing an austenitic stainless steel having excellent wire drawability and cold rollability.
％,Mn:0.2〜2.5％,P≦0.045％,S≦0.020％,Ni:6〜20％,
Cr:15〜25％,N:0.01〜0.10％,Al:0.0005〜0.005％,Ca:
0.0001〜0.002％,Mg:0.0001〜0.001％,O≦0.0025％を含
有し、さらにMo:0.5〜3.5％およびCu:0.5〜3.5％の１種
または２種を含有し、残部Feおよび不可避的不純物から
なるオーステナイト系ステンレス鋼の熱間圧延素材を、
1000℃以上1300℃以下の温度で10分以上加熱した後熱間
圧延することにより、熱間圧延材における非金属介在物
の組成を、重量％にて、SiO2:20〜50％,MnO:15〜60％,A
l2O3:3〜15％,CaO:3〜25％,MgO:0.5〜10％とすることを
特徴とする伸線性ならびに冷間圧延性に優れたオーステ
ナイト系ステンレス鋼の製造方法。2. C: 0.005 to 0.10% by weight%, Si: 0.2 to 1.0
%, Mn: 0.2 to 2.5%, P ≤ 0.045%, S ≤ 0.020%, Ni: 6 to 20%,
Cr: 15-25%, N: 0.01-0.10%, Al: 0.0005-0.005%, Ca:
0.0001 to 0.002%, Mg: 0.0001 to 0.001%, O ≤ 0.0025%, 1 or 2 kinds of Mo: 0.5 to 3.5% and Cu: 0.5 to 3.5%, balance Fe and unavoidable impurities Austenitic stainless steel hot rolled material consisting of
By heating for 10 minutes or more at a temperature of 1000 ° C or more and 1300 ° C or less and then hot rolling, the composition of the non-metallic inclusions in the hot rolled material, in% by weight, SiO 2 : 20 to 50%, MnO: 15-60%, A
l 2 O 3: 3~15%, CaO: 3~25%, MgO: drawability and manufacturing method of austenitic stainless steel excellent in cold rollability, characterized in that 0.5 to 10%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1194366A JPH0762171B2 (en) | 1989-07-28 | 1989-07-28 | Method for producing austenitic stainless steel excellent in wire drawability and cold rollability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1194366A JPH0762171B2 (en) | 1989-07-28 | 1989-07-28 | Method for producing austenitic stainless steel excellent in wire drawability and cold rollability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0361322A JPH0361322A (en) | 1991-03-18 |
| JPH0762171B2 true JPH0762171B2 (en) | 1995-07-05 |
Family
ID=16323390
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1194366A Expired - Lifetime JPH0762171B2 (en) | 1989-07-28 | 1989-07-28 | Method for producing austenitic stainless steel excellent in wire drawability and cold rollability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0762171B2 (en) |
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| FR2778188B1 (en) * | 1998-04-29 | 2000-06-02 | Ugine Savoie Sa | STAINLESS STEEL FOR MAKING DRAWN WIRE IN PARTICULAR TIRE REINFORCEMENT WIRE AND METHOD FOR MAKING THE SAME WIRE |
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Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62124220A (en) * | 1985-07-17 | 1987-06-05 | Nippon Steel Corp | Manufacture of stainless steel plate |
| JPH0674484B2 (en) * | 1985-10-26 | 1994-09-21 | 新日本製鐵株式曾社 | High cleanliness steel |
| JP2691713B2 (en) * | 1987-08-22 | 1997-12-17 | 新日本製鐵株式会社 | Method for producing Cr-Ni-based stainless steel having excellent hot workability |
| JPH0192342A (en) * | 1987-10-05 | 1989-04-11 | Kawasaki Steel Corp | Austenitic stainless steel plate having excellent deep drawability |
| JPH01298115A (en) * | 1988-05-26 | 1989-12-01 | Sumitomo Electric Ind Ltd | Production of high strength stainless steel wire |
-
1989
- 1989-07-28 JP JP1194366A patent/JPH0762171B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111155024A (en) * | 2020-01-19 | 2020-05-15 | 江苏省沙钢钢铁研究院有限公司 | Method for controlling ultralow-melting-point plastic inclusions of cord steel |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0361322A (en) | 1991-03-18 |
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