JPS58185722A - Manufacture of austenitic steel plate and band steel - Google Patents
Manufacture of austenitic steel plate and band steelInfo
- Publication number
- JPS58185722A JPS58185722A JP57065438A JP6543882A JPS58185722A JP S58185722 A JPS58185722 A JP S58185722A JP 57065438 A JP57065438 A JP 57065438A JP 6543882 A JP6543882 A JP 6543882A JP S58185722 A JPS58185722 A JP S58185722A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- less
- cold
- rolled
- hot
- 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.)
- Granted
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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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 Sheet Steel (AREA)
- Hard Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
本発明祉オーステナイト鋼板および銅帯の製造方法ＫＩ
Ｉ！するものである。[Detailed description of the invention] Method for producing austenitic steel sheet and copper strip of the present invention KI
I! It is something to do.
低温用鋼としては常温から一１００℃程度まではフェラ
イト鋼が使用され実用化されている。しかし、強磁性の
九め、特に磁気を嫌う構造用部材としては不適である。Ferritic steel is used as a low-temperature steel for temperatures from room temperature to about -100° C. and has been put into practical use. However, it is unsuitable for use as a structural member that is ferromagnetic and particularly dislikes magnetism.
一方、８ＵＩｉ ３０４（１８チＣｒ−ＩＮＩＮｌｍ）
で代表されるオーステナイト系ステンレス鋼は低温靭性
に優れｔ・つ非磁性であるが、高価である。このような
背景のもとに安価かつ非磁性のオーステナイト鋼の研究
が行なわれ、高価な組をＭＩ＆で置換した鋼が開発され
た。（例えば特公昭４９−１０８９２号公輸、＊公昭５
５−５１４２３号公報参照）しかし、これらは全て熱間
圧延鋼材に関するものである。On the other hand, 8UIi 304 (18chi Cr-ININlm)
Austenitic stainless steels, represented by , have excellent low-temperature toughness and are non-magnetic, but are expensive. Against this background, research has been carried out on inexpensive and non-magnetic austenitic steel, and a steel has been developed in which the expensive pair is replaced with MI&. (For example, Special Public Transport No. 49-10892, *Kokusho 5
(See Japanese Patent No. 5-51423) However, all of these relate to hot rolled steel materials.
最近、核−合朦Φ発電などの将来のエネルギー開発分野
の基礎応用研究のうち、陽子、電子の加速、プラズマ閉
じ込めに匣大な超電導磁石などが必要とされる。それら
の構造部材に非磁性鋼のニーズがよ〉高まっている０％
に、磁気損失、低温靭性の観点から３−以下の薄板を重
ね合わせ九積層構造も注目されている。このような板を
熱間圧延で製造すると、圧嬌機に対する負荷が極めて高
くなるにかりてなく、形状的には平坦度が悪く板を重ね
合わせ九場合の整合性に問題を生じ申す八本発明者らは
以上のような従来法の欠点を補うとともに安価かつさら
に高強度化した材料を得る事を目的として研究した結果
、組をＭ、で置換する事によシ安価でかつ安定した非磁
性鋼が得られ、また熱関圧蝙後２０９６以上の冷間圧延
を加える事によυ形状が優れ、かつ最終焼鈍後の結晶粒
の微細化により高強度化された材料が得られる事を見出
した。Recently, in basic applied research in future energy development fields such as nuclear-combined Φ power generation, large superconducting magnets are required for proton and electron acceleration and plasma confinement. The need for non-magnetic steel for these structural members is increasing.0%
In addition, from the viewpoint of magnetic loss and low-temperature toughness, a nine-layer structure in which three or less thin plates are stacked is also attracting attention. If such plates were manufactured by hot rolling, the load on the pressing machine would be extremely high, and the shape would be poor in flatness, causing problems with consistency when stacking the plates. The inventors conducted research with the aim of compensating for the drawbacks of the conventional method as well as obtaining a material that is inexpensive and has even higher strength.The inventors found that by replacing the set with M, an inexpensive and stable material was developed. Magnetic steel can be obtained, and by applying cold rolling of 2096 or more after hot rolling, a material with excellent υ shape and high strength can be obtained by refining the grains after final annealing. I found it.
すなわち、本発明の要旨とするところは王妃のとおシで
ある。In other words, the gist of the present invention is the queen's gift.
（１） Ｃ： ０．７０１１１下、ｌｌｌ５：２．５
１６以下、 Ｍａｒ ：９〜３５９Ｇ、 Ｃｒ ： ０
．５〜１９１Ｇ 、 Ｎ１ ： ８ ％以下、Ｎ：ｏ、
ｓｏｓ以下、ムｔ：２、〇−以下、 Ｃａ ： ０．０
２％以下を含有し残部が鉄および不可避的不純物からな
る鋼片を熱間および２〇−以上の冷間圧延を行なった後
、８００−１１６０℃で焼鈍する事を特徴とする冷関圧
嬌オー誠テナイト鋼板および銅帯の製造方法。(1) C: below 0.70111,ll5:2.5
16 or less, Mar: 9-359G, Cr: 0
．． 5-191G, N1: 8% or less, N: o,
SOS or less, Mut: 2, 〇- or less, Ca: 0.0
A cold rolling process characterized in that a steel billet containing 2% or less and the remainder consisting of iron and unavoidable impurities is hot-rolled and then cold-rolled to a temperature of 20 or more and then annealed at 800-1160°C. Method for manufacturing austenitic steel sheets and copper strips.
（２） Ｃ： ０．７０１１以下、８１：２５−以下
、 Ｋｍ ：９〜３５Ｉｓ、Ｃｒ ： ０．５〜１９％
、 Ｎｉ ： ８−以下、Ｎ：０５０ｓ以下、
Ａｊ ： ２．０−以下、 Ｃａ ： ０．０２−以下
に加えてＭＯ，Ｗ 、 ＣＩ 、 Ｃｍ 、 Ｎｂ 、
Ｔ１ 、 Ｖ 、 Ｚｒ ０１１１ま九は２種以上を
Ｍ・＊ ” ｅ Ｃ＠＠ ＣＩについては総量で０．０
１〜４０％ 、 Ｎｂ 、 Ｔｉ 、 Ｖ 、 Ｚｒ
Ｋ”：）イｌは総量で００１〜１５１Ｇを含有し、残部
が鉄および不可避的不純物からなる銅片を熱間および２
０チ以上の冷間圧延を行なった後、８００〜１１５０℃
で焼鈍する事を特徴とする冷間圧延オーステナイト鋼板
および鋼帯の製造方法。(2) C: 0.7011 or less, 81:25 or less, Km: 9-35Is, Cr: 0.5-19%
, Ni: 8- or less, N: 050s or less,
Aj: 2.0- or less, Ca: 0.02- or less, in addition to MO, W, CI, Cm, Nb,
For T1, V, Zr 0111, two or more types are M・*” e C@@CI, the total amount is 0.0
1-40%, Nb, Ti, V, Zr
K":)I is a copper piece containing 001 to 151G in total, with the remainder being iron and unavoidable impurities.
800-1150°C after cold rolling of 0.
A method for producing cold-rolled austenitic steel sheets and steel strips, which is characterized by annealing.
以下本発明を構成する鋼の成分と製造方法につ璽。The composition and manufacturing method of the steel constituting the present invention are described below.
いて詳細に説明する。This will be explained in detail.
Ｃはオーステナイト相を安定にし、強度を向上させるが
、ｆＩＩＩ接性、＊に溶接部の靭性を劣化させる傾向が
ある。溶接性を良好に膳持するために上限を０，７０チ
とした。C stabilizes the austenite phase and improves the strength, but tends to deteriorate the toughness of the welded joint. In order to maintain good weldability, the upper limit was set to 0.70 inches.
８１は脱酸剤として製鋼上必要であるとともに強度を向
上させる。しかし過剰の含有はフェライト相を生成しや
すくする。このため上限を２．５ｓとし友。81 is necessary for steel manufacturing as a deoxidizing agent and improves strength. However, excessive content tends to generate a ferrite phase. For this reason, I decided to set the upper limit to 2.5s.
Ｍ墓はオーステナイト相を得る丸めに有効な元素であシ
、オーステナイトで非磁性を得るためにはＭｎ ９チ以
上が必要である。ｔた、３５％を超えるとその効果紘飽
和する九めＭｍの範囲を９〜３５−とじ九〇
ＣｒはＭｎと同様、安定なオーステナイト相を得るのに
必要な元素て、その下Ｉｉｌは０．５−である。しかし
、１９ｓを超えるとフェライト相が生威しやすくなるた
め上限を１９％としえ、ｉた、Ｃｒ１ｄ耐食性を向上す
る元素であシ、その点でも上記の範囲が好ましい。Mn is an effective element for rounding to obtain an austenite phase, and Mn of 9 or more is required to obtain nonmagnetism in austenite. In addition, if it exceeds 35%, the effect saturates in the range of 9 to 35%.90 Cr, like Mn, is an element necessary to obtain a stable austenite phase, and below that, Iil is 0. .5-. However, if the content exceeds 19s, the ferrite phase tends to grow, so the upper limit is set at 19%.It is also an element that improves Cr1d corrosion resistance, and from that point of view as well, the above range is preferable.
Ｎｉはオーステナイト相を安定にし、熱間圧気鋼材の靭
性を向上させる。しかし、本発明におけるＭｎ、 Ｃｒ
の適当量の組合せによシ、オーステナイトを得るための
Ｎ１の上限は８ｓである。これ以上のＮ１はオーステナ
イト化に対して過剰であるばか抄でなく、大幅なコスト
ア、ｌを招き、有効でない、よってＮｌの上限を８ｓと
した。Ni stabilizes the austenite phase and improves the toughness of hot pressure steel materials. However, in the present invention, Mn, Cr
The upper limit of N1 to obtain austenite by combining appropriate amounts of is 8s. A N1 higher than this is not an excessive amount for austenitization, but also causes a large cost increase and is not effective.Therefore, the upper limit of N1 was set at 8 s.
ＮはＣと同様にオーステナイト相を安定にし、また強度
を向上させる。しかし、０．５０−を超えると＃ＩＩ接
熱影響部の靭性を劣化させる。このためＮの上限を０５
０％とした。Like C, N stabilizes the austenite phase and improves strength. However, when it exceeds 0.50-, the toughness of the #II heat affected zone deteriorates. Therefore, the upper limit of N is set to 05
It was set to 0%.
Ａｊは８１と同様、強力な脱酸元素であるとともに、窒
化物として析出して結晶粒の粗大化を防止する効果があ
シ、強度を向上させる。しかし、２，０％を超えると効
果が飽和する。このため、ＵＯ上訳を２０ｇ６とした。Like 81, Aj is a strong deoxidizing element, and also has the effect of precipitating as a nitride to prevent coarsening of crystal grains, thereby improving strength. However, if it exceeds 2.0%, the effect is saturated. Therefore, the UO equivalent was set to 20g6.
Ｃａは熱間加工性を向上させるのに有効な元素である。Ca is an effective element for improving hot workability.
しかし過剰の含有は清浄度を低下させるので上限を０．
０２−とじた。However, excessive content reduces cleanliness, so the upper limit should be set at 0.
02- Closed.
本発明は上記の成分組成で構成される鋼片の他さらに必
要に応じて前記成分に加えてＭｏ 、 Ｗ 。In addition to the steel billet having the above-mentioned composition, the present invention further contains Mo and W in addition to the above-mentioned composition as necessary.
ＣＩ 、 Ｃｍ 、 Ｗｂ 、 ＴＩ 、 Ｖ、 Ｚｒ
Ｃ）１種または２種以上を含有する鋼片を使用する。CI, Cm, Wb, TI, V, Zr
C) Use a steel billet containing one or more types.
ＭＯ、Ｗ 、 Ｃｔｓ 、 Ｃ髄、 Ｎｂ 、 Ｔｉ
、 Ｖ 、 Ｚｒはオーステナイト地の強度を向上させ
るばかシでなく脚。MO, W, Cts, C, Nb, Ti
, V, and Zr are not just for improving the strength of austenite.
窒化物として析出し、結晶粒の粗大化を抑制する効果が
ある。従って、熱間加工性、靭性の劣化をまねかない範
囲で、ＭＯＩＷ、Ｃ・、 Ｃｍについては総量で０．０
１〜４．（ＮＧｔたＮｂ 、 Ｔｉ 、 Ｖ 、 Ｚｒ
Ｋツイテは総量で０．０１〜１．５チを含有させる。It precipitates as a nitride and has the effect of suppressing coarsening of crystal grains. Therefore, within the range that does not cause deterioration of hot workability and toughness, the total amount of MOIW, C・, and Cm is 0.0.
1-4. (NGtNb, Ti, V, Zr
K-tweet contains 0.01 to 1.5 inches in total.
以上の他に、不可避的不純物としてｐ、ｓ等はそれぞれ
０．０８％以下であることが好ましい。In addition to the above, unavoidable impurities such as p and s are each preferably 0.08% or less.
本発明に従り九冷関圧銀鋼板および鋼帯は次の様にして
製造される。すなわち、転炉、電気１尋の溶解炉を用い
、さらに必要に応じ真空脱ｆス装置を用いてｆ＃ｒＩ！
！された溶鋼を造塊９分ａあるいは連続鋳造を経て鋼片
とする。続いて、この鋼片を熱間圧延し、熱間圧延鋼帯
とする。この時の仕上温度は５００℃以上が好ましい、
また、熱間圧延終了後の冷却は空冷、水冷等いかなる冷
却方法でもよい。その後、仁の熱間圧弛鋼帯を必要に応
じて軟化焼鈍し、続いて１回もしくは２回冷関圧嬌する
。なお、１回冷延の楊合社圧下率を２０９６以上とし、
２回冷延の場合は２目目の冷気の圧下率を２０−以上と
する。さらに、この冷間圧延銅帯を８００〜１１５０℃
で焼鈍を行なって冷間圧延銅帯もしくは鋼板成品とする
。焼鈍後の冷却は水冷−五８ｔＬいが、空冷でもよい。According to the present invention, Kurei-Kan pressed silver steel plates and steel strips are manufactured as follows. That is, f#rI! is produced using a converter, a melting furnace with an electric capacity of 1 fathom, and, if necessary, a vacuum de-fusing device.
! The resulting molten steel is made into steel billets through ingot making or continuous casting. Subsequently, this steel piece is hot rolled to form a hot rolled steel strip. The finishing temperature at this time is preferably 500°C or higher.
Further, cooling after hot rolling may be performed by any cooling method such as air cooling or water cooling. Thereafter, the hot-rolled steel strip is softened and annealed if necessary, and then cold-rolled once or twice. In addition, the Yanghesha rolling reduction ratio of one cold rolling is 2096 or more,
In the case of two-time cold rolling, the rolling reduction ratio of the second cold air is set to 20- or more. Furthermore, this cold rolled copper strip is heated to 800 to 1150℃.
The product is then annealed to produce a cold rolled copper strip or steel sheet product. Cooling after annealing is water cooling - 58 tL, but air cooling may be used.
本発明の特徴である冷間圧延による製造法は今までの熱
間圧ｋＬＫよる方法と異なり、冷間圧延することによ〉
その後の焼鈍後のオーステナイトの結晶粒を制御するこ
とができることにある。オーステナイトの強度は結晶粒
径に依存しており、結晶粒が黴細なほど強度が高くなる
。すなわち、冷間圧延をするととＫよって歪蓄積を増大
させ、焼鈍時の再結晶核が多く発生する。さらに、冷間
圧延によシ導入された転位および積層入路によシ、焼鈍
の際の昇温壕九祉保定時ｙｃ微細な炭、窒化物が粒内に
析出する。The manufacturing method using cold rolling, which is a feature of the present invention, is different from the conventional method using hot rolling kLK.
It is possible to control the austenite crystal grains after subsequent annealing. The strength of austenite depends on the crystal grain size, and the finer the crystal grains, the higher the strength. That is, cold rolling increases strain accumulation due to K, and many recrystallization nuclei are generated during annealing. Furthermore, due to dislocations introduced by cold rolling and lamination paths, fine carbon and nitrides precipitate within the grains during heating and holding during annealing.
以上のようＫ、冷間圧延を行なう事によシ、冷間圧延銅
帯の焼鈍時に再結晶核が多く発生するとともに、微細析
出物によシ結晶粒の成長が抑制される丸め極めて黴細な
結晶粒を得る事ができ高強度化が可能である。このよう
に、本発明Ｆｉ完全オーステナイトとしておいて、それ
にムｔさらに必要に応じてＮｂ 、 Ｔ１などの細粒化
元素を加え、これに冷間圧延工程を組合わせることによ
って材料を高強度化するものである。As mentioned above, by performing cold rolling, many recrystallized nuclei are generated during annealing of the cold rolled copper strip, and the growth of crystal grains is suppressed by fine precipitates. It is possible to obtain crystal grains with high strength. In this way, the present invention Fi is made into complete austenite, and if necessary, grain refining elements such as Nb and T1 are added to it, and this is combined with a cold rolling process to increase the strength of the material. It is something.
第１図は２５ ＩｓＭｎ −５１１ｃｒ−１１Ｎｉ −
０，０４％Ｎ鋼を熱間圧延後、種々の圧下率で冷間圧延
し、さらに１０００℃で１分間焼鈍後水冷した時の機械
的性質を示したものである。冷間圧延したものは冷間圧
延しないものに比べ結晶粒が細かく強度が高い。また、
冷間圧延を行なっても圧下率が２０１１未満であると十
分な歪が蓄積されず、焼鈍時に再結晶核の発生が少く、
炭、窒化物も微細に析出しない、このため、結晶粒が粗
大化しゃすく、強度も低い、従って焼鈍直前の冷間圧延
の圧下率は２０９１以上であることが必要である０％に
、４ｏＩｓ以上の圧下率で安定して黴細な結晶粒が得ら
れる。Figure 1 shows 25 IsMn -511cr-11Ni -
The mechanical properties of 0.04% N steel were hot rolled, then cold rolled at various rolling reductions, further annealed at 1000° C. for 1 minute, and then water cooled. Cold-rolled products have finer grains and higher strength than non-cold-rolled products. Also,
Even if cold rolling is performed, if the reduction ratio is less than 2011, sufficient strain will not be accumulated, and less recrystallization nuclei will occur during annealing.
Carbon and nitrides do not precipitate finely, so the crystal grains become coarse and the strength is low.Therefore, the rolling reduction in cold rolling immediately before annealing must be 2091 or more. At the above rolling reduction ratio, fine crystal grains can be stably obtained.
第２図は２５ ％ｋｌｈ −５１ＩＣｒ −１１１Ｎｉ
−０，０４＄Ｎ鋼を冷関圧砥後、種々の温度で１分間
および５分間焼鈍後、水冷し九時の機械的性質を示した
ものである。８００℃未満のｗ８鈍では未再結晶であシ
、伸びも低く薄板として必要な加工性に劣る・また１１
１５０℃を超えると結晶粒が粗大化して構造用材料とし
て必要な強度が低下する。この傾向は５分以下の殻時間
焼鈍では焼鈍時間による差は明瞭でない、また、５分を
起えるような長時間焼鈍では生産性およびｌｉＩ済性に
おいて不適当である。上記の如く焼鈍温度としてｔ′１
８００〜１１５０℃が適正である。Figure 2 shows 25% klh -51ICr -111Ni
The mechanical properties of -0.04$N steel are shown after cold pressure grinding, annealing at various temperatures for 1 minute and 5 minutes, and then water cooling. If W8 is dulled at less than 800℃, it will not be recrystallized, and the elongation will be low and the workability required as a thin plate will be poor.
If the temperature exceeds 150°C, the crystal grains become coarse and the strength required as a structural material decreases. This tendency shows that when the shell time is annealed for less than 5 minutes, the difference due to the annealing time is not clear, and when the shell time is annealed for 5 minutes, it is inappropriate in terms of productivity and processability. As mentioned above, the annealing temperature is t'1
A temperature of 800 to 1150°C is appropriate.
次に本発明の実施例にりいてａ９１Ｊｆる。Next, let us look at an embodiment of the present invention.
第１表は電気炉で＊ａされ丸鋼について、成分。Table 1 shows the composition of round steel processed in an electric furnace.
冷間加工率お↓び冷蝙後の焼鈍温度と材質特性の関係を
駒ぺ九ものである。但し焼鈍時間は１分間である。The relationship between cold working rate, annealing temperature after cold rolling, and material properties is explained in detail. However, the annealing time is 1 minute.
本発明法によればいずれも０．２チ耐力が２５ゆｆ／Ｉ
ＩＫ２以上で、伸びが５０−以上を示し、さらに良好な
熱間加工性を示し、形状も良好である。また、透磁率も
非磁性構造用として優れた値を示している。According to the method of the present invention, the 0.2 inch proof stress is 25 Yuf/I in both cases.
It has an IK of 2 or more, an elongation of 50 or more, good hot workability, and a good shape. The magnetic permeability also shows an excellent value for use in non-magnetic structures.
これに対し、比較法１，２はＣａを含有しておらず、本
発明法による場合とほぼ同等の機械的性質を示すが、熱
間加工性に劣る。On the other hand, Comparative Methods 1 and 2 do not contain Ca and exhibit almost the same mechanical properties as the method of the present invention, but are inferior in hot workability.
比較法３，４は冷延後の焼鈍温度が、本発明法の下限を
下まわっており、伸びが本発明法による場合よシ低く、
二次加工性に劣る。In Comparative Methods 3 and 4, the annealing temperature after cold rolling is lower than the lower limit of the method of the present invention, and the elongation is lower than that of the method of the present invention.
Poor secondary processability.
比較法５は焼鈍温度が本発明法範囲の上限を超えており
、０．２チ耐力、引張強さとも本発明法による場合よシ
低く、構造用部材として適さない。In Comparative Method 5, the annealing temperature exceeds the upper limit of the range of the method of the present invention, and both the 0.2 mm proof stress and tensile strength are lower than those obtained by the method of the present invention, making it unsuitable for use as a structural member.
比較法６は冷間圧延を省略しているため、比較法７は冷
間加工率が低いため、いずれも形状が悪くまた強度が低
いため構造用部材として不適である。Comparative method 6 omits cold rolling, and comparative method 7 has a low cold working rate, so both have poor shapes and low strength, making them unsuitable as structural members.
第１図ｕ ０．０２５ＧＣ−０，８６％８１−２５．６
％Ｍｍ −０，９７％Ｎ１−４．６７％Ｃｒ−０，０４
１１Ｎ鋼のスラブを１２００℃に加熱、均熱後、熱間圧
延し、０〜８０９Ｉの圧下率の冷間圧延した後、１ｏｏ
ｏ℃で１分間焼鈍後１水冷した鋼材の冷間圧延の圧下率
と機械的性質の関係を示す図、第２図は第１図と同様に
して製造した熱間圧延鋼材を圧下率７０９Ｇで冷間圧延
した抜、７００〜１２５０℃の各温度で１分間（Ｏ印）
および５分間（・印）ｗ８鈍した鋼材の焼鈍温度と引張
特性の関係を示す図である。
第１回
′Ｌ 没＠圧延６下卑Ｃ％）
第２ 図
ｉａｉ良Ｃ°０）Figure 1 u 0.025GC-0.86%81-25.6
%Mm -0,97%N1-4.67%Cr-0,04
A slab of 11N steel was heated to 1200°C, soaked, hot rolled, cold rolled with a rolling reduction of 0 to 809I, and then 1oo
A diagram showing the relationship between cold rolling reduction and mechanical properties of steel materials annealed at 0°C for 1 minute and then water-cooled. Figure 2 shows the relationship between hot rolled steel manufactured in the same manner as in Figure 1 at a reduction ratio of 709G. Cold-rolled drawing, 1 minute at each temperature of 700 to 1250℃ (O mark)
FIG. 3 is a diagram showing the relationship between the annealing temperature and tensile properties of steel materials annealed for 5 minutes (marked with *) w8. 1st 'L sink @rolling 6 lower C%) 2nd figure iai good C°0)
Claims (2)
下、 Ｍｅ ：９〜３５！Ｊ 、 Ｃｒ ： ０．５〜
１９％ −Ｎｉ ： ８１以下、Ｎ：０．５０ｓ以下、
Ａｔ ： ２．０−以下、 Ｃａ ： ０．０２ｓ以
下ヲ含有し、残部が鉄および不可避的不純物からなる鋼
片を熱間圧延および２〇−以上の冷間圧延を行なった後
、８００〜１１５０℃で焼鈍する事を特徴とする冷間圧
延オーステナイト鋼板および銅帯の製造方法。(1) C: 0.7 (1% or less, Si: 2.5- or less, Me: 9-35!J, Cr: 0.5-
19% -Ni: 81 or less, N: 0.50s or less,
A steel piece containing At: 2.0 or less, Ca: 0.02s or less, and the remainder consisting of iron and unavoidable impurities is hot rolled and cold rolled at 20 or more. A method for producing cold-rolled austenitic steel sheets and copper strips, characterized by annealing at ℃.
以下、 Ｍ諏：９〜３５’ｌＧ 、 Ｃｒ ： ０．
５〜１９％、Ｎｉ：８１以下、Ｎ：０．５０％以下、
ＡＡ ： ２．０１１６以下、 Ｃａ ： ０．０２１
６以下に加えて、Ｍｏ 、 Ｗ 、 Ｃｏ 、 Ｃａ
＊ Ｎｂ 、 Ｔｉ 、 Ｖ 、 Ｚｒの１種ｉ九は２
種以上をＭｅ 、 Ｗ 、 Ｃｏ 、 Ｃ髄については
総量で０．０１〜４．０％、Ｎｂ 、 ＴＩ 、 Ｖ
、 ＺｒＫツィては総量で０．０１〜１．５１６’を含
有し、残部が鉄および不可避的不純物からなる鋼片を熱
関圧嬌および２〇嗟以上の冷間圧延を行なった後、８０
０〜１１５０℃で焼鈍する事を％黴とする冷間圧延オー
ステナイト鋼板および銅帯の製造方法。(2) C: 0.701 or less, Si: 2.511
Below, M: 9-35'lG, Cr: 0.
5 to 19%, Ni: 81 or less, N: 0.50% or less,
AA: 2.0116 or less, Ca: 0.021
In addition to 6 or less, Mo, W, Co, Ca
*Type 1 i9 of Nb, Ti, V, and Zr is 2
The total amount is 0.01-4.0% for Me, W, Co, C pulp, Nb, TI, V
A steel piece containing a total of 0.01 to 1.516' of ZrK, with the remainder consisting of iron and unavoidable impurities, is subjected to hot compression and cold rolling for more than 20 hours, and then
A method for producing cold-rolled austenitic steel sheets and copper strips by annealing at 0 to 1150°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP57065438A JPS6054374B2 (en) | 1982-04-21 | 1982-04-21 | Method for manufacturing austenitic steel plates and steel strips |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP57065438A JPS6054374B2 (en) | 1982-04-21 | 1982-04-21 | Method for manufacturing austenitic steel plates and steel strips |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS58185722A true JPS58185722A (en) | 1983-10-29 |
| JPS6054374B2 JPS6054374B2 (en) | 1985-11-29 |
Family
ID=13287125
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP57065438A Expired JPS6054374B2 (en) | 1982-04-21 | 1982-04-21 | Method for manufacturing austenitic steel plates and steel strips |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6054374B2 (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6247428A (en) * | 1985-08-28 | 1987-03-02 | Nippon Kokan Kk <Nkk> | Manufacture of mn stainless steel having high strength and toughness at 4.2k |
| JPS63203753A (en) * | 1987-02-19 | 1988-08-23 | Hitachi Metals Ltd | Age hardening austenitic tool steel |
| JPH08503699A (en) * | 1992-12-08 | 1996-04-23 | プロ − ニューロン，インコーポレーテッド | Pyrimidine nucleotide precursors for the treatment of systemic inflammation and inflammatory hepatitis |
| DE102009003598A1 (en) * | 2009-03-10 | 2010-09-16 | Max-Planck-Institut Für Eisenforschung GmbH | Corrosion-resistant austenitic steel |
| US20120070330A1 (en) * | 2008-11-05 | 2012-03-22 | Klaus Brokmeier | High-strength steel sheet and the method for production therefor |
| DE102015112886A1 (en) * | 2015-08-05 | 2017-02-09 | Salzgitter Flachstahl Gmbh | High-strength aluminum-containing manganese steel, a process for producing a steel flat product from this steel and steel flat product produced therefrom |
| RU2694391C2 (en) * | 2014-09-29 | 2019-07-12 | Ниппон Стил Корпорейшн | Steel material and expandable pipes used in oil industry |
| CN113492153A (en) * | 2021-07-16 | 2021-10-12 | 山西太钢不锈钢股份有限公司 | Rolling method of austenitic stainless steel and austenitic stainless steel for electronic components |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6297397A (en) * | 1985-10-23 | 1987-05-06 | 松下電器産業株式会社 | Voice synthesizer |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5531810A (en) * | 1978-08-24 | 1980-03-06 | Nippon Zeon Co Ltd | Solventless epoxy resin composition |
-
1982
- 1982-04-21 JP JP57065438A patent/JPS6054374B2/en not_active Expired
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5531810A (en) * | 1978-08-24 | 1980-03-06 | Nippon Zeon Co Ltd | Solventless epoxy resin composition |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6247428A (en) * | 1985-08-28 | 1987-03-02 | Nippon Kokan Kk <Nkk> | Manufacture of mn stainless steel having high strength and toughness at 4.2k |
| JPH0138850B2 (en) * | 1985-08-28 | 1989-08-16 | Nippon Kokan Kk | |
| JPS63203753A (en) * | 1987-02-19 | 1988-08-23 | Hitachi Metals Ltd | Age hardening austenitic tool steel |
| JPH08503699A (en) * | 1992-12-08 | 1996-04-23 | プロ − ニューロン，インコーポレーテッド | Pyrimidine nucleotide precursors for the treatment of systemic inflammation and inflammatory hepatitis |
| US20120070330A1 (en) * | 2008-11-05 | 2012-03-22 | Klaus Brokmeier | High-strength steel sheet and the method for production therefor |
| US9267193B2 (en) * | 2008-11-05 | 2016-02-23 | Honda Motor Co., Ltd | High-strength steel sheet and the method for production therefor |
| DE102009003598A1 (en) * | 2009-03-10 | 2010-09-16 | Max-Planck-Institut Für Eisenforschung GmbH | Corrosion-resistant austenitic steel |
| RU2694391C2 (en) * | 2014-09-29 | 2019-07-12 | Ниппон Стил Корпорейшн | Steel material and expandable pipes used in oil industry |
| DE102015112886A1 (en) * | 2015-08-05 | 2017-02-09 | Salzgitter Flachstahl Gmbh | High-strength aluminum-containing manganese steel, a process for producing a steel flat product from this steel and steel flat product produced therefrom |
| CN113492153A (en) * | 2021-07-16 | 2021-10-12 | 山西太钢不锈钢股份有限公司 | Rolling method of austenitic stainless steel and austenitic stainless steel for electronic components |
| CN113492153B (en) * | 2021-07-16 | 2023-01-31 | 山西太钢不锈钢股份有限公司 | Rolling method of austenitic stainless steel and austenitic stainless steel for electronic components |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6054374B2 (en) | 1985-11-29 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO2013133259A1 (en) | Ferrite-austenite 2-phase stainless steel plate having low in-plane anisotropy and method for producing same | |
| JPS61270356A (en) | Austenitic stainless steels plate having high strength and high toughness at very low temperature | |
| JPH0536481B2 (en) | ||
| JPS58185722A (en) | Manufacture of austenitic steel plate and band steel | |
| CN108823509A (en) | Ferritic stainless steel with superior oxidation resistance, good elevated temperature strength and good formability | |
| JPH06322440A (en) | Method for rolling high manganese nonmagnetic steel slab | |
| US6007642A (en) | Super low loss motor lamination steel | |
| CN101168169A (en) | Technology method for using thin slab for continuous casting and rolling to produce low-carbon high-niobium high-strength toughness steel belt | |
| JPS58171527A (en) | Manufacture of low-grade electrical steel sheet | |
| US20200087745A1 (en) | Ferritic stainless steel having excellent strength and corrosion resistance to acid and method of manufacturing the same | |
| US20220056550A1 (en) | Non-oriented electrical steel sheet and method for producing same | |
| JPS63166931A (en) | Manufacture of high tension hot rolled steel sheet having high magnetic flux density | |
| JPH06179922A (en) | Production of high tensile strength steel sheet for deep drawing | |
| JPS6148531A (en) | Manufacture of hot-rolled low-carbon steel sheet having superior deep drawability | |
| KR102328127B1 (en) | Non-oriented electrical steel sheet and method for manufacturing the same | |
| KR102438474B1 (en) | Non-oriented electrical steel sheet and method for manufacturing the same | |
| KR100276300B1 (en) | The manufacturing method of high strength hot rolling steel sheet with having low tensil strength | |
| JPS6173836A (en) | Manufacture of hot rolled steel sheet superior in workability | |
| JPH1112691A (en) | Ferritic stainless cold rolled steel sheet having excellent formability and its manufacture | |
| JPH0331420A (en) | Production of full-processed non-oriented electrical steel sheet having excellent magnetic characteristics | |
| JPH02104614A (en) | Manufacture of hot rolled steel sheet having high workability | |
| JPS5856012B2 (en) | Manufacturing method of ferrite single-phase stainless steel sheet that does not cause ridging | |
| JPH1025517A (en) | Production of iron-nickel alloy sheet | |
| JPS5677333A (en) | Production of composite structure type high ductility high strength cold-rolled steel plate | |
| US20240047105A1 (en) | Non-oriented electrical steel sheet |