JPH05148548A - Production of high-toughness ferritic stainless steel strip - Google Patents
Production of high-toughness ferritic stainless steel stripInfo
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- JPH05148548A JPH05148548A JP31493991A JP31493991A JPH05148548A JP H05148548 A JPH05148548 A JP H05148548A JP 31493991 A JP31493991 A JP 31493991A JP 31493991 A JP31493991 A JP 31493991A JP H05148548 A JPH05148548 A JP H05148548A
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- steel strip
- temperature
- ferritic stainless
- stainless steel
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- Heat Treatment Of Sheet Steel (AREA)
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、比較的多量のAlまた
はSiを含むフェライト系ステンレス鋼の高靱性熱延鋼帯
を製造する方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a high toughness hot rolled steel strip of ferritic stainless steel containing a relatively large amount of Al or Si.
【０００２】[0002]
【従来の技術】Alを含むフェライト系ステンレス鋼（例
えば、18Cr−３Al鋼）、Siを含むフェライト系ステンレ
ス鋼（例えば、18Cr−2.5Si 鋼、16.5Cr−2.0Si 鋼)
は、優れた耐食性、耐熱・耐酸化性の故に、近年、自動
車排ガス処理機器、ストーブ部品、フロッピーディスク
センターコア材等、多方面に用途が拡大している。しか
しながら、通常の熱間圧延条件で製造したこれらの鋼種
の熱延鋼帯（ホットコイル）は、熱延のままでは、極め
て靱性に乏しく、焼鈍後の手入れ（表面の疵取り）ライ
ン等でわずかな曲げ応力がかかっただけで破断するとい
う事故がおこりやすい。2. Description of the Related Art Ferritic stainless steel containing Al (eg 18Cr-3Al steel), ferritic stainless steel containing Si (eg 18Cr-2.5Si steel, 16.5Cr-2.0Si steel)
Due to its excellent corrosion resistance, heat resistance and oxidation resistance, has been used in various fields in recent years, such as automobile exhaust gas treatment equipment, stove parts, and floppy disk center core materials. However, hot-rolled steel strips (hot coils) of these steel types produced under normal hot rolling conditions have extremely poor toughness when hot-rolled, and are only slightly damaged by the maintenance (surface flaw removal) line after annealing. Accidents such as breakage are likely to occur even if a large bending stress is applied.
【０００３】図１中の▲印は 2.5％のSiと 0.3％のNbを
含有するフェライト系ステンレス鋼(後述の実施例の鋼
種ｂ)を、下記の通常の製造工程でコイルにしたもの、
即ち、熱延のままの試験片の室温(25 ℃) での衝撃値で
あるが、わずか１kgf-m/cm2強に過ぎない。後続工程で
の破断等の事故を避けるためには４kgf-m/cm2 以上の衝
撃値が必要とされるが、上記のように通常の熱延のまま
ではこの基準は到底満足されない。The ▲ mark in FIG. 1 is obtained by forming a coil from a ferritic stainless steel containing 2.5% Si and 0.3% Nb (steel type b in the example described later) in the following ordinary manufacturing process.
That is, the impact value at room temperature (25 ° C.) of the as-hot-rolled test piece is only 1 kgf-m / cm 2 or more. An impact value of 4 kgf-m / cm 2 or more is required to avoid accidents such as breakage in the subsequent process, but as mentioned above, this standard cannot be satisfied at all with normal hot rolling.
【０００４】スラブ加熱：1180℃×３時間 タンデムミルによる熱間圧延で、200 mm厚から4.0 mm
まで圧延 圧延仕上温度：950 ℃ 巻取温度： 600〜650 ℃（巻取り後は自然放冷） ホットコイルには、通常、結晶組織の均一化および軟質
化のためにベル焼鈍を施す。この焼鈍によって、衝撃値
はいくらか回復する。図１に、焼鈍温度と靱性との関係
を●で示す。焼鈍の均熱時間は12時間でその後は炉冷し
ている。図示のとおり、 700℃でベル焼鈍すれば衝撃値
は４kgf-m/cm2 前後に回復するが、必ずしも目標とする
４kgf-m/cm2 以上になるとは限らない。更に、焼鈍温度
が 770℃、830 ℃と高くなれば、衝撃値は２kgf-m/cm2
以下に低下してしまう。このような低靱性の鋼帯は、そ
れ自体を製品として出荷するにも不適当であり、これを
冷延鋼板の素材として使用する場合にも、先に述べたと
おり、後続の工程で破断等のトラブルを招く。Slab heating: 1180 ° C x 3 hours Hot rolling by tandem mill, 200 mm thickness to 4.0 mm
Rolling finishing temperature: 950 ° C Winding temperature: 600 to 650 ° C (natural cooling after winding) Hot coils are usually subjected to bell annealing in order to make the crystal structure uniform and soften. With this annealing, the impact value is somewhat recovered. In FIG. 1, the relationship between the annealing temperature and the toughness is indicated by ●. The soaking time for annealing is 12 hours, after which the furnace is cooled. As shown in the figure, the impact value recovers to around 4 kgf-m / cm 2 by bell annealing at 700 ℃, but it does not always reach the target value of 4 kgf-m / cm 2 or more. Furthermore, if the annealing temperature rises to 770 ℃ and 830 ℃, the impact value becomes 2kgf-m / cm 2
It drops below. Such a low toughness steel strip is unsuitable for shipping itself as a product, and even when it is used as a material for cold-rolled steel sheet, as described above, it breaks in the subsequent process. Cause trouble.
【０００５】本発明者は、上記図１の▲で示すような熱
延のままの鋼帯の靱性が低い原因は、熱間圧延後、巻取
りまでの冷却過程、および巻取り後の冷却過程で結晶粒
界に炭化物や金属間化合物が析出することにあると推測
した。そして、熱間圧延の仕上をできるだけ低温とし、
かつ巻取り温度も低くし、さらに巻取り後にコイルを水
冷することによって高靱性熱延鋼帯を製造できることを
確認した。しかし、このような方法で製造した靱性の高
い鋼帯であっても、後に詳述する図２に示すように、次
のベル焼鈍の条件が不適当であれば、靱性が再び低下し
てしまう。The inventor of the present invention causes the low toughness of the as-hot-rolled steel strip as shown by ▲ in FIG. 1 to be caused by the cooling process after hot rolling and before winding, and the cooling process after winding. It was assumed that carbides and intermetallic compounds were precipitated at the grain boundaries. And make the finish of hot rolling as low as possible,
It was also confirmed that the high toughness hot-rolled steel strip can be manufactured by lowering the coiling temperature and cooling the coil with water after coiling. However, even with a steel strip having high toughness manufactured by such a method, as shown in FIG. 2 which will be described in detail later, if the conditions for the next bell annealing are inappropriate, the toughness will be reduced again. ..
【０００６】[0006]
【発明が解決しようとする課題】本発明の目的は、従来
の製造方法では低靱性の熱延鋼帯しか得られないフェラ
イト系ステンレス鋼を対象として、ベル焼鈍の後の鋼帯
に室温での衝撃値が４kgf/cm2 以上となる高い靱性を持
たせる方法を提供することにある。SUMMARY OF THE INVENTION An object of the present invention is to target a ferritic stainless steel for which only a low-toughness hot-rolled steel strip can be obtained by a conventional manufacturing method, and the steel strip after bell-annealing at room temperature is used. It is intended to provide a method of imparting high toughness with an impact value of 4 kgf / cm 2 or more.
【０００７】[0007]
【課題を解決するための手段】本発明の要旨は『高Al系
または高Si系のフェライト系ステンレス鋼を仕上温度90
0 ℃以下で熱間圧延し、600 ℃以下で巻取り、巻取り後
直ちに水冷して得た鋼帯をベル焼鈍するに際し、焼鈍温
度を 700〜850 ℃とし、かつ焼鈍後 500℃以上の温度か
ら水冷することを特徴とする高靱性フェライト系ステン
レス鋼帯の製造方法』にある。[Means for Solving the Problems] The gist of the present invention is "a high Al-based or high Si-based ferritic stainless steel having a finishing temperature of 90
The steel strip obtained by hot rolling at 0 ° C or lower, winding at 600 ° C or lower, and water cooling immediately after winding was subjected to bell annealing at a temperature of 700 to 850 ° C and a temperature of 500 ° C or higher after annealing. The method for producing a high toughness ferritic stainless steel strip characterized in that it is water-cooled.
【０００８】本発明の対象となるフェライト系ステンレ
ス鋼とは、通常の熱間圧延とベル焼鈍では室温での衝撃
値が４kgf-m/cm2 に達しないものである。代表的な鋼種
としては、前述の18Cr−３Al鋼、18Cr−2.5 Si鋼、16.5
Cr−2.0 Si鋼の外、11Cr−2.0 Si鋼等がある。The ferritic stainless steel which is the object of the present invention is one in which the impact value at room temperature does not reach 4 kgf-m / cm 2 by ordinary hot rolling and bell annealing. Typical steel types include the aforementioned 18Cr-3Al steel, 18Cr-2.5 Si steel, 16.5
Besides Cr-2.0 Si steel, there are 11Cr-2.0 Si steel and the like.
【０００９】[0009]
【作用】本発明方法の特徴は、熱間圧延の仕上温度およ
び巻取り温度をともに低くし、巻取り後に直ちに水冷し
たコイルを、低温で焼鈍し、かつ水冷することにある。The method of the present invention is characterized in that the finishing temperature of hot rolling and the coiling temperature are both low, and the coil which is water-cooled immediately after coiling is annealed at a low temperature and water-cooled.
【００１０】以下、本発明の製造方法の諸条件について
詳論する。Hereinafter, various conditions of the manufacturing method of the present invention will be described in detail.
【００１１】(1) 熱間圧延：熱間圧延に供するスラブ
は、連続鋳造スラブでも分塊圧延スラブでもよい。スラ
ブ加熱温度も通常の範囲でよい。ただし、熱間圧延の仕
上温度は 900℃以下としなければならない。仕上温度が
900℃よりも高いと後述する低温巻取を行っても靱性は
向上しない。(1) Hot rolling: The slab used for hot rolling may be either a continuous cast slab or a slab of slabs. The slab heating temperature may also be in the usual range. However, the finishing temperature of hot rolling must be 900 ℃ or less. The finishing temperature is
If the temperature is higher than 900 ° C, the toughness will not be improved even if the low temperature winding described below is performed.
【００１２】仕上温度の下限は、熱間圧延が可能な限界
温度であり、鋼種によって異なるが、およそ 850℃程度
である。圧延終了後は、次の巻取り温度までできるだけ
急速に冷却するのがよい。The lower limit of the finishing temperature is the limit temperature at which hot rolling is possible, and it is about 850 ° C., although it depends on the steel type. After rolling, it is preferable to cool to the next coiling temperature as quickly as possible.
【００１３】(2) 巻取り：巻取温度は、可能な限り低温
であることが望ましい。600 ℃を超える温度では、たと
え水冷しても巻き取った後のコイルの冷却速度が小さく
なり粒界析出物が増加して靱性を損なう。(2) Winding: The winding temperature is preferably as low as possible. If the temperature exceeds 600 ° C, even if water-cooled, the coil cooling rate after winding becomes small, and grain boundary precipitates increase to impair toughness.
【００１４】巻取り後は、コイルを水冷する。冷却速度
としては20℃／秒以上が望ましい。After winding, the coil is cooled with water. The cooling rate is preferably 20 ° C / sec or more.
【００１５】これによってコイルの冷却過程での炭化物
や金属間化合物の析出が防止されて、靱性の高い鋼帯が
得られる。As a result, precipitation of carbides and intermetallic compounds during the coil cooling process is prevented, and a steel strip having high toughness can be obtained.
【００１６】(3) ベル焼鈍：ベル焼鈍は、700 〜850 ℃
の温度で行い、しかも焼鈍後は 500℃以上の温度から水
冷する。図２に示すのは、図１の試験で用いたと同じ
2.5％Si− 0.3％Nbフェライト系ステンレス鋼を仕上温
度 850℃で熱間圧延し、550 〜600 ℃で巻取り、その後
直ちに水冷して得た鋼帯を、横軸に示す各温度で 12 時
間ベル焼鈍し、焼鈍後炉冷（実線）した場合、および 5
50℃から水冷した場合（破線）の各鋼帯の室温での衝撃
値である。熱間圧延仕上温度およびを巻取温度を低く
し、かつ巻取り後は水冷したので、熱延のまま（As-Ho
t) の鋼帯は、８kgf-m/cm2 という高い衝撃値を示して
いる。しかし、これをベル焼鈍すると、焼鈍温度が高い
ほど衝撃値は低下する傾向を示す。特に、焼鈍後にその
まま炉中で徐冷した場合 (実線) には、その低下傾向が
著しく、焼鈍温度が 700℃を超えると４kgf-m/cm2 を割
ってしまう。しかし、焼鈍後に水冷するならば、焼鈍温
度が 850℃程度であっても、目標を上回る靱性を保持し
ている。この図から、靱性向上のためには焼鈍温度は低
い方が良いといえるが、ベル焼鈍の目的上、700 ℃以上
の温度は必要である。これより低温では結晶組織の整粒
化および炭化物の拡散が不十分となる。(3) Bell annealing: Bell annealing is 700 to 850 ° C.
At a temperature of 500 ° C or higher, and after annealing, cool it to a temperature of 500 ° C or higher with water. 2 shows the same as used in the test of FIG.
A 2.5% Si-0.3% Nb ferritic stainless steel was hot rolled at a finishing temperature of 850 ° C, wound at 550 to 600 ° C, and immediately water-cooled to obtain a steel strip for 12 hours at each temperature shown on the horizontal axis. Bell-annealed, furnace-annealed (solid line) after annealing, and 5
It is the impact value at room temperature of each steel strip when water cooling from 50 ° C (broken line). Since the hot rolling finishing temperature and the coiling temperature were lowered and water cooling was performed after coiling, hot rolling (As-Ho
The steel strip of t) shows a high impact value of 8 kgf-m / cm 2 . However, when this is subjected to bell annealing, the impact value tends to decrease as the annealing temperature increases. In particular, when the material is annealed in the furnace as it is after annealing (solid line), the decreasing tendency is remarkable, and when the annealing temperature exceeds 700 ° C, it falls below 4 kgf-m / cm 2 . However, if water cooling is performed after annealing, the toughness that exceeds the target is maintained even if the annealing temperature is about 850 ° C. From this figure, it can be said that a lower annealing temperature is better for improving toughness, but a temperature of 700 ° C or higher is necessary for the purpose of bell annealing. At temperatures lower than this, grain size control of the crystal structure and diffusion of carbides become insufficient.
【００１７】焼鈍温度を上記のように低くしても、焼鈍
後に従来のように炉冷すると、靱性は落ちてしまう。従
って、焼鈍後は、速やかに炉から取り出して、コイルを
水冷して急速冷却しなければならない。水冷開始温度
(炉からの取り出し温度) は、500 ℃以上とする必要が
ある。これより低温では水冷の効果が乏しい。Even if the annealing temperature is lowered as described above, if the furnace is cooled in the conventional manner after annealing, the toughness deteriorates. Therefore, after annealing, the coil must be quickly taken out of the furnace and water-cooled to be rapidly cooled. Water cooling start temperature
(Take-out temperature from furnace) must be 500 ℃ or more. At lower temperatures, the effect of water cooling is poor.
【００１８】図３は、図２の試験材の10000 倍の電子顕
微鏡像のスケッチである。（ａ）は750 ℃焼鈍した炉冷
材（図２の記号ａ）、（ｂ）は 750℃で焼鈍した水冷材
（図２の記号ｂ）である。（ａ）の炉冷材では、結晶粒
界にCr−Si−Nb−Fe等の金属間化合物が多量に析出して
おり、これが靱性低下の原因になっていると思われる。
これに対して、（ｂ）の水冷材（本発明方法で製造した
もの）では、上記の金属間化合物の粒界析出が殆どな
い。FIG. 3 is a sketch of an electron microscope image of the test material of FIG. (A) is a furnace-cooled material annealed at 750 ° C. (symbol a in FIG. 2), and (b) is a water-cooled material annealed at 750 ° C. (symbol b in FIG. 2). In the furnace cooling material of (a), a large amount of intermetallic compounds such as Cr-Si-Nb-Fe are precipitated at the crystal grain boundaries, which is considered to be the cause of the toughness reduction.
On the other hand, in the water-cooled material of (b) (produced by the method of the present invention), there is almost no intergranular precipitation of the above intermetallic compound.
【００１９】[0019]
【実施例】表１に示す化学組成の鋼をＶＯＤ炉で溶製
し、連続鋳造して得たスラブを表２に示す条件で熱間圧
延し、ベル焼鈍（すべて 12 時間均熱）を施した。な
お、熱間圧延では、連続鋳造スラブを冷却せずに加熱炉
に装入する、いわゆるホットチャージを行った。EXAMPLE Steels having the chemical composition shown in Table 1 were melted in a VOD furnace and continuously cast into slabs, which were hot-rolled under the conditions shown in Table 2 and subjected to bell annealing (soaking for 12 hours). did. In the hot rolling, so-called hot charging was performed by charging the continuous casting slab into the heating furnace without cooling it.
【００２０】表１の鋼種ａは18Cr−３Al系、鋼種ｂは18
Cr−2.5Si 系、鋼種ｃは16.5Cr−2.0Si 系、鋼種ｄは11
Cr−2.0Si 系のステンレス鋼である。これらを本発明で
定める条件で熱間圧延し、巻取り後は水冷した。その
後、表２に示すような種々の条件でベル焼鈍を行い、得
られた鋼帯から試験片（JIS 4 号衝撃試験片のサブサイ
ズ）を採取して25℃で衝撃試験を行った。その結果を表
２に併記する。In Table 1, steel type a is 18Cr-3Al system and steel type b is 18
Cr-2.5Si system, steel type c is 16.5Cr-2.0Si system, steel type d is 11
Cr-2.0Si type stainless steel. These were hot-rolled under the conditions specified in the present invention, and after being wound, they were water-cooled. Then, bell annealing was performed under various conditions as shown in Table 2, and a test piece (subsize of JIS 4 impact test piece) was sampled from the obtained steel strip and subjected to an impact test at 25 ° C. The results are also shown in Table 2.
【００２１】表２から明らかなように、本発明で定めた
条件を全て満足する場合（実施例と表示したもの）は、
いずれも４kgf-m/cm2 以上の衝撃値を有する。なお、表
示していないが、これらの実施例で得られた鋼帯の引張
強さは 650 N/mm2以上で、伸びは 1.0％以上であった。As is clear from Table 2, when all the conditions defined in the present invention are satisfied (denoted as Examples),
All have an impact value of 4 kgf-m / cm 2 or more. Although not shown, the tensile strength of the steel strips obtained in these examples was 650 N / mm 2 or more, and the elongation was 1.0% or more.
【００２２】[0022]
【表１】 [Table 1]
【００２３】[0023]
【表２】 [Table 2]
【００２４】[0024]
【発明の効果】本発明の製造方法によれば、通常の製造
方法では極めて靱性の乏しい鋼帯しか得られない鋼種で
あっても、十分に靱性の高い鋼帯とすることが可能であ
る。According to the manufacturing method of the present invention, it is possible to obtain a steel strip having a sufficiently high toughness, even if the steel type can obtain only a steel strip having an extremely poor toughness by the usual manufacturing method.
【図１】2.5％Si− 0.3％Nbフェライト系ステンレス鋼
の従来法で製造した熱延鋼帯のベル焼鈍温度と室温衝撃
値との関係を示す図である。FIG. 1 is a diagram showing a relationship between a bell annealing temperature and a room temperature impact value of a hot rolled steel strip of a 2.5% Si-0.3% Nb ferritic stainless steel manufactured by a conventional method.
【図２】2.5％Si− 0.3％Nbフェライト系ステンレス鋼
の熱延のままで高靱性の鋼帯をベル焼鈍した場合の焼鈍
条件と室温衝撃値との関係を示す図である。FIG. 2 is a diagram showing a relationship between annealing conditions and room temperature impact values when a high toughness steel strip of 2.5% Si-0.3% Nb ferritic stainless steel is hot-rolled and bell-annealed.
【図３】2.5％Si− 0.3％Nbフェライト系ステンレス鋼
のベル焼鈍後の電子顕微鏡像（10000 倍) のスケッチ
で、（ａ）は従来法で製造したもの、（ｂ）は本発明法
で製造したものである。FIG. 3 is a sketch of electron microscope images (10000 times) after bell annealing of 2.5% Si-0.3% Nb ferritic stainless steel, where (a) is the one manufactured by the conventional method and (b) is the method of the present invention. It is manufactured.
Claims (1)
レス鋼を仕上温度 900℃以下で熱間圧延し、600 ℃以下
で巻取り、巻取り後直ちに水冷して得た鋼帯をベル焼鈍
するに際し、焼鈍温度を 700〜850 ℃とし、かつ焼鈍後
500℃以上の温度から水冷することを特徴とする高靱性
フェライト系ステンレス鋼帯の製造方法。1. A steel strip obtained by hot rolling a high Al-based or high Si-based ferritic stainless steel at a finishing temperature of 900 ° C. or lower, winding it at 600 ° C. or lower, and immediately cooling it with water after bell annealing. When annealing, set the annealing temperature to 700 ~ 850 ℃, and after annealing
A method for producing a high toughness ferritic stainless steel strip, which comprises water cooling from a temperature of 500 ° C or higher.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31493991A JP2705411B2 (en) | 1991-11-28 | 1991-11-28 | Manufacturing method of high toughness ferritic stainless steel strip |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31493991A JP2705411B2 (en) | 1991-11-28 | 1991-11-28 | Manufacturing method of high toughness ferritic stainless steel strip |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05148548A true JPH05148548A (en) | 1993-06-15 |
| JP2705411B2 JP2705411B2 (en) | 1998-01-28 |
Family
ID=18059476
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP31493991A Expired - Lifetime JP2705411B2 (en) | 1991-11-28 | 1991-11-28 | Manufacturing method of high toughness ferritic stainless steel strip |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2705411B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013079428A (en) * | 2011-10-04 | 2013-05-02 | Jfe Steel Corp | METHOD FOR MANUFACTURING HOT-ROLLED FERRITIC STAINLESS STEEL STRIP CONTAINING Al, HOT-ROLLED FERRITIC STAINLESS STEEL STRIP CONTAINING Al, STAINLESS STEEL FOIL, AND CATALYST CARRIER FOR AUTOMOTIVE EXHAUST EMISSION CONTROL SYSTEM |
-
1991
- 1991-11-28 JP JP31493991A patent/JP2705411B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013079428A (en) * | 2011-10-04 | 2013-05-02 | Jfe Steel Corp | METHOD FOR MANUFACTURING HOT-ROLLED FERRITIC STAINLESS STEEL STRIP CONTAINING Al, HOT-ROLLED FERRITIC STAINLESS STEEL STRIP CONTAINING Al, STAINLESS STEEL FOIL, AND CATALYST CARRIER FOR AUTOMOTIVE EXHAUST EMISSION CONTROL SYSTEM |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2705411B2 (en) | 1998-01-28 |
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