JP3448542B2 - Ferritic stainless steel sheet excellent in formability and ridging properties and method for producing the same - Google Patents

Ferritic stainless steel sheet excellent in formability and ridging properties and method for producing the same

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Publication number
JP3448542B2
JP3448542B2 JP2000112010A JP2000112010A JP3448542B2 JP 3448542 B2 JP3448542 B2 JP 3448542B2 JP 2000112010 A JP2000112010 A JP 2000112010A JP 2000112010 A JP2000112010 A JP 2000112010A JP 3448542 B2 JP3448542 B2 JP 3448542B2
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JP
Japan
Prior art keywords
ridging
stainless steel
formability
ferritic stainless
steel sheet
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
Application number
JP2000112010A
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Japanese (ja)
Other versions
JP2001294991A (en
Inventor
謙 木村
雅之 天藤
正夫 菊池
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
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Nippon Steel Corp
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Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【発明の属する技術分野】本発明は、成形性とリジング
特性に優れたフェライト系ステンレス鋼板及びその製造
方法に関する。
TECHNICAL FIELD The present invention relates to a ferritic stainless steel sheet having excellent formability and ridging characteristics, and a method for producing the same.

【0002】[0002]

【従来の技術】フェライト系ステンレス鋼は耐食性に優
れており、多くの用途に用いられている。しかし、オー
ステナイト系ステンレス鋼の代表鋼種であるSUS30
4に比べて成形性が劣り、成形時にリジングと呼ばれる
表面凹凸が発生すると言う問題があった。
2. Description of the Related Art Ferritic stainless steel has excellent corrosion resistance and is used in many applications. However, SUS30, which is a representative steel type of austenitic stainless steel,
There was a problem that the moldability was inferior to that of No. 4, and surface irregularities called ridging occurred during molding.

【0003】成形性の指標であるr値を高めるために、
特開昭61−261460号公報のようにCやNを低減
し、且つTiやNbを添加して固溶C、Nを減らす方法
が用いられている。このようにフェライト系ステンレス
鋼を高純化し、C,N固定元素を添加することで成形性
は向上するが、逆にリジング特性は劣化する場合があっ
た。
In order to increase the r value, which is an index of formability,
A method of reducing C and N and reducing solid solution C and N by adding Ti and Nb is used as in JP-A-61-261460. As described above, although the ferritic stainless steel is highly purified and the C and N fixing elements are added, the formability is improved, but on the contrary, the ridging characteristic is sometimes deteriorated.

【0004】リジングの成因は鋳造組織の粗大粒にある
と考えられている。フェライト系ステンレス鋼はδ→γ
→α完全変態が無いため、元々存在する粗大粒は類似方
位の結晶粒集団(以下、コロニーと呼ぶ)として成品板
に残存し、リジングとなると考えられている。このコロ
ニーを小さくすればリジングは改善する。
The cause of ridging is believed to be the coarse grains of the cast structure. Ferritic stainless steel is δ → γ
→ Since there is no α perfect transformation, it is considered that the coarse particles that originally existed remain in the product sheet as a crystal grain group of similar orientations (hereinafter, referred to as colonies), resulting in ridging. Reducing this colony improves ridging.

【0005】コロニーのサイズを測定する方法として
は、ECP(Electron Channeling Pattern )法や、E
BSP(Electron Back Scattering Pattern)法が用い
られている。「鉄と鋼」76−9(1990),P.1520 では、
ECPにより測定したコロニーの分布とリジング特性の
関係を述べている。また「CAMP−ISIJ」11(1
998),P.590では、EBSPにより測定したコロニーサイ
ズからリジング発生を予測するモデルが提示されてい
る。
ECP (Electron Channeling Pattern) method and E method are available for measuring the size of colonies.
BSP (Electron Back Scattering Pattern) method is used. “Iron and Steel” 76-9 (1990), P.1520,
The relationship between the distribution of colonies measured by ECP and the ridging characteristics is described. In addition, “CAMP-ISIJ” 11 (1
998), P.590, a model for predicting ridging occurrence from the colony size measured by EBSP is presented.

【0006】リジング改善法(すなわちコロニー微細化
法と考えられる)として、鋳造組織の等軸晶化や熱延、
焼鈍等の製造条件の適正化が行われてきた。凝固組織を
等軸晶化する手法としては、特開昭50−123294
号公報に代表されるように、鋳造時の電磁撹拌、凝固核
の接種、鋳造温度の低下等がある。また、熱間圧延条件
や焼鈍条件を適正化する手法である特公昭61−196
88号公報、特公昭57−38655号公報が知られて
いる。最近では特開昭9−263900号公報、特開平
10−330887号公報のように、熱間圧延条件を規
定して成品板の板幅及び板厚方向のコロニーサイズを限
定する手法が公知となっている。
As a method for improving ridging (which is considered to be a colony refining method), equiaxed crystallization of a cast structure or hot rolling,
The manufacturing conditions such as annealing have been optimized. As a method for making the solidified structure equiaxed, Japanese Patent Application Laid-Open No. 50-123294 is known.
As typified by the publication, there are electromagnetic stirring during casting, inoculation of solidification nuclei, lowering of casting temperature, and the like. Also, Japanese Patent Publication No. 61-196, which is a method for optimizing hot rolling conditions and annealing conditions.
No. 88 and Japanese Patent Publication No. 57-38655 are known. Recently, as disclosed in JP-A-9-263900 and JP-A-10-330887, methods for defining hot rolling conditions to limit the width of a product plate and the colony size in the plate thickness direction have become known. ing.

【0007】しかし、上記の手法では良好なリジング特
性が安定して得られなかったり、熱間圧延で大圧下(圧
下率40%以上)を行うことによるキズの発生等、製造
性を大きく低下させる問題が生じていた。また板幅及び
板厚方向のコロニーサイズを限定しても、目視でリジン
グが認められる場合があった。
[0007] However, the above method does not stably obtain good ridging characteristics, and the manufacturability is greatly reduced, such as the occurrence of scratches due to large reduction (40% or more reduction) in hot rolling. There was a problem. Further, even if the colony size in the plate width and plate thickness directions was limited, ridging could be visually observed in some cases.

【0008】[0008]

【発明が解決しようとする課題】本発明は、製造性の大
幅な低下なく、成形性が良好で安定したリジング特性を
有するフェライト系ステンレス鋼板、及びその製造方法
を提供することを目的とするものである。
SUMMARY OF THE INVENTION It is an object of the present invention to provide a ferritic stainless steel sheet having good formability and stable ridging characteristics without a significant decrease in productivity, and a method for producing the same. Is.

【0009】[0009]

【課題を解決するための手段】発明者らは、実験室で数
種のフェライト系ステンレス鋼薄板を作製し、鋼板のコ
ロニー構造とリジング特性の関係を調査した。成品板の
板厚は0.4〜1.5mmとした。結晶方位測定にはE
BSPを用いた。{hkl}コロニーの定義は、{hk
l}方位より±15°以内の結晶方位を有する粒が2ヶ
以上隣接している範囲とした。{hkl}は板面に垂直
な方位を示す。リジングはL方向に15%引張した後の
試験片形状から目視で判断した。
The inventors made several kinds of ferritic stainless steel thin plates in a laboratory and investigated the relationship between the colony structure of the steel plates and the ridging characteristics. The thickness of the product plate was 0.4 to 1.5 mm. E for crystal orientation measurement
BSP was used. The definition of {hkl} colony is {hk
Two or more grains having a crystallographic orientation within ± 15 ° from the l} orientation were set to be adjacent to each other. {Hkl} indicates an azimuth perpendicular to the plate surface. The ridging was visually judged from the shape of the test piece after pulling 15% in the L direction.

【0010】(1)コロニーには主として{100}、
{111}、{110}がある。 (2)コロニーのサイズ(幅、厚、長さ)が小さいほど
リジング特性は良好となる。リジングが目視では観察で
きないくらいに低減するのは、上記のコロニーの大きさ
を圧延方向に2000μm以下、板幅方向に500μm
以下、板厚方向に300μm以下にした場合である。こ
こで重要なことは、コロニーサイズを板幅方向と板厚方
向のみ細かくしても、圧延方向に展伸していると目視で
リジングが認められることである。リジングが目視で認
められなくなるのは、コロニーサイズの圧延方向長さを
2000μm以下にしたときであった。
(1) The colonies mainly consist of {100},
There are {111} and {110}. (2) The smaller the colony size (width, thickness, length), the better the ridging characteristics. The size of the above colonies is 2000 μm or less in the rolling direction and 500 μm in the width direction of the plate.
In the following, the case is 300 μm or less in the plate thickness direction. What is important here is that even if the colony size is reduced only in the plate width direction and the plate thickness direction, ridging is visually recognized when the colony size is expanded in the rolling direction. The ridging was not visually observed when the length of the colony size in the rolling direction was 2000 μm or less.

【0011】また、コロニーの大きさに及ぼす成分及び
製造条件の影響を調査し、さらに下記の知見を得た。 (3)フェライト系ステンレス鋼にTiとMgを適量添
加した際にコロニーサイズが小さくなり、リジングが極
めて良好な場合があった。このときの介在物はMg系介
在物をTiNが覆った形態を有するものが多く認められ
た。 (4)コロニーサイズは熱間圧延条件によって大きく変
わり、900℃〜1200℃で圧下率15%以上の圧延
を10回以上行った場合に、コロニーサイズが小さくな
った。 (5)上記の(3)と(4)を組み合わせたときに、
(2)に示すようなコロニーの大きさが得られる。
Further, the influence of the components and the production conditions on the colony size was investigated, and the following findings were obtained. (3) When the appropriate amounts of Ti and Mg were added to the ferritic stainless steel, the colony size became small and the ridging was sometimes very good. Many of the inclusions at this time were found to have a form in which Mg-based inclusions were covered with TiN. (4) The colony size greatly changed depending on the hot rolling conditions, and the colony size was reduced when rolling was performed at 900 ° C to 1200 ° C with a reduction rate of 15% or more 10 times or more. (5) When the above (3) and (4) are combined,
The colony size as shown in (2) is obtained.

【0012】本発明は上記知見に基づくものであって、
その要旨とするところは以下の通りである。 (1) mass%で、 C :0.0005〜0.03%、 Si:0.01〜1%、 Mn:0.01〜1%、 P :0.04%未満、 S :0.0001〜0.01%、 Cr:10〜25%、 Ti:0.01〜0.8%、 Al:0.005〜0.1%、 N :0.0005〜0.03%、 Mg:0.0005〜0.01% を含有し、残部Fe及び不可避的不純物からなり、最大
径が0.05〜5μmのMg系介在物をTiNで覆った
形態を有する介在物が3個/mm2 以上の密度で鋼中存
在し、さらに、{100},{110},{111}コ
ロニーのうち最も大きいコロニーの大きさが圧延方向に
2000μm以下、幅方向に500μm以下、板厚方向
に300μm以下であることを特徴とする成形性とリジ
ング特性に優れたフェライト系ステンレス鋼板。
The present invention is based on the above findings,
The summary is as follows. (1) Mass%, C: 0.0005 to 0.03%, Si: 0.01 to 1%, Mn: 0.01 to 1%, P: less than 0.04%, S: 0.0001 to 0.01%, Cr: 10 to 25%, Ti: 0.01 to 0.8%, Al: 0.005 to 0.1%, N: 0.0005 to 0.03%, Mg: 0.0005 containing 0.01%, the balance being Fe and unavoidable impurities, the density of the inclusions 3 / mm 2 or more in the form of maximum size covers the Mg-based inclusions 0.05~5μm with TiN The size of the largest colony among the {100}, {110}, and {111} colonies is 2000 μm or less in the rolling direction, 500 μm or less in the width direction, and 300 μm or less in the plate thickness direction. Fe-based ferrite with excellent formability and ridging characteristics Nresu steel plate.

【0013】 (2) mass%で、 B :0.0005〜0.005%、 Nb:0.05〜0.5%、 V :0.05〜0.5%、 Ta:0.05〜0.5%、 W :0.05〜0.5%、 Hf:0.05〜0.5%、 Zr:0.05〜0.5% の1種もしくは2種以上を、さらに含有することを特徴
とする前記(1)に記載の成形性とリジング特性に優れ
たフェライト系ステンレス鋼板。 (3) mass%で、 Mo:0.1〜2%、 Ni:0.1〜2%、 Cu:0.1〜2% の1種もしくは2種以上を、さらに含有することを特徴
とする前記(1)又は(2)記載の成形性とリジング特
性に優れたフェライト系ステンレス鋼板。 (4) mass%で、 Y:0.0002〜0.005%、 La:0.0002〜0.005%、 Ce:0.0002〜0.005% の1種もしくは2種以上を、さらに含有することを特徴
とする前記(1)乃至(3)のいずれかに記載の成形性
とリジング特性に優れたフェライト系ステンレス鋼板。
(2) In mass%, B: 0.0005 to 0.005%, Nb: 0.05 to 0.5%, V: 0.05 to 0.5%, Ta: 0.05 to 0 0.5%, W: 0.05 to 0.5%, Hf: 0.05 to 0.5%, Zr: 0.05 to 0.5%, and one or more of them may be further contained. A ferritic stainless steel sheet having excellent formability and ridging characteristics described in (1) above. (3) One or more of Mo: 0.1 to 2%, Ni: 0.1 to 2%, and Cu: 0.1 to 2% in mass% are further contained. A ferritic stainless steel sheet having excellent formability and ridging characteristics according to (1) or (2) above. (4) In mass%, Y: 0.0002 to 0.005%, La: 0.0002 to 0.005%, Ce: 0.0002 to 0.005%, and further contains one or more kinds. The ferritic stainless steel sheet having excellent formability and ridging characteristics according to any one of (1) to (3) above.

【0014】(5) mass%で、 Ca:0.0002〜0.005% を、さらに含有することを特徴とする前記(1)〜
(4)のいずれかに記載の成形性とリジング特性に優れ
たフェライト系ステンレス鋼板。 (6) mass%で、 Sb:0.0002〜0.005%、 Sn:0.001〜0.1% の1種もしくは2種を、さらに含有することを特徴とす
る前記(1)乃至(5)のいずれかに記載の成形性とリ
ジング特性に優れたフェライト系ステンレス鋼板。
(7) mass%で、 Ag:0.0005〜0.3% を、さらに含有することを特徴とする前記(1)乃至
(6)のいずれかに記載の成形性とリジング特性に優れ
たフェライト系ステンレス鋼板。 (8) 前記(1)乃至(7)のいずれかに記載のフェ
ライト系ステンレス鋼板を製造するに際し、熱間圧延工
程において900〜1200℃で圧下率15%以上の圧
延を10回以上行うことを特徴とする成形性とリジング
特性に優れたフェライト系ステンレス鋼板の製造方法。
(5) The above (1) to (10) characterized by further containing Ca: 0.0002 to 0.005% in mass%.
A ferritic stainless steel sheet having excellent formability and ridging characteristics according to any one of (4). (6) One or two kinds of Sb: 0.0002 to 0.005% and Sn: 0.001 to 0.1% in mass% are further contained, and the above (1) to (). A ferritic stainless steel sheet having excellent formability and ridging characteristics according to any one of 5).
(7) Ferrite excellent in formability and ridging property according to any one of (1) to (6), further containing Ag: 0.0005 to 0.3% in mass%. Series stainless steel plate. (8) When manufacturing the ferritic stainless steel sheet according to any one of (1) to (7), rolling at a rolling reduction of 15% or more at 900 to 1200 ° C. is performed 10 times or more in a hot rolling step. A method for producing a ferritic stainless steel sheet having excellent formability and ridging characteristics.

【0015】[0015]

【発明の実施の形態】以下本発明について詳細に説明す
る。なお、下記の説明における%とはmass%を示す
ものである。 C,N:C,Nを多量に添加すると強度が上昇して成形
加工性が低下するため、それぞれ上限は0.03%とし
た。一方、下限は精錬段階での大幅なコスト増加なしに
製造できるのは0.0005%である。厳しい加工用途
等に用いる場合には、C,N共に0.0005〜0.0
15%とすることが好ましい。
BEST MODE FOR CARRYING OUT THE INVENTION The present invention will be described in detail below. In addition,% in the following description means mass%. C, N: If a large amount of C, N is added, the strength increases and the moldability decreases, so the upper limit was made 0.03%. On the other hand, the lower limit is 0.0005% that can be manufactured without a significant increase in cost in the refining stage. When used for severe processing applications, both C and N are 0.0005-0.0
It is preferably set to 15%.

【0016】Si:Siは脱酸元素として必要である
が、多量の添加により成形性が低下する。したがって上
限は1%とした。下限は脱酸効果を得るために0.01
%とした。
Si: Si is necessary as a deoxidizing element, but if added in a large amount, the formability is lowered. Therefore, the upper limit was set to 1%. The lower limit is 0.01 to obtain a deoxidizing effect.
%.

【0017】Mn:Mnは多量の添加により強度を上昇
させ、成形性を低下させる為、上限を1%とした。下限
はコストの観点より0.01%とした。
Mn: Mn increases the strength by adding a large amount and lowers the formability, so the upper limit was made 1%. The lower limit is 0.01% from the viewpoint of cost.

【0018】P:Pは成形加工性の点からは低い方が好
ましく、0.04%未満とする必要がある。低いほど延
性は向上するので、0.02%以下にすることが好まし
い。下限は原料コストの点から0.005%程度が望ま
しい。
From the viewpoint of moldability, P: P is preferably low, and it must be less than 0.04%. The lower the value, the better the ductility, so it is preferably 0.02% or less. The lower limit is preferably about 0.005% from the viewpoint of raw material cost.

【0019】S:Sは多量に添加すると耐食性、加工性
が低下するため、上限は0.01%とした。下限は近年
の脱硫技術で極低化が可能であるので、0.0001%
とした。
S: When S is added in a large amount, corrosion resistance and workability are deteriorated, so the upper limit was made 0.01%. The lower limit is 0.0001% because it can be extremely lowered by recent desulfurization technology.
And

【0020】Cr:Crは10%未満ではステンレス鋼
としての耐食性が不十分であり、25%を超えると強度
上昇のために成形しづらくなるばかりでなく、靱性が低
下する場合があるため、10〜25%を範囲とした。ま
た、Cr量が多くなると加工性が低下するため、加工用
途としては10〜19%が好ましい。
Cr: If Cr is less than 10%, the corrosion resistance as stainless steel is insufficient, and if it exceeds 25%, not only is it difficult to form due to an increase in strength, but also the toughness may decrease, so that 10 The range was -25%. Further, if the amount of Cr increases, the workability decreases, so 10-19% is preferable for processing applications.

【0021】Ti:TiはC,Nを固定して成形性を高
めるだけでなく、Mgとの組み合わせでTiNを晶出さ
せて本発明の課題であるリジング特性を向上させる重要
な元素である。本発明では成形性向上効果があるのは
0.01%以上であり、これを下限とした。またTi量
が多すぎると強度が増加し、延性の低下を招くため、上
限を0.8%とした。延性に加えて製造性等の観点か
ら、最も好ましい範囲は0.08〜0.3%である。
Ti: Ti is an important element that not only fixes C and N to enhance the formability but also crystallizes TiN in combination with Mg to improve the ridging property which is the subject of the present invention. In the present invention, the effect of improving the moldability is 0.01% or more, and this is set as the lower limit. Further, if the amount of Ti is too large, the strength increases and the ductility decreases, so the upper limit was made 0.8%. From the viewpoint of ductility and manufacturability, the most preferable range is 0.08 to 0.3%.

【0022】Al:AlはN等を固定して加工性を向上
する元素であるが、多量の添加は成形性の低下及びコス
トの増加をもたらすため、上限は0.1%とした。一
方、Al量の低減により脱酸が困難になるため、下限は
0.005%とした。
Al: Al is an element that fixes N and the like to improve workability, but addition of a large amount thereof causes deterioration of formability and increase of cost, so the upper limit was made 0.1%. On the other hand, since lowering the amount of Al makes it difficult to deoxidize, the lower limit was made 0.005%.

【0023】Mg:Mgは介在物を形成して、本発明の
課題であるリジング性を向上させる重要な元素である。
その効果を発揮する下限は0.0005%であり、これ
を下限とした。また多量に添加してもその効果は飽和す
るため、0.01%を上限とした。
Mg: Mg is an important element that forms inclusions and improves the ridging property which is the subject of the present invention.
The lower limit for exerting the effect is 0.0005%, and this was made the lower limit. Even if added in a large amount, the effect is saturated, so 0.01% was made the upper limit.

【0024】B,Nb,V,Ta、W,Hf,Zr:こ
れらは成形性を向上する元素であり、必要に応じて上記
のうち1種又は2種以上を組み合わせて添加する。B:
0.0005%、Nb,V,Ta、W,Hf,Zr:
0.05%以上添加することで効果が現れる。しかし、
Bは0.005%、Nb,V,Ta、W,Hf,Zrは
0.5%より多くてもその効果は飽和する。
B, Nb, V, Ta, W, Hf, Zr: These are elements that improve the moldability, and if necessary, one or more of the above may be added in combination. B:
0.0005%, Nb, V, Ta, W, Hf, Zr:
The effect is exhibited by adding 0.05% or more. But,
Even if B is 0.005% and Nb, V, Ta, W, Hf, and Zr are more than 0.5%, the effect is saturated.

【0025】Mo,Ni,Cu:これらは耐食性を向上
する元素であり、耐食性が問題となる用途ではMo,N
i,Cuのうち1種又は2種以上を組み合わせて添加す
る。それぞれ0.1%以上添加することにより効果が現
れる。しかし加工性を考慮すると、上限はいずれも2%
である。
Mo, Ni, Cu: These are elements that improve corrosion resistance, and Mo, N are used in applications where corrosion resistance is a problem.
One or more of i and Cu are added in combination. The effect is exhibited by adding 0.1% or more of each. However, considering workability, the upper limit is 2%
Is.

【0026】Y,La,Ce:これらは溶鋼の流動性を
向上し、清浄度をあげる。その効果が発揮される0.0
002%を下限とした。また、0.005%超添加して
も効果は飽和されるため、これを上限とした。 Ca:Caは脱酸、脱硫材として用いられる。その効果
が発揮される下限は0.0002%である。0.005
0%超存在すると、逆に成形性や耐食性を低下させるた
め、上限を0.0050%とした。
Y, La, Ce: These improve the fluidity of molten steel and improve cleanliness. The effect is demonstrated 0.0
The lower limit was 002%. Further, even if added over 0.005%, the effect is saturated, so this was made the upper limit. Ca: Ca is used as a deoxidizing and desulfurizing material. The lower limit at which the effect is exhibited is 0.0002%. 0.005
On the other hand, if the content exceeds 0%, the moldability and the corrosion resistance are deteriorated, so the upper limit was made 0.0050%.

【0027】Sb,Sn:これらの元素は圧延時に変形
帯を生成しやすくするため、リジング向上効果がある。
Sb:0.0002%、Sn:0.001%以上で効果
を発揮するためこれを下限とした。しかしSb:0.0
05%、Sn:0.1%超添加すると強度上昇等成形性
への悪影響をもたらすため、これを上限とした。
Sb, Sn: These elements have an effect of improving ridging because they easily form a deformation zone during rolling.
Since Sb: 0.0002% and Sn: 0.001% or more exert the effect, the lower limit is set. But Sb: 0.0
Addition of more than 05% and Sn: 0.1% has an adverse effect on formability such as strength increase, so the upper limit was made this.

【0028】Ag:Agは抗菌性を向上させる元素であ
る。その効果が発揮される0.0005%を下限とし
た。しかし0.3%超添加すると成形性の低下等をもた
らすため、これを上限とした。
Ag: Ag is an element that improves antibacterial properties. The lower limit was set to 0.0005% at which the effect is exhibited. However, if over 0.3% is added, the formability is deteriorated, so this was made the upper limit.

【0029】さらに本発明では、Mg系介在物の最大径
は0.05〜5μmのサイズが必要である。0.05μ
mより小さいとTiNの晶出核として働かず、リジング
の原因であるコロニーのサイズを小さくできない。5μ
m超であると製造欠陥(キズ)が増加する。
Further, according to the present invention, the maximum diameter of the Mg-based inclusions is required to be 0.05 to 5 μm. 0.05μ
If it is smaller than m, it does not act as a crystallization nucleus of TiN, and the size of the colony that causes ridging cannot be reduced. 5μ
If it exceeds m, manufacturing defects (scratches) increase.

【0030】また、Mg系介在物を覆ってTiNが存在
する形態が必要となる。これは任意の断面で観察した際
に、図1に示すようにMg系介在物の周囲全面を囲んで
TiNが存在することを示す。このような形態の介在物
分布密度は3個/mm2 以上が必要となる。これより少
ないとコロニーサイズを小さくできない。リジング特性
をさらに向上させるには30個/mm2 以上とすること
が好ましい。密度の上限は強度上昇が著しくない範囲で
10000個/mm2 が望ましい。これらの介在物のサ
イズの調査は、鋼塊及び鋼板の任意の断面において介在
物の抽出レプリカあるいは薄膜を作成し、電子顕微鏡で
調査する方法がよい。分布は、前述のごとく電子顕微
鏡、あるいはEPMAを用いて調査する方法がよい。
Further, a form in which TiN exists so as to cover the Mg-based inclusions is required. This indicates that, when observed in an arbitrary cross section, TiN is present so as to surround the entire surface of the Mg-based inclusion as shown in FIG. The distribution density of inclusions in such a form needs to be 3 pieces / mm 2 or more. If it is less than this, the colony size cannot be reduced. In order to further improve the ridging property, the number is preferably 30 pieces / mm 2 or more. The upper limit of the density is preferably 10,000 pieces / mm 2 within a range in which the strength is not significantly increased. The size of these inclusions may be investigated by making an extraction replica or a thin film of the inclusions on an arbitrary cross section of the steel ingot and the steel plate, and inspecting with an electron microscope. The distribution is preferably examined by using an electron microscope or EPMA as described above.

【0031】リジングの成因となる{100},{11
0},{111}コロニーのうち、最も大きいコロニー
のサイズは圧延方向に2000μm以下、板幅方向に5
00μm以下、板厚方向に300μm以下とする必要が
ある。このことによってリジングをほとんど皆無に出来
る。このコロニーサイズを得るには、介在物制御と後述
の熱延条件制御の両者が必要である。コロニーサイズの
調査にはEBSP法を用いると良い。
{100} and {11 which cause ridging
The largest of the 0} and {111} colonies has a size of 2000 μm or less in the rolling direction and 5 in the plate width direction.
It is necessary to set the thickness to 00 μm or less and to 300 μm or less in the plate thickness direction. This allows almost no ridging. In order to obtain this colony size, both inclusion control and hot rolling condition control described later are required. The EBSP method may be used to investigate the colony size.

【0032】Mgは脱酸材としても用いられる元素であ
り、長時間溶鋼中に存在すると粗大化して浮上すること
があるため、Mg介在物を上記のようなサイズ及び分布
で存在させるには、Mgを添加後120min以内に鋳
造させる必要がある。他の成分元素を添加した最後にM
gを添加する方法が好ましい。Mg系介在物とは、Mg
を含有する介在物を示す。酸化物(MgO、MgAl 2
4 等)や硫化物(MgS)等、いずれの組成でも良
い。EDSで解析した際にMgのピークが認められる介
在物を指す。
Mg is an element also used as a deoxidizer.
If it remains in molten steel for a long time, it will become coarse and float.
Therefore, the size and distribution of Mg inclusions are
In order to make it exist by casting, cast within 120 min after adding Mg.
It needs to be built. Finally M after adding other component elements
The method of adding g is preferred. Mg-based inclusions are Mg
The inclusions containing are shown. Oxides (MgO, MgAl 2
OFourEtc.) and sulfide (MgS), etc.
Yes. The peak of Mg is observed when analyzed by EDS
Refers to existing things.

【0033】また、上記のフェライト系ステンレス鋼の
製造方法は、通常、鋼塊を熱延、焼鈍、冷延、焼鈍する
が、熱延板の焼鈍を省略しても、冷延途中に焼鈍を行っ
ても、また熱延を省略しても良い。ただし熱間圧延工程
において900℃〜1200℃で圧下率15%以上の圧
延を10回以上行うことを必要としている。圧延温度が
900℃未満あるいは1200℃超、圧下率が15%未
満、回数10回に満たない場合にはコロニーサイズが小
さくならない。好ましくは、熱間圧延途中の再結晶を促
進させるために圧下率は25%以上がよい。但し40%
以上のような大圧下は必要としない。この方法は通常の
熱間圧延に比べて製造性を大きく低減することはない。
In the above-mentioned method for producing a ferritic stainless steel, a steel ingot is usually hot rolled, annealed, cold rolled or annealed. However, even if the annealing of the hot rolled sheet is omitted, the annealing is performed during the cold rolling. Alternatively, hot rolling may be omitted. However, it is necessary to perform rolling at a rolling reduction of 15% or more at 900 ° C. to 1200 ° C. 10 times or more in the hot rolling process. When the rolling temperature is lower than 900 ° C. or higher than 1200 ° C., the rolling reduction is lower than 15%, and the number of times is less than 10 times, the colony size does not decrease. Preferably, the rolling reduction is 25% or more in order to promote recrystallization during hot rolling. However, 40%
The above large reduction is not necessary. This method does not significantly reduce manufacturability as compared with ordinary hot rolling.

【0034】本発明により、成形性とリジング特性が良
好なフェライト系ステンレス鋼が得られる原因を次のよ
うに考えている。溶鋼中にMg介在物を多数存在させ、
これを核としてTiNを晶出させる。このTiNはフェ
ライト相の凝固時の凝固核となるため凝固組織が微細な
等軸晶になる。すなわちコロニーの単位と考えられる結
晶粒が微細になり、{100}に成長している柱状晶を
減らすことによって方位がランダム化する。この組織を
スタートとして熱延をした場合には、組織が細かいため
に再結晶核となる結晶粒界が多いことに加えて、熱間再
結晶しづらい方位である{100}が少ないため、熱間
圧延中に再結晶しやすくなる。したがって熱延時に軽圧
下を繰り返すだけで再結晶によって組織は微細に、すな
わちリジングの成因であるコロニーを細分化していると
考えられる。
The cause of obtaining a ferritic stainless steel excellent in formability and ridging property according to the present invention is considered as follows. A large number of Mg inclusions are present in the molten steel,
TiN is crystallized using this as a nucleus. Since this TiN serves as a solidification nucleus when the ferrite phase solidifies, the solidification structure becomes a fine equiaxed crystal. That is, the crystal grains considered as a unit of colony become fine, and the orientation is randomized by reducing the columnar crystals growing to {100}. When hot rolling is started with this structure as a starting point, in addition to the fact that there are many crystal grain boundaries that become recrystallization nuclei because of the fine structure and there are few {100}, which is the orientation that makes hot recrystallization difficult, Easily recrystallized during hot rolling. Therefore, it is considered that the structure is finely divided by recrystallization, that is, the colony that is the cause of ridging is subdivided only by repeating the light reduction during hot rolling.

【0035】[0035]

【実施例】以下に本発明の実施例を示す。 [実施例1]表1に示すフェライト系ステンレス鋼を溶
製し、熱延後、冷延、焼鈍等により0.4〜1.0mm
の鋼板を作成した。熱延では900℃〜1200℃の範
囲で圧下率15%以上の圧延を10回以上行う条件で行
った。鋼板のL及びC断面の結晶方位分布をEBSPで
調査し、コロニーサイズを求めた。また、板厚中心近傍
のZ断面組織より電顕及びEPMAにより介在物の調査
を行った。
EXAMPLES Examples of the present invention will be shown below. [Example 1] The ferritic stainless steels shown in Table 1 were melted, hot-rolled, then cold-rolled, annealed, or the like to form 0.4 to 1.0 mm.
The steel plate of The hot rolling was performed under the condition of rolling at a rolling reduction of 15% or more in the range of 900 ° C to 1200 ° C 10 times or more. The crystal orientation distribution of the L and C cross sections of the steel sheet was investigated by EBSP, and the colony size was obtained. Further, inclusions were examined from the Z-section structure near the center of the plate thickness by electron microscopy and EPMA.

【0036】鋼板から引張試験片を採取し、r値測定試
験(15%引張、L、D、C方向の平均(rL+2rD
+rC)/4))及びリジング測定用の15%引張試験
に供した。引張後、目視及びリジング高さ(C方向の表
面粗度の山と谷の最大差)でリジング特性を評価した。
目視のランクはA:リジングが全く認められない、B:
リジングが目視で若干認められる、C:リジングが目視
ではっきりと認められる、である。リジング高さはA:
5μm以下、B:15μm以下、C:30μm以下、
D:30μm超である。
Tensile test pieces were sampled from the steel sheet and subjected to r value measurement test (15% tensile, average in L, D and C directions (rL + 2rD).
+ RC) / 4)) and a 15% tensile test for ridging measurement. After the tension, the ridging characteristics were evaluated visually and by the ridging height (the maximum difference between the peak and the valley of the surface roughness in the C direction).
The visual rank is A: no ridging is observed, B:
Some ridging is visually recognized, and C: Ridging is clearly visible. Ridging height is A:
5 μm or less, B: 15 μm or less, C: 30 μm or less,
D: It is more than 30 μm.

【0037】各種評価結果を表2に示す。本発明鋼は比
較鋼に比べて成形性、リジング特性が優れている。特に
リジングは目視でも認められないくらいに大きく改善さ
れている。
The results of various evaluations are shown in Table 2. The steel of the present invention is superior to the comparative steel in formability and ridging characteristics. In particular, ridging has been greatly improved so that it cannot be visually observed.

【0038】[0038]

【表1】 [Table 1]

【0039】[0039]

【表2】 [Table 2]

【0040】[実施例2]表1に示すフェライト系ステ
ンレス鋼のC,Gについて、熱延条件を数水準変化させ
て熱延板を作製した。この熱延板を焼鈍、冷延等により
0.6mmの鋼板を作成した。鋼板のL及びC断面の結
晶方位分布をEBSPで調査し、コロニーサイズを求め
た。また、板厚中心近傍のZ断面組織より電顕及びEP
MAにより介在物の調査を行った。鋼板より引張試験片
を採取し、r値測定試験及びリジング測定用の15%引
張試験に供した。引張後、目視及びリジング高さ(C方
向の表面粗度の山と谷の最大差)でリジング特性を評価
した。各種評価結果を表3に示す。本発明法は比較法に
比べて成形性、リジング特性が優れている。
Example 2 With respect to C and G of ferritic stainless steel shown in Table 1, hot rolled sheets were prepared by changing hot rolling conditions by several levels. This hot-rolled sheet was annealed, cold-rolled, etc. to prepare a steel sheet of 0.6 mm. The crystal orientation distribution of the L and C cross sections of the steel sheet was investigated by EBSP, and the colony size was obtained. In addition, the electron microscope and EP
Inclusions were investigated by MA. Tensile test pieces were taken from the steel sheet and subjected to a r-value measurement test and a 15% tensile test for ridging measurement. After the tension, the ridging characteristics were evaluated visually and by the ridging height (the maximum difference between the peak and the valley of the surface roughness in the C direction). Table 3 shows the results of various evaluations. The method of the present invention is superior in moldability and ridging property to the comparative method.

【0041】[0041]

【表3】 [Table 3]

【0042】[0042]

【発明の効果】本発明によれば、成分、介在物及びコロ
ニーサイズを限定することで、製造性の大幅な低下無く
成形性とリジング特性に優れたフェライト系ステンレス
鋼板を提供できる。
According to the present invention, by limiting the components, inclusions and colony size, it is possible to provide a ferritic stainless steel sheet which is excellent in formability and ridging characteristics without significantly reducing the manufacturability.

【図面の簡単な説明】[Brief description of drawings]

【図1】本発明における介在物の形態を示す模式図であ
る。
FIG. 1 is a schematic view showing the form of inclusions in the present invention.

フロントページの続き (58)調査した分野(Int.Cl.7,DB名) C22C 38/00 - 38/60 Continuation of front page (58) Fields surveyed (Int.Cl. 7 , DB name) C22C 38/00-38/60

Claims (8)

(57)【特許請求の範囲】(57) [Claims] 【請求項1】 mass%で、 C :0.0005〜0.03%、 Si:0.01〜1%、 Mn:0.01〜1%、 P :0.04%未満、 S :0.0001〜0.01%、 Cr:10〜25%、 Ti:0.01〜0.8%、 Al:0.005〜0.1%、 N :0.0005〜0.03%、 Mg:0.0005〜0.01% を含有し、最大径が0.05〜5μmのMg系介在物を
TiNで覆った形態を有する介在物が3個/mm2 以上
の密度で鋼中存在し、さらに、{100},{11
0},{111}コロニーのうち最も大きいコロニーの
大きさが圧延方向に2000μm以下、幅方向に500
μm以下、板厚方向に300μm以下であることを特徴
とする成形性とリジング特性に優れたフェライト系ステ
ンレス鋼板。
1. Mass%, C: 0.0005 to 0.03%, Si: 0.01 to 1%, Mn: 0.01 to 1%, P: less than 0.04%, S: 0.0. 0001 to 0.01%, Cr: 10 to 25%, Ti: 0.01 to 0.8%, Al: 0.005 to 0.1%, N: 0.0005 to 0.03%, Mg: 0 0.0005 to 0.01% of Mg-based inclusions having a maximum diameter of 0.05 to 5 μm and covered with TiN are present in the steel at a density of 3 / mm 2 or more. , {100}, {11
The largest of the 0} and {111} colonies has a size of 2000 μm or less in the rolling direction and 500 in the width direction.
A ferritic stainless steel sheet having excellent formability and ridging characteristics, characterized in that the thickness is 300 μm or less in the plate thickness direction.
【請求項2】 mass%で、 B :0.0005〜0.005%、 Nb:0.05〜0.5%、 V :0.05〜0.5%、 Ta:0.05〜0.5%、 W :0.05〜0.5%、 Hf:0.05〜0.5%、 Zr:0.05〜0.5% の1種もしくは2種以上を、さらに含有することを特徴
とする請求項1に記載の成形性とリジング特性に優れた
フェライト系ステンレス鋼板。
2. In mass%, B: 0.0005 to 0.005%, Nb: 0.05 to 0.5%, V: 0.05 to 0.5%, Ta: 0.05 to 0. 5%, W: 0.05 to 0.5%, Hf: 0.05 to 0.5%, Zr: 0.05 to 0.5%, or a combination of two or more thereof. A ferritic stainless steel sheet having excellent formability and ridging characteristics according to claim 1.
【請求項3】 mass%で、 Mo:0.1〜2%、 Ni:0.1〜2%、 Cu:0.1〜2% の1種もしくは2種以上を、さらに含有することを特徴
とする請求項1又は2記載の成形性とリジング特性に優
れたフェライト系ステンレス鋼板。
3. Mass%, Mo: 0.1 to 2%, Ni: 0.1 to 2%, Cu: 0.1 to 2%, and further contains one or more kinds. A ferritic stainless steel sheet excellent in formability and ridging property according to claim 1 or 2.
【請求項4】 mass%で、 Y :0.0002〜0.005%、 La:0.0002〜0.005%、 Ce:0.0002〜0.005% の1種もしくは2種以上を、さらに含有することを特徴
とする請求項1乃至3のいずれかに記載の成形性とリジ
ング特性に優れたフェライト系ステンレス鋼板。
4. In mass%, one or more of Y: 0.0002 to 0.005%, La: 0.0002 to 0.005%, Ce: 0.0002 to 0.005%, The ferritic stainless steel sheet excellent in formability and ridging property according to any one of claims 1 to 3, further containing.
【請求項5】 mass%で、 Ca:0.0002〜0.005% を、さらに含有することを特徴とする請求項1乃至4の
いずれかに記載の成形性とリジング特性に優れたフェラ
イト系ステンレス鋼板。
5. A ferrite system excellent in moldability and ridging property according to claim 1, further comprising Ca: 0.0002 to 0.005% in mass%. Stainless steel plate.
【請求項6】 mass%で、 Sb:0.0002〜0.005%、 Sn:0.001〜0.1% の1種もしくは2種を、さらに含有することを特徴とす
る請求項1〜5のいずれか記載の成形性とリジング特性
に優れたフェライト系ステンレス鋼板。
6. In mass%, Sb: 0.0002 to 0.005%, Sn: 0.001 to 0.1%, one or two kinds are further contained. 5. A ferritic stainless steel sheet having excellent formability and ridging characteristics according to any one of 5 above.
【請求項7】 mass%で、 Ag:0.0005〜0.3% を、さらに含有することを特徴とする請求項1乃至6の
いずれかに記載の成形性とリジング特性に優れたフェラ
イト系ステンレス鋼板。
7. A ferrite system excellent in formability and ridging property according to claim 1, further comprising Ag: 0.0005 to 0.3% in mass%. Stainless steel plate.
【請求項8】 請求項1〜7のいずれかに記載のフェラ
イト系ステンレス鋼板を製造するに際し、熱間圧延工程
において900〜1200℃で圧下率15%以上の圧延
を10回以上行うことを特徴とする成形性とリジング特
性に優れたフェライト系ステンレス鋼板の製造方法。
8. When manufacturing the ferritic stainless steel sheet according to any one of claims 1 to 7, rolling in a hot rolling step at 900 to 1200 ° C. with a reduction rate of 15% or more is performed 10 times or more. And a method for producing a ferritic stainless steel sheet having excellent formability and ridging characteristics.
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