JP2020164905A - Stainless steel plate and method for producing the same - Google Patents
Stainless steel plate and method for producing the same Download PDFInfo
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- POWFTOSLLWLEBN-UHFFFAOYSA-N tetrasodium;silicate Chemical compound [Na+].[Na+].[Na+].[Na+].[O-][Si]([O-])([O-])[O-] POWFTOSLLWLEBN-UHFFFAOYSA-N 0.000 description 1
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Abstract
Description
本発明は、ステンレス鋼板およびステンレス鋼板の製造方法に関する。 The present invention relates to a stainless steel sheet and a method for manufacturing a stainless steel sheet.
フォトエッチング加工とは、フォトレジスト法によって金属板表面に所望のパターンを形成した後に不要部分の金属をエッチング液により溶解し、金属板を前記パターンに沿った形状に加工する方法である。当該加工法は、集積回路等を形成する際に用いられるメタルマスクや、高精細ディスプレイに用いられるシャドーマスク等の製造に使用されている。 The photoetching process is a method in which a desired pattern is formed on the surface of a metal plate by a photoresist method, and then the metal in an unnecessary portion is dissolved by an etching solution to process the metal plate into a shape along the pattern. This processing method is used in the manufacture of metal masks used when forming integrated circuits and the like, shadow masks used in high-definition displays, and the like.
フォトエッチング加工に好適なステンレス鋼板として、例えば特許文献１には、エッチング面の平滑性を向上させたステンレス鋼板が開示されている。また特許文献２には、エッチング速度の向上とエッチング面の平滑性とを兼ね備えたステンレス鋼板が開示されている。 As a stainless steel sheet suitable for photo-etching, for example, Patent Document 1 discloses a stainless steel sheet having improved smoothness of an etched surface. Further, Patent Document 2 discloses a stainless steel sheet having both an improvement in etching rate and smoothness of an etching surface.
しかしながら、特許文献１に開示されているステンレス鋼板は、平滑な表面を得るためにエッチング加工が均一に施されるため、エッチング速度の向上は望めない。また、特許文献２に開示されているステンレス鋼板は、粗大炭化物の生成と結晶粒の成長抑制を目的としてＮｂを添加し、粒界のエッチング速度を速めている。しかし、粒界が優先的にエッチングされても母材のエッチング速度は変わらないと考えられるため、ステンレス鋼板全体としてのエッチング速度の向上は望めない可能性がある。また、Ｎｂ添加が必須となることから、ステンレス鋼板の製造コストも上昇してしまう。 However, since the stainless steel sheet disclosed in Patent Document 1 is uniformly etched in order to obtain a smooth surface, improvement in etching rate cannot be expected. Further, in the stainless steel sheet disclosed in Patent Document 2, Nb is added for the purpose of producing coarse carbides and suppressing the growth of crystal grains, thereby increasing the etching rate of grain boundaries. However, since it is considered that the etching rate of the base material does not change even if the grain boundaries are preferentially etched, it may not be possible to expect an improvement in the etching rate of the stainless steel sheet as a whole. In addition, since the addition of Nb is indispensable, the manufacturing cost of the stainless steel sheet also increases.
これらの問題点を鑑み、本発明の一態様は、エッチング性に優れたステンレス鋼板を実現することを目的とする。 In view of these problems, one aspect of the present invention is to realize a stainless steel sheet having excellent etching properties.
上記の課題を解決するために、本発明の一態様に係るステンレス鋼板は、Ｎｉが偏析した偏析層を有し、前記偏析層において、Ｎｉ濃度が最大となる部分と、Ｎｉ濃度が最小となる部分とのＮｉ濃度差が１．５質量％以上である。 In order to solve the above problems, the stainless steel sheet according to one aspect of the present invention has a segregation layer in which Ni is segregated, and the portion of the segregation layer where the Ni concentration is maximum and the Ni concentration are minimum. The difference in Ni concentration from the portion is 1.5% by mass or more.
本発明の一態様に係るステンレス鋼板は、下記（１）式により定まるＸ値が３未満である化学組成を有していてもよい；
Ｘ＝３０（Ｃ＋Ｎ）＋０．５Ｍｎ＋Ｎｉ−１．３Ｃｒ＋１１．８ （１）
ここで、（１）式の元素記号の箇所には質量％で表される当該元素の含有量が代入され、無添加の元素については０（ゼロ）が代入される。
The stainless steel sheet according to one aspect of the present invention may have a chemical composition in which the X value determined by the following equation (1) is less than 3.
X = 30 (C + N) + 0.5Mn + Ni-1.3Cr + 11.8 (1)
Here, the content of the element represented by mass% is substituted in the place of the element symbol in the formula (1), and 0 (zero) is substituted for the element without addition.
本発明の一態様に係るステンレス鋼板は、質量％で、Ｃ：０．０８％以下、Ｓｉ：１．００％以下、Ｍｎ：２．５０％以下Ｐ：０．０４５％以下、Ｓ：０．０３０％以下、Ｎｉ：７．００〜１５．００％、およびＣｒ：１６．００〜２０．００％を含有し、残部がＦｅおよび不可避的不純物を含むものであってもよい。 The stainless steel sheet according to one aspect of the present invention has a mass% of C: 0.08% or less, Si: 1.00% or less, Mn: 2.50% or less, P: 0.045% or less, S: 0. It may contain 030% or less, Ni: 7.00 to 15.00%, and Cr: 16.0 to 20.00%, and the balance may contain Fe and unavoidable impurities.
本発明の一態様に係るステンレス鋼板は、質量％で、Ｍｏ：２．００〜３．００％、Ｃｕ：２．５０〜４．００％、Ｎ：０．０６％以下、およびＢ：０．０１％以下のいずれか２種以上をさらに含有していてもよい。 The stainless steel sheet according to one aspect of the present invention has Mo: 2.00 to 3.00%, Cu: 2,500 to 4.00%, N: 0.06% or less, and B: 0. Any two or more of 01% or less may be further contained.
上記の課題を解決するために、本発明の一態様に係るステンレス鋼板の製造方法は、Ｎｉが偏析した偏析層を有し、前記偏析層において、Ｎｉ濃度が最大となる部分と、Ｎｉ濃度が最小となる部分とのＮｉ濃度差が１．５質量％以上であるステンレス鋼板の製造方法であって、巻取り温度を４００℃以上７００℃以下とし、圧延率を９７％以下とする熱間圧延工程と、焼鈍温度を９００℃以上１０００℃以下とする焼鈍工程と、を含む。 In order to solve the above problems, the method for producing a stainless steel sheet according to one aspect of the present invention has a segregated layer in which Ni is segregated, and the portion of the segregated layer where the Ni concentration is maximum and the Ni concentration are high. A method for manufacturing a stainless steel sheet having a Ni concentration difference of 1.5% by mass or more from the minimum portion, in which the winding temperature is 400 ° C. or higher and 700 ° C. or lower and the rolling ratio is 97% or lower. It includes a step and an annealing step of setting the annealing temperature to 900 ° C. or higher and 1000 ° C. or lower.
本発明の一態様によれば、エッチング性に優れたステンレス鋼板を実現できる。 According to one aspect of the present invention, a stainless steel sheet having excellent etching properties can be realized.
以下、本発明の一実施形態について詳細に説明する。なお、以下の記載は発明の趣旨をより良く理解させるためのものであり、特に指定のない限り、本発明を限定するものではない。また、本明細書において特記しない限り、数値範囲を表す「Ａ〜Ｂ」は、「Ａ以上Ｂ以下」を意味する。 Hereinafter, one embodiment of the present invention will be described in detail. The following description is intended to better understand the gist of the invention, and does not limit the present invention unless otherwise specified. Further, unless otherwise specified in the present specification, "A to B" representing a numerical range means "A or more and B or less".
〔Ｎｉの偏析層〕
本実施形態に係るステンレス鋼板は、Ｎｉが偏析したＮｉ偏析層を有する。本発明におけるＮｉ偏析層とは、Ｎｉ濃度が最大となる部分と、Ｎｉ濃度が最小となる部分とのＮｉ濃度差が１．５質量％以上であるステンレス鋼板の層と定義される。ここで、Ｎｉ濃度が最大となる部分と、Ｎｉ濃度が最小となる部分との間の直線距離は３００μｍ以下であることが好ましい。
[Ni segregation layer]
The stainless steel sheet according to the present embodiment has a Ni segregation layer in which Ni is segregated. The Ni segregation layer in the present invention is defined as a layer of a stainless steel sheet in which the difference in Ni concentration between the portion having the maximum Ni concentration and the portion having the minimum Ni concentration is 1.5% by mass or more. Here, the linear distance between the portion where the Ni concentration is maximum and the portion where the Ni concentration is minimum is preferably 300 μm or less.
このようなＮｉ偏析層を有するステンレス鋼板であれば、エッチング加工におけるエッチング性が優れている。なぜならば、Ｎｉ偏析層を有するステンレス鋼板は、３次元的には当該偏析層が複数積層しているとともに、Ｎｉ濃度の濃度差が存在する領域はずれるように積層している。したがって、Ｎｉ濃度が高い部分（すなわち、Ｃｒ濃度が低い部分）が優先的にエッチングされるに際して、ステンレス鋼板の板厚方向に比較的速くエッチングが進行するためである。なお、「エッチング性に優れる」とは、エッチング加工による加工速度が速いことを示す。 A stainless steel sheet having such a Ni segregation layer has excellent etching properties in the etching process. This is because the stainless steel sheet having the Ni segregation layer is three-dimensionally laminated with a plurality of the segregation layers and is laminated so as to deviate from the region where the concentration difference of the Ni concentration exists. Therefore, when the portion having a high Ni concentration (that is, the portion having a low Cr concentration) is preferentially etched, the etching proceeds relatively quickly in the thickness direction of the stainless steel sheet. In addition, "excellent in etching property" means that the processing speed by the etching process is high.
本実施形態に係る、エッチング性に優れるステンレス鋼板は、例えばメタルマスクまたはシャドーマスク等の製造において使用することにより、エッチング加工に要する時間を短縮できる。したがって、本実施形態に係るステンレス鋼板をこれらのエッチング加工品に使用すれば、製造時間を低減し生産性を向上できる。 By using the stainless steel sheet having excellent etching properties according to the present embodiment in the production of, for example, a metal mask or a shadow mask, the time required for etching can be shortened. Therefore, if the stainless steel sheet according to the present embodiment is used for these etched products, the production time can be reduced and the productivity can be improved.
〔化学組成〕
（凝固組織の形態）
本実施形態に係るステンレス鋼板は、凝固組織の形態の指標となる下記（１）式により定まるＸ値が３未満である化学組成を有することが好ましく、Ｘ値が０以下である化学組織を有することがより好ましい。
[Chemical composition]
(Morphology of coagulated tissue)
The stainless steel sheet according to the present embodiment preferably has a chemical composition having an X value of less than 3 determined by the following formula (1), which is an index of the form of the solidified structure, and has a chemical structure having an X value of 0 or less. Is more preferable.
Ｘ＝３０（Ｃ＋Ｎ）＋０．５Ｍｎ＋Ｎｉ−１．３Ｃｒ＋１１．８ （１）
ここで、（１）式の元素記号の箇所には質量％で表される当該元素の含有量が代入され、無添加の元素については０（ゼロ）が代入される。
X = 30 (C + N) + 0.5Mn + Ni-1.3Cr + 11.8 (1)
Here, the content of the element represented by mass% is substituted in the place of the element symbol in the formula (1), and 0 (zero) is substituted for the element without addition.
ステンレス鋼板の凝固組織の形態は、Ｃｒ当量およびＮｉ当量の関係から表すことができ、オーステナイト単相凝固組織（Ａモード）、初晶オーステナイト＋δフェライトの二相凝固組織（ＡＦモード）、初晶δフェライト＋オーステナイトの二相凝固組織（ＦＡモード）に大別される。 The morphology of the solidified structure of the stainless steel plate can be expressed from the relationship between Cr equivalent and Ni equivalent, with austenite single-phase solidified structure (A mode), primary crystal austenite + δ ferrite biphase solidified structure (AF mode), and primary crystal δ. It is roughly classified into a ferrite + austenite two-phase solidification structure (FA mode).
エッチング性の向上に重要なＮｉの成分偏析には、凝固組織がＦＡモードまたはＡモードであることが好ましい。凝固組織中のＮｉの拡散速度は、オーステナイトとδフェライトとで異なり、オーステナイトの方が当該拡散速度が遅い。ＦＡモードでは、初晶フェライトの晶出によりＮｉの成分偏析が生じ、その後拡散速度が遅いオーステナイトが晶出することで、Ｎｉの成分偏析が保たれやすい。またＡモードでは、液相からオーステナイト層が凝固するときに生じるＮｉの成分偏析が、そのまま保持されやすい。 The solidified structure is preferably FA mode or A mode for segregation of Ni components, which is important for improving the etchability. The diffusion rate of Ni in the solidified structure differs between austenite and δ ferrite, and the diffusion rate of austenite is slower. In the FA mode, the segregation of the Ni component occurs due to the crystallization of the primary crystal ferrite, and then the austenite having a slow diffusion rate crystallizes, so that the Ni component segregation is easily maintained. Further, in the A mode, the segregation of Ni components generated when the austenite layer solidifies from the liquid phase is easily retained as it is.
したがって、上述のＸ値が３未満となるようなＦＡモードまたはＡモードを有するステンレス鋼板は、Ｎｉの成分偏析に好適である。このように、上述の（１）式は本発明者等により調査検討の結果から導き出された関係式であり、ステンレス鋼板の凝固組織を形態制御する上で有効な指標である。 Therefore, a stainless steel sheet having an FA mode or an A mode such that the X value is less than 3 is suitable for segregation of Ni components. As described above, the above-mentioned equation (1) is a relational expression derived from the results of investigation and examination by the present inventor and the like, and is an effective index for morphological control of the solidified structure of the stainless steel sheet.
以下に、本実施形態に係るステンレス鋼板において好ましい成分の含有量を示す。なお、化学組成における「％」は特に断らない限り「質量％」を意味する。 The contents of preferable components in the stainless steel sheet according to the present embodiment are shown below. In addition, "%" in a chemical composition means "mass%" unless otherwise specified.
（Ｃ）
Ｃ（炭素）は、鋼の強度を向上させる元素である。ただし、Ｃ含有量が高くなりすぎると延性・靱性が低下する。また、多量のＣ添加はエッチング液に溶解しないスマット発生の原因となり、エッチング性を低下させる。そのため、Ｃ含有量は０．０８％以下に制限されることが好ましい。
(C)
C (carbon) is an element that improves the strength of steel. However, if the C content is too high, ductility and toughness will decrease. Further, the addition of a large amount of C causes the generation of smut that does not dissolve in the etching solution, and reduces the etching property. Therefore, the C content is preferably limited to 0.08% or less.
（Ｓｉ）
Ｓｉ（ケイ素）は、製鋼での脱酸作用を有する元素である。ただし、多量のＳｉ含有はＳｉ酸化物を主体とする硬質な介在物の形成を招き、強度、疲労特性、およびエッチング性に悪影響を及ぼす。したがって、Ｓｉ含有量は１．００％以下に制限されることが好ましい。
(Si)
Si (silicon) is an element that has a deoxidizing effect in steelmaking. However, a large amount of Si content causes the formation of hard inclusions mainly composed of Si oxide, which adversely affects the strength, fatigue characteristics, and etchability. Therefore, the Si content is preferably limited to 1.00% or less.
（Ｍｎ）
Ｍｎ（マンガン）は、製鋼での脱酸作用を有する元素である。ただし、多量のＭｎ含有はＭｎ系の硬質な介在物の形成を招き、強度およびエッチング性が低下する要因となるため、Ｍｎ含有量は２．５０％以下に制限されることが好ましい。
(Mn)
Mn (manganese) is an element that has a deoxidizing effect in steelmaking. However, since a large amount of Mn content causes the formation of Mn-based hard inclusions and causes a decrease in strength and etchability, the Mn content is preferably limited to 2.50% or less.
（Ｐ、Ｓ）
Ｐ（リン）およびＳ（硫黄）は、ステンレス鋼板の靱性を低下させる元素である。そのため、Ｐは０．０４５％以下に、Ｓは０．０３０％以下にそれぞれ制限されることが好ましい。
(P, S)
P (phosphorus) and S (sulfur) are elements that reduce the toughness of stainless steel sheets. Therefore, it is preferable that P is limited to 0.045% or less and S is limited to 0.030% or less.
（Ｎｉ）
Ｎｉ（ニッケル）は、偏析によってステンレス鋼板のエッチング性を向上させる元素である。また、靱性向上にも有効である。Ｎｉ濃度の偏析を大きくするため、Ｎｉ含有量は７．００％以上であることが好ましい。ただし、Ｎｉは高価な元素であるため、製造コストの観点から１５．００％以下に制限されてもよい。
(Ni)
Ni (nickel) is an element that improves the etchability of stainless steel sheets by segregation. It is also effective in improving toughness. The Ni content is preferably 7.00% or more in order to increase the segregation of the Ni concentration. However, since Ni is an expensive element, it may be limited to 15.00% or less from the viewpoint of manufacturing cost.
（Ｃｒ）
Ｃｒ（クロム）は、ステンレス鋼板の耐食性向上に有効な元素である。Ｃｒの含有量は、１６．００％以上であることが好ましい。ただし多量のＣｒは靱性低下の要因となるため、Ｃｒの含有量は２０．００％以下に制限されることが好ましい。
(Cr)
Cr (chromium) is an element effective for improving the corrosion resistance of stainless steel sheets. The Cr content is preferably 16.00% or more. However, since a large amount of Cr causes a decrease in toughness, the Cr content is preferably limited to 20.00% or less.
（Ｍｏ）
Ｍｏ（モリブデン）は、耐食性向上に有効な元素である。Ｍｏ含有量は、２．００％以上であること好ましい。ただし、Ｍｏは高価な元素であるためコスト上昇を招くことから、Ｍｏ含有量は３．００％以下に制限されることが好ましい。
(Mo)
Mo (molybdenum) is an element effective for improving corrosion resistance. The Mo content is preferably 2.00% or more. However, since Mo is an expensive element and causes an increase in cost, the Mo content is preferably limited to 3.00% or less.
（Ｃｕ）
Ｃｕ（銅）は、オーステナイト層の安定化に有効な元素である。Ｃｕ含有量は、２．５０％以上であることが好ましい。ただし、過度のＣｕ添加は製造性の低下を招くので、Ｃｕ含有量は４．００％以下であることが好ましい。
(Cu)
Cu (copper) is an element effective for stabilizing the austenite layer. The Cu content is preferably 2.50% or more. However, since excessive addition of Cu causes a decrease in manufacturability, the Cu content is preferably 4.00% or less.
（Ｎ）
Ｎ（窒素）は、Ｃと同様、鋼の強度向上に寄与する元素である。ただし、過度にＮを含有させると表面欠陥が生じやすくなるため、Ｎ含有量は０．０６％以下に制限されることが好ましい。
(N)
Like C, N (nitrogen) is an element that contributes to improving the strength of steel. However, if N is excessively contained, surface defects are likely to occur, so the N content is preferably limited to 0.06% or less.
（Ｂ）
Ｂ（ホウ素）は、熱間加工性向上に有効な元素である。ただし、多量の添加は延性に悪影響を及ぼすので、Ｂ含有量は０．０１％以下に制限されることが好ましい。
(B)
B (boron) is an element effective for improving hot workability. However, since a large amount of addition adversely affects ductility, the B content is preferably limited to 0.01% or less.
本実施形態に係るステンレス鋼板は、上述の式（１）によって定まるＸ値が３未満であり、好適な態様としてはＣ、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ｎｉ、およびＣｒを含有し、残部がＦｅからなるものである。さらに別の態様では、上述の式（１）によって定まるＸ値が３未満であり、Ｃ、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ｎｉ、およびＣｒを含有し、さらに、Ｍｏ、Ｃｕ、Ｎ、およびＢのうちのいずれか２種以上を含有し、残部がＦｅおよび不可避的不純物を含むものである。 The stainless steel sheet according to the present embodiment has an X value of less than 3 determined by the above formula (1), and preferably contains C, Si, Mn, P, S, Ni, and Cr, and the balance is It is composed of Fe. In yet another embodiment, the X value determined by the above formula (1) is less than 3, contains C, Si, Mn, P, S, Ni, and Cr, and further contains Mo, Cu, N, and B. It contains any two or more of them, and the balance contains Fe and unavoidable impurities.
〔ステンレス鋼板の製造方法〕
本実施形態に係るステンレス鋼板の製造方法について説明する。当該製造方法は、熱間圧延工程と、焼鈍工程とを含む。なお、熱間圧延工程および焼鈍工程以外の工程については、従来一般的なステンレス鋼板の製造方法に従って実施してよい。
[Manufacturing method of stainless steel sheet]
A method for manufacturing a stainless steel sheet according to the present embodiment will be described. The manufacturing method includes a hot rolling step and an annealing step. The steps other than the hot rolling step and the annealing step may be carried out according to a conventional general method for manufacturing a stainless steel sheet.
（熱間圧延工程）
熱間圧延工程では、ステンレス鋼板の素材となる素材スラブに熱間圧延処理を施した後に、得られた熱延鋼板をコイル状に巻取る。ここで、熱間圧延処理における圧延率は９７％以下とする。このような圧延率であれば、熱間圧延処理において発生するひずみの蓄積が緩和され、Ｎｉ偏析消失のための駆動力が低下する。そのため、熱延鋼板が有するＮｉ偏析が熱間圧延処理によって消失しにくい。
(Hot rolling process)
In the hot rolling step, the material slab, which is the material of the stainless steel sheet, is hot-rolled, and then the obtained hot-rolled steel sheet is wound into a coil. Here, the rolling ratio in the hot rolling process is 97% or less. With such a rolling ratio, the accumulation of strain generated in the hot rolling process is alleviated, and the driving force for eliminating Ni segregation is reduced. Therefore, the Ni segregation of the hot-rolled steel sheet is unlikely to disappear by the hot rolling process.
また、熱延鋼板の巻取りは、４００℃以上７００℃以下の巻取り温度まで冷却した後に行う。巻取り温度がこのような温度であれば、熱による熱延鋼板のＮｉ偏析消失を低減できる。また、熱間圧延後における巻取り温度までの冷却は水冷であることが好ましい。水冷によって熱延鋼板を熱間圧延終了時の温度から巻取り温度まで急速に冷却することで、熱間圧延処理後に熱延鋼板が熱を保持する時間がより短くなる。そのため、熱延鋼板のＮｉ偏析消失をより低減できる。 Further, the hot-rolled steel sheet is wound after being cooled to a winding temperature of 400 ° C. or higher and 700 ° C. or lower. When the winding temperature is such a temperature, the disappearance of Ni segregation of the hot-rolled steel sheet due to heat can be reduced. Further, the cooling to the winding temperature after hot rolling is preferably water cooling. By rapidly cooling the hot-rolled steel sheet from the temperature at the end of hot rolling to the winding temperature by water cooling, the time for the hot-rolled steel sheet to retain heat after the hot rolling process becomes shorter. Therefore, the disappearance of Ni segregation of the hot-rolled steel sheet can be further reduced.
（焼鈍工程）
次に、熱延鋼板を軟質化するために、当該熱延鋼板に焼鈍を施す焼鈍工程を実施する。焼鈍工程における焼鈍温度は、９００℃以上１０００℃以下とする。このように、焼鈍温度を金属組織の再結晶に必要な最低限の温度範囲に設定することにより、焼鈍工程におけるＮｉ偏析消失を低減できる。
(Annealing process)
Next, in order to soften the hot-rolled steel sheet, an annealing step of annealing the hot-rolled steel sheet is carried out. The annealing temperature in the annealing step is 900 ° C. or higher and 1000 ° C. or lower. By setting the annealing temperature to the minimum temperature range required for recrystallization of the metal structure in this way, it is possible to reduce the disappearance of Ni segregation in the annealing step.
〔エッチング処理〕
本実施形態に係るステンレス鋼板をエッチング加工する場合に用いられるエッチング液の種類および濃度には特に制限がない。エッチング液は例えば、通常用いられる塩化第二鉄水溶液または塩化第二鉄を含む塩酸溶液等であってよい。また、エッチング加工の方法についても、ステンレス鋼板表面へのエッチング液のスプレーまたはステンレス鋼板のエッチング液への浸潤等、通常用いられる方法を用いてよい。
[Etching process]
There is no particular limitation on the type and concentration of the etching solution used when etching the stainless steel sheet according to the present embodiment. The etching solution may be, for example, a commonly used ferric chloride aqueous solution or a hydrochloric acid solution containing ferric chloride. Further, as the etching processing method, a commonly used method such as spraying an etching solution on the surface of the stainless steel sheet or infiltration of the stainless steel sheet into the etching solution may be used.
本発明は上述した各実施形態に限定されるものではなく、請求項に示した範囲で種々の変更が可能であり、異なる実施形態にそれぞれ開示された技術的手段を適宜組み合わせて得られる実施形態についても本発明の技術的範囲に含まれる。 The present invention is not limited to the above-described embodiments, and various modifications can be made within the scope of the claims, and the embodiments obtained by appropriately combining the technical means disclosed in the different embodiments. Is also included in the technical scope of the present invention.
本発明の一実施例について、図１および図２を参照して以下に説明する。 An embodiment of the present invention will be described below with reference to FIGS. 1 and 2.
〔鋼種および製造方法〕
以下の表１に示す化学成分を有する素材スラブを用いてステンレス鋼板を製造した。このとき、熱間圧延工程における巻取り温度および焼鈍工程における焼鈍温度については、以下の表２に示す巻取り温度および焼鈍温度を用いた。
[Steel grade and manufacturing method]
A stainless steel sheet was produced using a material slab having the chemical components shown in Table 1 below. At this time, as the winding temperature in the hot rolling process and the annealing temperature in the annealing process, the winding temperature and annealing temperature shown in Table 2 below were used.
なお、鋼種ＡおよびＣについては、２種類の仕上げ条件を試行した。表２に示す仕上げ条件における「熱延焼鈍鋼板」は、熱間圧延工程および焼鈍工程を実施したステンレス鋼板である。また、「冷延焼鈍鋼板」はこれらの工程の後にさらに従来一般的な冷間圧延工程を実施したステンレス鋼板である。なお、鋼種Ｂは熱延焼鈍鋼板条件のみ実施した。 For steel types A and C, two types of finishing conditions were tried. The "hot-rolled annealed steel sheet" under the finishing conditions shown in Table 2 is a stainless steel sheet that has undergone a hot rolling process and an annealing process. Further, the "cold-rolled annealed steel sheet" is a stainless steel sheet in which a conventional cold rolling process is further performed after these steps. For steel type B, only the hot-rolled annealed steel sheet condition was carried out.
実施例１〜４は本発明の規定範囲内の製造方法によって得られたステンレス鋼板であるのに対し、比較例１は巻取り温度が７００℃より高く、焼鈍温度が１０００℃より高い条件であり、本発明の規定範囲外の製造方法によって得られたステンレス鋼板である。 Examples 1 to 4 are stainless steel sheets obtained by a manufacturing method within the specified range of the present invention, whereas Comparative Example 1 has a winding temperature higher than 700 ° C. and an annealing temperature higher than 1000 ° C. , A stainless steel sheet obtained by a manufacturing method outside the specified range of the present invention.
〔偏析層のマッピング分析〕
実施例１〜４および比較例１のステンレス鋼板表面における偏析層を把握するために、ＥＰＭＡ（Electron Probe Micro Analyzer）によって各ステンレス鋼板表面の分析を行った。ＥＰＭＡは、日本電子株式会社製のJXA-8530F Plusを使用した。より具体的には、各ステンレス鋼板におけるＦｅ、Ｃｒ、Ｎｉ、およびＣｕの濃度について、ＥＰＭＡを使用した各ステンレス鋼板表面のマッピング分析を行った。マッピング分析の測定範囲は１０００μｍ２とした。
[Mapping analysis of segregation layer]
In order to grasp the segregated layer on the surface of the stainless steel sheets of Examples 1 to 4 and Comparative Example 1, the surface of each stainless steel sheet was analyzed by EPMA (Electron Probe Micro Analyzer). For EPMA, JXA-8530F Plus manufactured by JEOL Ltd. was used. More specifically, the mapping analysis of the surface of each stainless steel sheet using EPMA was performed for the concentrations of Fe, Cr, Ni, and Cu in each stainless steel sheet. The measurement range of the mapping analysis was 1000 μm 2 .
図１に示すように、実施例１〜４および比較例１のステンレス鋼板の表面について、それぞれＦｅ、Ｃｒ、Ｎｉ、およびＣｕの濃度分布を分析した。いずれの条件においても、Ｎｉの偏析が確認された。特に、実施例１〜４のステンレス鋼板については、Ｎｉの強い偏析が見られた。 As shown in FIG. 1, the concentration distributions of Fe, Cr, Ni, and Cu were analyzed on the surfaces of the stainless steel sheets of Examples 1 to 4 and Comparative Example 1, respectively. Segregation of Ni was confirmed under all conditions. In particular, strong segregation of Ni was observed in the stainless steel sheets of Examples 1 to 4.
〔Ｎｉ濃度ライン分析〕
次に、実施例１〜４および比較例１のステンレス鋼板の表面におけるＮｉ濃度のライン分析を行った。ライン分析にも、上述のＥＰＭＡを用いた。ライン分析では、上述のマッピング分析によりＮｉの偏析が確認された部分について、ステンレス鋼板の圧延方向に対し垂直方向に３００μｍの直線を設定し、当該直線上におけるＮｉ濃度を分析した。同様の分析を１０視野について行い、各視野について、得られたＮｉ濃度が最大となる部分と、Ｎｉ濃度が最小となる部分とのＮｉ濃度差を求め、当該Ｎｉ濃度差について１０視野の平均値を算出した。得られた平均値を、表２の「偏析層の濃度差（質量％）」に示した。
[Ni concentration line analysis]
Next, a line analysis of the Ni concentration on the surfaces of the stainless steel sheets of Examples 1 to 4 and Comparative Example 1 was performed. The EPMA described above was also used for line analysis. In the line analysis, a straight line of 300 μm was set in the direction perpendicular to the rolling direction of the stainless steel sheet for the portion where the segregation of Ni was confirmed by the above mapping analysis, and the Ni concentration on the straight line was analyzed. The same analysis was performed for 10 visual fields, and for each visual field, the Ni concentration difference between the portion where the obtained Ni concentration was maximum and the portion where the Ni concentration was minimum was obtained, and the average value of the 10 visual fields was obtained for the Ni concentration difference. Was calculated. The obtained average values are shown in "Difference in concentration (mass%) of segregated layer" in Table 2.
図２および表２に示すように、実施例１〜４のステンレス鋼板については、Ｎｉ濃度差が１．５質量％以上のＮｉ偏析層が確認された。一方、比較例１のステンレス鋼板では、Ｎｉ濃度差が１．５質量％未満であった。 As shown in FIGS. 2 and 2, in the stainless steel sheets of Examples 1 to 4, a Ni segregation layer having a Ni concentration difference of 1.5% by mass or more was confirmed. On the other hand, in the stainless steel sheet of Comparative Example 1, the difference in Ni concentration was less than 1.5% by mass.
〔エッチング速度〕
実施例１〜４および比較例１のステンレス鋼板に対して、エッチング処理を実施し、各ステンレス鋼板のエッチング性を調査した。まず、各ステンレス鋼板を５質量％オルソケイ酸ナトリウムに浸漬し、６０℃条件下でアノード電流を５Ａ／ｄｍ２となるように１０秒流すことで、アルカリ電解脱脂処理を行った。その後、各ステンレス鋼板を３０℃条件下で５質量％塩酸に１０秒浸漬して中和処理を行った。そして、４０ｇ／Ｌ塩酸を含む１４質量％塩化第二鉄溶液をエッチング液として、中和処理後の各ステンレス鋼板を当該エッチング液に浸漬し、５５℃条件下で４時間反応させることでエッチング処理を行った。エッチング処理後の各ステンレス鋼板について、板厚の減少量（μｍ）を測定した。
[Etching speed]
Etching treatments were carried out on the stainless steel sheets of Examples 1 to 4 and Comparative Example 1, and the etching properties of each stainless steel sheet were investigated. First, each stainless steel sheet was immersed in 5% by mass sodium orthosilicate, and an anode current of 5 A / dm 2 was passed for 10 seconds under the condition of 60 ° C. to perform an alkaline electrolytic degreasing treatment. Then, each stainless steel sheet was immersed in 5 mass% hydrochloric acid for 10 seconds under the condition of 30 ° C. for neutralization treatment. Then, using a 14% by mass ferric chloride solution containing 40 g / L hydrochloric acid as an etching solution, each stainless steel sheet after the neutralization treatment is immersed in the etching solution and reacted under 55 ° C. conditions for 4 hours for etching treatment. Was done. The amount of decrease in plate thickness (μm) was measured for each stainless steel sheet after the etching treatment.
表２に示すように、Ｎｉ濃度差が１．５質量％以上のＮｉ偏析層が確認された実施例１〜４のステンレス鋼板における板厚減少量と、当該Ｎｉ偏析層が確認されなかった比較例１の板厚減少量とは、少なくとも５倍以上の大きな差が見られた。また、実施例１〜４の中でも上述のＸ値が０以下である鋼種ＡまたはＢを用いた実施例１〜３と、Ｘ値が０以上３未満である実施例４との間には、２倍以上の板厚減少量の差が見られた。 As shown in Table 2, the amount of decrease in the thickness of the stainless steel sheets of Examples 1 to 4 in which the Ni segregation layer having a Ni concentration difference of 1.5% by mass or more was confirmed and the comparison in which the Ni segregation layer was not confirmed. A large difference of at least 5 times or more was observed from the amount of decrease in plate thickness of Example 1. Further, among Examples 1 to 4, between Examples 1 to 3 using the steel type A or B having an X value of 0 or less and Example 4 having an X value of 0 or more and less than 3. A difference of more than 2 times in the amount of plate thickness reduction was observed.
以上の結果から、Ｎｉ偏析層を有するステンレス鋼板は、エッチング性に優れることが示された。また、Ｎｉ偏析層を有するステンレス鋼板の中でも、上述のＸ値が０以下であれば、より優れたエッチング性が得られることが示された。 From the above results, it was shown that the stainless steel sheet having the Ni segregation layer is excellent in etching property. Further, it was shown that even among the stainless steel sheets having a Ni segregation layer, when the above-mentioned X value is 0 or less, better etching properties can be obtained.
Claims (5)
前記偏析層において、Ｎｉ濃度が最大となる部分と、Ｎｉ濃度が最小となる部分とのＮｉ濃度差が１．５質量％以上である、ステンレス鋼板。 It has a segregation layer in which Ni segregates.
A stainless steel sheet having a Ni concentration difference of 1.5% by mass or more between a portion having a maximum Ni concentration and a portion having a minimum Ni concentration in the segregation layer.
Ｘ＝３０（Ｃ＋Ｎ）＋０．５Ｍｎ＋Ｎｉ−１．３Ｃｒ＋１１．８ （１）
ここで、（１）式の元素記号の箇所には質量％で表される当該元素の含有量が代入され、無添加の元素については０（ゼロ）が代入される。 The stainless steel sheet according to claim 1, which has a chemical composition in which the X value determined by the following formula (1) is less than 3.
X = 30 (C + N) + 0.5Mn + Ni-1.3Cr + 11.8 (1)
Here, the content of the element represented by mass% is substituted in the place of the element symbol in the formula (1), and 0 (zero) is substituted for the element without addition.
巻取り温度を４００℃以上７００℃以下とし、圧延率を９７％以下とする熱間圧延工程と、
焼鈍温度を９００℃以上１０００℃以下とする焼鈍工程と、を含む、ステンレス鋼板の製造方法。 A method for producing a stainless steel sheet having a segregated layer in which Ni is segregated, and the difference in Ni concentration between the portion having the maximum Ni concentration and the portion having the minimum Ni concentration in the segregated layer is 1.5% by mass or more. And
A hot rolling process in which the winding temperature is 400 ° C or higher and 700 ° C or lower and the rolling ratio is 97% or lower.
A method for manufacturing a stainless steel sheet, which comprises an annealing step of setting the annealing temperature to 900 ° C. or higher and 1000 ° C. or lower.
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| JP (1) | JP7296756B2 (en) |
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| JPH07268455A (en) * | 1994-03-29 | 1995-10-17 | Nippon Steel Corp | Production of cr-ni stainless alloy free from microracking in hot rolling |
| JPH07292438A (en) * | 1994-04-26 | 1995-11-07 | Nippon Steel Corp | Austenitic stainless cold rolled steel sheet excellent in oxidation resistance and its production |
| JPH08281305A (en) * | 1995-04-10 | 1996-10-29 | Nippon Steel Corp | Manufacture of cr-ni base stainless steel without generating surface defect in hot rolling |
| JPH09279248A (en) * | 1996-04-18 | 1997-10-28 | Nippon Steel Corp | Production of chrome-nickel stainless hot rolled steel sheet and cold rolled steel sheet excellent in surface quality and workability |
| JPH10204586A (en) * | 1997-01-21 | 1998-08-04 | Hitachi Ltd | Austenitic stainless steel excellent in stress corrosion cracking resistance, and its production |
| JP2000328142A (en) * | 1999-05-11 | 2000-11-28 | Nisshin Steel Co Ltd | Production of stainless steel strip small in unevenness of gloss |
| JP2003313643A (en) * | 2002-04-24 | 2003-11-06 | Nippon Steel Corp | Cr-Ni STAINLESS STEEL THIN-SHEET |
| JP2005314772A (en) * | 2004-04-30 | 2005-11-10 | Nippon Yakin Kogyo Co Ltd | Stainless steel sheet to be photo-etched and manufacturing method therefor |
| KR20110069602A (en) * | 2009-12-17 | 2011-06-23 | 주식회사 포스코 | A method of manufacturing ostenite-origin stainless steel plate by using twin roll strip caster and austenite stainless steel plate manufactured thereby |
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2019
- 2019-03-28 JP JP2019064829A patent/JP7296756B2/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02173243A (en) * | 1988-12-24 | 1990-07-04 | Nippon Mining Co Ltd | Stainless steel excellent in etching workability |
| JPH07268455A (en) * | 1994-03-29 | 1995-10-17 | Nippon Steel Corp | Production of cr-ni stainless alloy free from microracking in hot rolling |
| JPH07292438A (en) * | 1994-04-26 | 1995-11-07 | Nippon Steel Corp | Austenitic stainless cold rolled steel sheet excellent in oxidation resistance and its production |
| JPH08281305A (en) * | 1995-04-10 | 1996-10-29 | Nippon Steel Corp | Manufacture of cr-ni base stainless steel without generating surface defect in hot rolling |
| JPH09279248A (en) * | 1996-04-18 | 1997-10-28 | Nippon Steel Corp | Production of chrome-nickel stainless hot rolled steel sheet and cold rolled steel sheet excellent in surface quality and workability |
| JPH10204586A (en) * | 1997-01-21 | 1998-08-04 | Hitachi Ltd | Austenitic stainless steel excellent in stress corrosion cracking resistance, and its production |
| JP2000328142A (en) * | 1999-05-11 | 2000-11-28 | Nisshin Steel Co Ltd | Production of stainless steel strip small in unevenness of gloss |
| JP2003313643A (en) * | 2002-04-24 | 2003-11-06 | Nippon Steel Corp | Cr-Ni STAINLESS STEEL THIN-SHEET |
| JP2005314772A (en) * | 2004-04-30 | 2005-11-10 | Nippon Yakin Kogyo Co Ltd | Stainless steel sheet to be photo-etched and manufacturing method therefor |
| KR20110069602A (en) * | 2009-12-17 | 2011-06-23 | 주식회사 포스코 | A method of manufacturing ostenite-origin stainless steel plate by using twin roll strip caster and austenite stainless steel plate manufactured thereby |
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