JP2019501289A - Austenitic stainless steel with improved workability - Google Patents
Austenitic stainless steel with improved workability Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- 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
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- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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Abstract
加工性が向上したオーステナイト系ステンレス鋼が開示される。開示されたオーステナイト系ステンレス鋼は、重量％で、シリコン（Ｓｉ）：０．１％〜０．６５％、マンガン（Ｍｎ）：０．２％〜３．０％、ニッケル（Ｎｉ）：６．５％〜１０．０％、クロム（Ｃｒ）：１６．５％〜２０．０％、銅（Ｃｕ）：６．０％以下（０は除外）、炭素（Ｃ）および窒素（Ｎ）：０．０８％以下（０は除外）、残りはＦｅおよび不可避な不純物を含み、真ひずみ０．１５〜０．４の範囲で加工硬化速度が１５００ＭＰａ以下である。したがって、真ひずみと加工硬化速度が制御され、シンクボウルなどに加工する際に、加工量が多いエッジ部分でも成形後に遅れ破壊の発生を防止することができる。【選択図】図２An austenitic stainless steel with improved workability is disclosed. The disclosed austenitic stainless steel is, by weight, silicon (Si): 0.1% to 0.65%, manganese (Mn): 0.2% to 3.0%, nickel (Ni): 6. 5% to 10.0%, chromium (Cr): 16.5% to 20.0%, copper (Cu): 6.0% or less (excluding 0), carbon (C) and nitrogen (N): 0 0.08% or less (excluding 0), the rest contains Fe and inevitable impurities, and the work hardening rate is 1500 MPa or less in the range of true strain of 0.15 to 0.4. Therefore, true strain and work hardening speed are controlled, and when processing into a sink bowl or the like, it is possible to prevent the occurrence of delayed fracture after molding even at the edge portion where the processing amount is large. [Selection] Figure 2
Description
本発明は、加工性が向上したオーステナイト系ステンレス鋼（ａｕｓｔｅｎｉｔｉｃ ｓｔａｉｎｌｅｓｓ ｓｔｅｅｌ）に関し、より詳しくは、複雑な形状に加工しても、遅れ破壊などの欠陥が発生しない加工性が向上したオーステナイト系ステンレス鋼に関する。 The present invention relates to an austenitic stainless steel having improved workability, and more particularly, an austenitic stainless steel having improved workability in which defects such as delayed fracture do not occur even when processed into a complex shape. About.
キッチン用流し台のシンクボウルには、一般的にステンレス鋼が使用される。主に、特定の汎用ステンレス鋼が使用されるが、このようなステンレス鋼は、一般的なシンクボウル形状に成形するのに問題がないため、広く使用されている。 Stainless steel is generally used for sink bowls in kitchen sinks. Although a specific general-purpose stainless steel is mainly used, since such a stainless steel has no problem in forming into a general sink bowl shape, it is widely used.
しかし、最近、市場での競争力強化のために、多様で且つ複雑な形状のシンクボウルを設計しようとする試みが多くなっている。この場合、従来使用されているステンレス鋼をそのまま適用すると、図１に示すように、シンクボウルの成形後に遅れ破壊が発生する問題がある。図１は、従来のオーステナイト系ステンレス鋼でシンクボウルを加工した後のエッジ部を撮影した写真である。 Recently, however, many attempts have been made to design sink bowls with various and complex shapes in order to enhance competitiveness in the market. In this case, if the conventionally used stainless steel is applied as it is, there is a problem that delayed fracture occurs after forming the sink bowl as shown in FIG. FIG. 1 is a photograph of an edge portion after processing a sink bowl with conventional austenitic stainless steel.
遅れ破壊は、鋼板の加工後に一定時間が経過した後に破裂が発生するものであって、加工された形状に応じて加工量が多い部分で主に発生する。 Delayed fracture occurs when a certain amount of time elapses after the processing of the steel sheet, and mainly occurs at a portion where the processing amount is large according to the processed shape.
通常、オーステナイト系ステンレス鋼は、高加工性であるが、加工率が限界を超えると、時効割れという遅れ破壊が発生する。このような割れは、オーステナイト系ステンレス鋼をディープドローイング（ｄｅｅｐ ｄｒａｗｉｎｇ）加工した後に数分から数か月が経過した後に発生し、ディープドローイング方向に直線的に進行するが、微視的に見れば、オーステナイト系ステンレス鋼の結晶粒／粒界に関係なくジグザグ状に進行する。 Usually, austenitic stainless steel has high workability, but when the processing rate exceeds the limit, delayed fracture called aging cracking occurs. Such cracks occur after a few minutes to several months after deep drawing of austenitic stainless steel and proceed linearly in the deep drawing direction. Progresses in a zigzag pattern regardless of the crystal grains / grain boundaries of austenitic stainless steel.
本発明は、上記従来の問題点に鑑みてなされたものであって、本発明の目的は、シンクボウルに加工する際に、遅れ破壊が発生しない加工性に優れたオーステナイト系ステンレス鋼管を提供することにある。 The present invention has been made in view of the above-described conventional problems, and an object of the present invention is to provide an austenitic stainless steel pipe excellent in workability in which delayed fracture does not occur when processing into a sink bowl. There is.
上記目的を達成するためになされた本発明の一態様による加工性が向上したオーステナイト系ステンレス鋼は、重量％で、シリコン（Ｓｉ）を０．１％〜０．６５％、マンガン（Ｍｎ）を０．２％〜３．０％、ニッケル（Ｎｉ）を６．５％〜１０．０％、クロム（Ｃｒ）を１６．５％〜２０．０％、銅（Ｃｕ）を６．０％以下（０は除外）、炭素（Ｃ）および窒素（Ｎ）を合計で０．０８％以下（０は除外）、残りにＦｅおよび不可避な不純物を含み、真ひずみ０．１５〜０．４の範囲で加工硬化速度が１５００ＭＰａ以下であることを特徴とする。 The austenitic stainless steel with improved workability according to one aspect of the present invention made to achieve the above object is 0.1% to 0.65% silicon (Si) and manganese (Mn) in weight%. 0.2% to 3.0%, nickel (Ni) 6.5% to 10.0%, chromium (Cr) 16.5% to 20.0%, copper (Cu) 6.0% or less (Excludes 0), carbon (C) and nitrogen (N) in a total of 0.08% or less (excludes 0), the remainder includes Fe and inevitable impurities, and the true strain ranges from 0.15 to 0.4 The work hardening rate is 1500 MPa or less.
前記オーステナイト系ステンレス鋼は、炭素（Ｃ）および窒素（Ｎ）を合計で０．０５重量％以下（０は除外）を含み得る。
さらに、炭素（Ｃ）および窒素（Ｎ）を合計で０．０３重量％以下（０は除外）を含むことが好ましい。
前記オーステナイト系ステンレス鋼は、ＡＳＴＭ結晶粒度番号が８以下であることが好ましい。
また、前記オーステナイト系ステンレス鋼は、フェライト相分率またはマルテンサイト相分率が１％未満であることが好ましい。
The austenitic stainless steel may contain a total of 0.05% by weight or less (excluding 0) of carbon (C) and nitrogen (N).
Furthermore, it is preferable that carbon (C) and nitrogen (N) are contained in total 0.03% by weight or less (excluding 0).
The austenitic stainless steel preferably has an ASTM grain size number of 8 or less.
The austenitic stainless steel preferably has a ferrite phase fraction or a martensite phase fraction of less than 1%.
本発明によれば、シンクボウルなどに加工する際に、加工量が多いエッジ部分でも成形後に遅れ破壊の発生を防止することができる、真ひずみと加工硬化速度が制御されたオーステナイト系ステンレス鋼をすることができる。 According to the present invention, when processing into a sink bowl or the like, an austenitic stainless steel with controlled true strain and work hardening rate, which can prevent the occurrence of delayed fracture after forming even at the edge portion where the processing amount is large. can do.
以下、本発明を実施するための具体例を、図面を参照しながら詳細に説明する。以下の実施形態は、本発明の属する技術分野における通常の知識を有する者に本発明の技術思想を十分に伝達するために提示するものである。本発明は、本明細書に提示した実施形態のみに限定されず、他の態様で具現され得る。図面は、本発明を明確にするために、説明と無関係な部分は図示を省略し、理解を助けるために構成要素のサイズを多少誇張して表現する。 Hereinafter, specific examples for carrying out the present invention will be described in detail with reference to the drawings. The following embodiments are presented in order to sufficiently convey the technical idea of the present invention to those who have ordinary knowledge in the technical field to which the present invention belongs. The present invention is not limited to the embodiments presented herein and can be embodied in other ways. In the drawings, for the purpose of clarifying the present invention, portions not related to the description are not shown, and the sizes of the components are exaggerated to help understanding.
本発明の一実施形態による加工性が向上したオーステナイト系ステンレス鋼は、重量％で、シリコン（Ｓｉ）を０．１％〜０．６５％、マンガン（Ｍｎ）を０．２％〜３．０％、ニッケル（Ｎｉ）を６．５％〜１０．０％、クロム（Ｃｒ）を１６．５％〜２０．０％、銅（Ｃｕ）を６．０％以下（０は除外）、炭素（Ｃ）および窒素（Ｎ）を合計で０．０８％以下（０は除外）、残りにＦｅおよび不可避な不純物を含む。 The austenitic stainless steel with improved workability according to one embodiment of the present invention is 0.1% to 0.65% silicon (Si) and 0.2% to 3.0% manganese (Mn) by weight. %, Nickel (Ni) 6.5% to 10.0%, chromium (Cr) 16.5% to 20.0%, copper (Cu) 6.0% or less (excluding 0), carbon ( C) and nitrogen (N) in total are 0.08% or less (excluding 0), and the remainder contains Fe and inevitable impurities.
以下、本実施形態による加工性が向上したオーステナイト系ステンレス鋼管を構成する成分の数値限定理由について説明する。 Hereinafter, the reason for limiting the numerical values of the components constituting the austenitic stainless steel pipe with improved workability according to the present embodiment will be described.
シリコン（Ｓｉ）は、０．１重量％〜０．６５重量％の範囲内で調節して添加する。 Silicon (Si) is added within the range of 0.1 wt% to 0.65 wt%.
シリコン（Ｓｉ）は、脱酸素のために必ず添加される元素であり、その含有量をあまりに低い量に制御するには、製鋼工程のコストが高くなるので、０．１重量％以上に限定する。 Silicon (Si) is an element that must be added for deoxidation, and in order to control its content to be too low, the cost of the steelmaking process increases, so it is limited to 0.1% by weight or more. .
しかし、過度に高い含有量のＳｉを添加すると、Ｓｉは、固溶強化元素であるため、強度が増大して、素材が硬質化される。そして、Ｓｉは、酸素と結合して介在物を形成することにより、耐食性が低下するので、その上限を０．６５重量％に制限する。 However, when an excessively high content of Si is added, since Si is a solid solution strengthening element, the strength is increased and the material is hardened. And since Si couple | bonds with oxygen and forms an inclusion and corrosion resistance falls, the upper limit is restrict | limited to 0.65 weight%.
マンガン（Ｍｎ）は、０．２重量％〜３．０重量％の範囲内で調節して添加する。 Manganese (Mn) is added within the range of 0.2 wt% to 3.0 wt%.
マンガン（Ｍｎ）は、脱酸素のために必ず添加されるだけでなく、オーステナイト相の安定性を増加させ、フェライトあるいはマルテンサイトの生成量を減らす元素であり、加工硬化速度を低減する効果があり、０．２重量％以上を添加する。 Manganese (Mn) is an element that is not only added for deoxidation but also increases the stability of the austenite phase and reduces the amount of ferrite or martensite produced, and has the effect of reducing the work hardening rate. , 0.2% by weight or more is added.
しかし、Ｍｎは、固溶強化元素であって、過度に高い含有量のＭｎ添加は、鋼の強度増加の虞があり、材料の耐食性を低下させるので、その上限は３．０重量％に制限する。 However, Mn is a solid solution strengthening element, and addition of Mn with an excessively high content may increase the strength of steel and lower the corrosion resistance of the material, so the upper limit is limited to 3.0% by weight. To do.
ニッケル（Ｎｉ）は、６．５重量％〜１０．０重量％の範囲内で調節して添加する。 Nickel (Ni) is added within a range of 6.5 wt% to 10.0 wt%.
ニッケル（Ｎｉ）は、クロム（Ｃｒ）とともに添加すると、耐孔食性のような耐食性の向上に効果的だけでなく、その含有量が増加すると、オーステナイト鋼の軟質化および加工硬化速度を低下させる効果がある。また、ニッケル（Ｎｉ）は、オーステナイト相の安定性を増加させ、鋼管のフェライトあるいはマルテンサイトの生成量を低減させる元素であり、オーステナイトのバランス維持のために６．５重量％以上を添加する。 When nickel (Ni) is added together with chromium (Cr), it is effective not only for improving corrosion resistance such as pitting corrosion resistance, but also for increasing the content thereof, the effect of softening austenitic steel and reducing the work hardening rate. There is. Nickel (Ni) is an element that increases the stability of the austenite phase and reduces the amount of ferrite or martensite produced in the steel pipe, and is added in an amount of 6.5% by weight or more for maintaining the balance of austenite.
しかし、過度に高い含有量のニッケル（Ｎｉ）添加は、鋼のコスト上昇を招くので、上限を１０．０重量％に制限する。 However, adding an excessively high content of nickel (Ni) causes an increase in the cost of the steel, so the upper limit is limited to 10.0% by weight.
クロム（Ｃｒ）は、１６．５重量％〜２０．０重量％の範囲内で調節して添加する。 Chromium (Cr) is added within the range of 16.5 wt% to 20.0 wt%.
クロム（Ｃｒ）は、ステンレス鋼の耐食性を向上させる必須元素であって、汎用に使用されるためには、１６．５重量％以上が添加されなければならない。 Chromium (Cr) is an essential element that improves the corrosion resistance of stainless steel, and in order to be used for general purposes, 16.5% by weight or more must be added.
しかし、Ｃｒは、固溶強化元素であって、過度に高い含有量のＣｒ添加は、コストの上昇を招くので、上限を２０．０重量％に制限する。 However, Cr is a solid solution strengthening element, and addition of an excessively high content of Cr causes an increase in cost, so the upper limit is limited to 20.0% by weight.
銅（Ｃｕ）は、６．０重量％以下（０は除外）の範囲内で調節して添加する。 Copper (Cu) is added within a range of 6.0% by weight or less (excluding 0).
銅（Ｃｕ）は、オーステナイト鋼の軟質化および加工硬化速度を低下させる効果があり、鋼のフェライトあるいはマルテンサイトの生成量を低減させる元素であって、これを添加することが好ましい。 Copper (Cu) is an element that has the effect of softening austenitic steel and lowering the work hardening rate, and is an element that reduces the amount of ferrite or martensite produced in the steel, and it is preferable to add this.
しかし、過度に高い含有量の銅（Ｃｕ）添加は、熱間加工性を低下させ、かえってオーステナイト相を硬質化させ、コスト上昇および製造難易度を上昇させるので、その上限を６．０重量％に制限する。 However, the addition of an excessively high content of copper (Cu) decreases the hot workability, hardens the austenite phase, and increases the cost and the difficulty of production, so the upper limit is 6.0% by weight. Limit to.
炭素（Ｃ）および窒素（Ｎ）の合計は、０．０８重量％以下（０は除外）で添加されなければならない。 The sum of carbon (C) and nitrogen (N) must be added at 0.08 wt% or less (excluding 0).
炭素（Ｃ）および窒素（Ｎ）は、侵入型（ｉｎｔｅｒｓｔｉｔｉａｌ）固溶強化元素であって、オーステナイト系ステンレス鋼を硬質化させるだけでなく、その含有量が高いと、加工時に発生する変形有機マルテンサイトを硬質化して、材料の加工硬化度が増加する。 Carbon (C) and nitrogen (N) are interstitial solid solution strengthening elements that not only harden austenitic stainless steel, but if the content is high, deformed organic martens that are generated during processing. Hardening the site increases the work hardening of the material.
したがって、炭素（Ｃ）および窒素（Ｎ）の含有量を制限する必要性があり、本発明では、炭素（Ｃ）および窒素（Ｎ）の合計の含有量を０．０８重量％以下に制限する。材料の硬質化を防止するために、好ましくは、炭素（Ｃ）および窒素（Ｎ）の合計の含有量は、０．０５重量％以下（０は除外）、より好ましくは、炭素（Ｃ）および窒素（Ｎ）の合計の含有量は、０．０３重量％以下（０は除外）である。 Therefore, there is a need to limit the content of carbon (C) and nitrogen (N), and in the present invention, the total content of carbon (C) and nitrogen (N) is limited to 0.08% by weight or less. . In order to prevent hardening of the material, preferably the total content of carbon (C) and nitrogen (N) is 0.05% by weight or less (excluding 0), more preferably carbon (C) and The total content of nitrogen (N) is 0.03% by weight or less (excluding 0).
また、オーステナイト系ステンレス鋼は、真ひずみ０．１５〜０．４の範囲で加工硬化速度が１５００ＭＰａ以下である。 In addition, the austenitic stainless steel has a work hardening rate of 1500 MPa or less within a true strain range of 0.15 to 0.4.
図２は、本発明の一実施形態によるオーステナイト系ステンレス鋼でシンクボウルを加工した後、エッジ部分を撮影した写真図である。図２は、図１のような形状のシンクボウル加工時に本発明で提示する方法で製造されたステンレス鋼の適用時に加工量が多いエッジ部分でも成形後に遅れ破壊が発生しないことを示す。 FIG. 2 is a photograph showing an edge portion after processing a sink bowl with austenitic stainless steel according to an embodiment of the present invention. FIG. 2 shows that delayed fracture does not occur after forming even at the edge portion where the amount of processing is large when the stainless steel manufactured by the method presented in the present invention is applied when processing the sink bowl having the shape shown in FIG.
図３は、本発明の一実施例によるオーステナイト系ステンレス鋼の真ひずみと加工硬化速度の相関関係を示すグラフである。図３は、従来のステンレス鋼と本発明のステンレス鋼の１軸引張試験後に真ひずみによる加工硬化速度を示す。従来のステンレス鋼は、真ひずみ０．１５以上０．４以下の範囲で、加工硬化速度が１５００ＭＰａ以上に増加するのに対し、本発明によるステンレス鋼の加工硬化速度は、１５００ＭＰａ以下に維持されることを示す。 FIG. 3 is a graph showing the correlation between the true strain and work hardening rate of austenitic stainless steel according to an embodiment of the present invention. FIG. 3 shows the work hardening rate due to true strain after the uniaxial tensile test of the conventional stainless steel and the stainless steel of the present invention. In the conventional stainless steel, the work hardening rate increases to 1500 MPa or more in the range of true strain of 0.15 to 0.4, whereas the work hardening rate of the stainless steel according to the present invention is maintained at 1500 MPa or less. It shows that.
一般的にステンレス鋼を加工すると、加工硬化が発生する。遅れ破壊は、加工量が多い場合に発生するので、本発明では、真ひずみが０．１５以上０．４以下の範囲で加工硬化を調べた。 Generally, when stainless steel is processed, work hardening occurs. Since delayed fracture occurs when the amount of machining is large, in the present invention, work hardening was examined in the range of true strain of 0.15 to 0.4.
加工硬化は、ステンレス鋼の真ひずみ変化に対する真応力の変化の比である加工硬化速度で定量的に示した。図３を参照すると、従来使用されたステンレス鋼（比較例）では、加工硬化速度が真ひずみ０．１５以上０．４以下の範囲で１５００ＭＰａ以上であることが分かる。 Work hardening was quantitatively expressed as the work hardening rate, which is the ratio of the change in true stress to the change in true strain of stainless steel. Referring to FIG. 3, it can be seen that conventionally used stainless steel (comparative example) has a work hardening rate of 1500 MPa or more in a range of true strain of 0.15 to 0.4.
図３を参照すると、本発明（実施例）では、真ひずみ０．１５以上０．４以下の範囲で加工硬化速度が１５００ＭＰａ以下に制御されることにより、加工後にも遅れ破壊が発生せず、加工性に優れたステンレス鋼を得ることができた。 Referring to FIG. 3, in the present invention (Example), the work hardening rate is controlled to 1500 MPa or less in the range of true strain of 0.15 or more and 0.4 or less, so that no delayed fracture occurs after processing. Stainless steel with excellent workability could be obtained.
加工硬化速度は、板材をＪＩＳ１３Ｂ、ＪＩＳ５規格に準拠して引張試験片を加工した後、破断されるまで１軸引張試験をして得られた真ひずみと真応力値から計算した。引張試験の規格は、特に限定されず、規格は単に例として提供される。遅れ破壊を試験するために、板材は、実際にシンクボウル形状に加工してもよく、または直径５０ｍｍ、高さ１００ｍｍの簡単なカップ形状に加工してもよい。 The work hardening rate was calculated from the true strain and the true stress value obtained by processing a tensile test piece in accordance with JIS13B and JIS5 standards and then conducting a uniaxial tensile test until it was broken. The standard for the tensile test is not particularly limited, and the standard is provided merely as an example. In order to test delayed fracture, the plate material may actually be processed into a sink bowl shape, or may be processed into a simple cup shape with a diameter of 50 mm and a height of 100 mm.
例えば、ステンレス鋼のＡＳＴＭ結晶粒度番号が８以下である。この結晶粒度は、ステンレス鋼管の長さ方向の断面で測定した結晶粒度である。 For example, the ASTM grain size number of stainless steel is 8 or less. This crystal grain size is a crystal grain size measured in a cross section in the length direction of a stainless steel pipe.
例えば、ステンレス鋼は、フェライト相分率が１％未満であり、マルテンサイト相分率が１％未満である。すなわち、ステンレス鋼は、磁化方式で測定したフェライトまたはマルテンサイト分率が１％未満である。 For example, stainless steel has a ferrite phase fraction of less than 1% and a martensite phase fraction of less than 1%. That is, stainless steel has a ferrite or martensite fraction measured by a magnetization method of less than 1%.
以下、実施例を通じて本発明をより詳細に説明する。 Hereinafter, the present invention will be described in more detail through examples.
＜実施例＞
表１に示す発明例１〜発明例１１および比較例１〜２の成分を含むオーステナイト系ステンレス鋼スラブを連続鋳造により製造した。その後、オーステナイト系ステンレス鋼スラブを熱間圧延し、総圧下率５０％で冷間圧延して、冷延鋼板を製造した。
<Example>
An austenitic stainless steel slab containing the components of Invention Examples 1 to 11 and Comparative Examples 1 and 2 shown in Table 1 was produced by continuous casting. Thereafter, the austenitic stainless steel slab was hot-rolled and cold-rolled at a total reduction of 50% to produce a cold-rolled steel sheet.
その後、冷延鋼板を利用してシンクボウルへの加工を行い、鋼板の加工硬化速度を測定し、シンクボウルに加工した後、遅れ破壊の有無を目視で観察して、以下の表２に示した。 After that, the cold-rolled steel plate was processed into a sink bowl, the work hardening rate of the steel plate was measured, and after processing into the sink bowl, the presence or absence of delayed fracture was visually observed and shown in Table 2 below. It was.
表１および表２は、本発明で提示する成分範囲と加工硬化速度に応じて製造したステンレス鋼は遅れ破壊が発生しないことを示す。一方、従来使用されるステンレス鋼の比較例２種は、同条件で加工硬化速度が１５００ＭＰａ以下を満たさず、遅れ破壊が発生した。 Tables 1 and 2 show that the stainless steel produced according to the component range and work hardening rate presented in the present invention does not cause delayed fracture. On the other hand, two types of comparative examples of stainless steel conventionally used did not satisfy the work hardening rate of 1500 MPa or less under the same conditions, and delayed fracture occurred.
図１は、比較例１によるオーステナイト系ステンレス鋼でシンクボウルを加工した後、エッジ部分を撮影した写真であり、図２は、発明例１によるオーステナイト系ステンレス鋼でシンクボウルを加工した後、エッジ部分を撮影した写真である。図３は、比較例１によるオーステナイト系ステンレス鋼および発明例１によるオーステナイト系ステンレス鋼の真ひずみと加工硬化速度の相関関係を示すグラフである。 FIG. 1 is a photograph of an edge portion taken after processing a sink bowl with austenitic stainless steel according to Comparative Example 1, and FIG. 2 shows an edge after processing a sink bowl with austenitic stainless steel according to Invention Example 1. This is a photograph of the part. FIG. 3 is a graph showing the correlation between true strain and work hardening rate of austenitic stainless steel according to Comparative Example 1 and austenitic stainless steel according to Inventive Example 1.
図１〜図３および表２を参照すると、本発明の実施例による真ひずみおよび加工硬化速度の範囲内で加工後にも遅れ破壊が発生しないが分かった。 Referring to FIGS. 1 to 3 and Table 2, it was found that delayed fracture did not occur even after machining within the range of true strain and work hardening rate according to the examples of the present invention.
以上、本発明の例示的な実施例を説明したが、本発明は、これに限定されず、当該技術分野における通常の知識を有する者であれば、本発明の技術範囲から逸脱しない範囲内で多様に変更実施することが可能である。 The exemplary embodiment of the present invention has been described above. However, the present invention is not limited to this example, and any person having ordinary knowledge in the technical field may depart from the technical scope of the present invention. Various changes can be made.
本発明によるオーステナイト系ステンレス鋼は、キッチン用流し台のシンクボウルなどに適用可能な産業上の利用可能性がある。
The austenitic stainless steel according to the present invention has industrial applicability applicable to a sink bowl of a kitchen sink.
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| KR1020150184668A KR101756701B1 (en) | 2015-12-23 | 2015-12-23 | Austenitic stainless steel with increased workability |
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| PCT/KR2016/015024 WO2017111467A1 (en) | 2015-12-23 | 2016-12-21 | Austenitic stainless steel having improved processability |
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| JP2022014147A (en) * | 2020-07-06 | 2022-01-19 | 日鉄ステンレス株式会社 | Non-magnetic stainless steel plate and method for manufacturing steel material for mechanical component |
| JP2024522170A (en) * | 2021-06-21 | 2024-06-11 | ポスコ カンパニー リミテッド | Austenitic stainless steel and its manufacturing method |
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| KR102268906B1 (en) * | 2019-07-17 | 2021-06-25 | 주식회사 포스코 | Austenitic stainless steel with imporoved strength and method for manufacturing the same |
| CN118460926B (en) * | 2024-05-21 | 2025-11-21 | 山西太钢不锈钢股份有限公司 | Easy-to-process high-hardening austenitic stainless steel and manufacturing method thereof |
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