JP7479166B2 - High strength duplex stainless steel and its manufacturing method - Google Patents
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- 229910001039 duplex stainless steel Inorganic materials 0.000 title claims description 41
- 238000004519 manufacturing process Methods 0.000 title claims description 12
- 229910000734 martensite Inorganic materials 0.000 claims description 33
- 238000000034 method Methods 0.000 claims description 12
- 229910000859 α-Fe Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 63
- 239000010935 stainless steel Substances 0.000 description 57
- 229910000831 Steel Inorganic materials 0.000 description 12
- 239000010959 steel Substances 0.000 description 12
- 238000011835 investigation Methods 0.000 description 10
- 239000000203 mixture Substances 0.000 description 10
- 230000007423 decrease Effects 0.000 description 9
- 239000000126 substance Substances 0.000 description 8
- 238000005260 corrosion Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 239000010949 copper Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 238000004881 precipitation hardening Methods 0.000 description 4
- 238000007670 refining Methods 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000007545 Vickers hardness test Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 239000004840 adhesive resin Substances 0.000 description 1
- 229920006223 adhesive resin Polymers 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000011889 copper foil Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
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Description
本発明は、高強度複相ステンレス鋼およびその製造方法に関する。 The present invention relates to high-strength duplex stainless steel and its manufacturing method.
近年、多層プリント配線基板等の製造に必要となる高強度の鋼板材料として、高強度のステンレス鋼が用いられる場合がある。プレスプレートとは、銅箔、接着用樹脂および基板等を積層した多層積層体を熱プレス成形する場合に、熱プレス装置と多層積層体との間および多層積層体の各層同士の間に挟まれて配置される、厚さ数ｍｍ程度の平板状治具である。プレスプレートの材料となる鋼板は、その用途特性から一般的には、ビッカース硬さがおよそ３９０ＨＶ以上となるような高い強度が求められている。 In recent years, high-strength stainless steel is sometimes used as the high-strength steel plate material required for the manufacture of multilayer printed wiring boards and the like. A press plate is a flat jig with a thickness of about several mm that is sandwiched between the heat press device and the multilayer laminate and between each layer of the multilayer laminate when heat-pressing a multilayer laminate made of copper foil, adhesive resin, substrates, etc. Due to its application characteristics, the steel plate used as the material for the press plate is generally required to have high strength, such as a Vickers hardness of approximately 390 HV or more.
そのため、従来は析出硬化系ステンレス鋼であるＳＵＳ６３０および複相組織からなる高強度複相ステンレス鋼等が、プレスプレート等の高い強度の鋼板が求められる場合に用いられてきた。例えば特許文献１～３では、フェライト＋マルテンサイトの複相組織からなる高強度複相ステンレス鋼が提案されている。 For this reason, precipitation hardening stainless steel SUS630 and high-strength duplex stainless steels made of a duplex structure have traditionally been used when high-strength steel plates such as press plates are required. For example, Patent Documents 1 to 3 propose high-strength duplex stainless steels made of a duplex structure of ferrite + martensite.
しかしながら、プレスプレート用の高強度ステンレス鋼として用いられているＳＵＳ６３０はＮｉを相当量含有しており、製造コストが高いという問題がある。さらに、ＳＵＳ６３０は固溶化熱処理後に、強度を高めるために析出硬化熱処理を施す必要がある。この析出硬化熱処理は、例えば加工業者において鋼板材料が製品形状に成型加工された後に施されるため、加工業者での負担が増加し、最終製品の価格が高くなってしまう。 However, SUS630, which is used as a high-strength stainless steel for press plates, contains a significant amount of Ni, which poses the problem of high manufacturing costs. Furthermore, after solution heat treatment, SUS630 needs to be subjected to precipitation hardening heat treatment to increase its strength. This precipitation hardening heat treatment is performed, for example, after the steel plate material has been formed into the product shape by a processor, which increases the burden on the processor and raises the price of the final product.
一方、高強度複相ステンレス鋼は析出硬化熱処理を必要とせず、ＳＵＳ６３０よりも価格が安くなる。さらに高強度複相ステンレス鋼は、強度および延性のバランスが良好であり、高強度の鋼板材料として十分な特性を有している。しかしながら、特許文献１～３で提案されている高強度複相ステンレス鋼の成分系によっては、ビッカース硬さが３９０ＨＶに達するステンレス鋼板を安定して得ることが困難な場合がある。 On the other hand, high-strength duplex stainless steel does not require precipitation hardening heat treatment and is less expensive than SUS630. Furthermore, high-strength duplex stainless steel has a good balance of strength and ductility and has sufficient properties as a high-strength steel plate material. However, depending on the composition system of the high-strength duplex stainless steel proposed in Patent Documents 1 to 3, it may be difficult to consistently obtain stainless steel plate with a Vickers hardness of 390 HV.
本発明の一態様は、安価かつ安定的に３９０ＨＶ以上のビッカース硬さを有する高強度複相ステンレス鋼を提供することを目的とする。 One aspect of the present invention aims to provide a high-strength duplex stainless steel that has a Vickers hardness of 390 HV or more at low cost and in a stable manner.
前記の課題を解決するために、本発明の一態様に係る高強度複相ステンレス鋼は、Ｃ：０．０９質量％以上０．１５質量％以下およびＮｉ：１．５質量％以上３．０質量％以下を含み、下記（１）式で表されるγｍａｘの値が８５．０以上９８．０以下であり、前記γｍａｘの値が８５．０以上９１．０未満の場合には、Ｃｒ：１５．０質量％以上１６．５質量％以下をさらに含み、前記γｍａｘの値が９１．０以上９８．０以下の場合には、Ｃｒ：１５．０質量％以上１８．０質量％以下をさらに含む。 In order to solve the above problems, a high-strength duplex stainless steel according to one embodiment of the present invention contains C: 0.09% by mass to 0.15% by mass and Ni: 1.5% by mass to 3.0% by mass, and further contains Cr: 15.0% by mass to 16.5% by mass when the value of γmax represented by the following formula (1) is 85.0 to 98.0 and the value of γmax is 85.0 to less than 91.0, and further contains Cr: 15.0% by mass to 18.0% by mass when the value of γmax is 91.0 to 98.0.
γｍａｘ＝４２０Ｃ－１１．５Ｓｉ＋７Ｍｎ＋２３Ｎｉ－１１．５Ｃｒ＋９Ｃｕ－５２Ａｌ＋４７０Ｎ＋１８９ （１）
ここで、前記（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が代入される。
γmax=420C-11.5Si+7Mn+23Ni-11.5Cr+9Cu-52Al+470N+189 (1)
Here, the content of the element expressed in mass % is substituted for the element symbol in the formula (1), and 0 is substituted for elements that are not added.
本発明の一態様に係る高強度複相ステンレス鋼は、８５体積％以上９８体積％以下のマルテンサイト相を含み、残部にフェライト相を含む複相組織を有していてもよい。 The high-strength duplex stainless steel according to one embodiment of the present invention may have a duplex structure containing 85% to 98% by volume of martensite phase, with the remainder being ferrite phase.
本発明の一態様に係る高強度複相ステンレス鋼は、Ｓｉ：１．０質量％以下、Ｍｎ：１．０質量％以下、Ｃｕ：１．０質量％以下、Ａｌ：０．５質量％以下およびＮ：０．０３質量％以下の少なくとも何れか１つの条件を満たしていてもよい。 The high-strength duplex stainless steel according to one embodiment of the present invention may satisfy at least one of the following conditions: Si: 1.0 mass% or less, Mn: 1.0 mass% or less, Cu: 1.0 mass% or less, Al: 0.5 mass% or less, and N: 0.03 mass% or less.
本発明の一態様に係る高強度複相ステンレス鋼は、Ｂ：０．０１質量％以下およびＶ：０．２質量％以下の少なくとも何れか１つの条件を満たしていてもよい。 The high-strength duplex stainless steel according to one embodiment of the present invention may satisfy at least one of the following conditions: B: 0.01 mass% or less and V: 0.2 mass% or less.
本発明の一態様に係る高強度複相ステンレス鋼の製造方法は、Ｃ：０．０９質量％以上０．１５質量％以下およびＮｉ：１．５質量％以上３．０質量％以下を含み、Ｃｒ：１５．０質量％以上１６．５質量％未満の場合には、下記（１）式で表されるγｍａｘの値が８５．０以上９８．０以下となるように、Ｃｒ：１６．５質量％以上１８．０質量％以下の場合には、前記γｍａｘの値が９１．０以上９８．０以下となるように、前記高強度複相ステンレス鋼に含まれる各成分元素の添加量を調整する工程を含む。 The method for producing a high-strength duplex stainless steel according to one embodiment of the present invention includes a step of adjusting the amount of each component element added to the high-strength duplex stainless steel, so that when the content of Cr is 15.0 mass% or more and less than 16.5 mass%, the value of γmax represented by the following formula (1) is 85.0 or more and 98.0 or less, and when the content of Cr is 16.5 mass% or more and 18.0 mass% or less, the value of γmax is 91.0 or more and 98.0 or less.
γｍａｘ＝４２０Ｃ－１１．５Ｓｉ＋７Ｍｎ＋２３Ｎｉ－１１．５Ｃｒ＋９Ｃｕ－５２Ａｌ＋４７０Ｎ＋１８９ （１）
ここで、前記（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が代入される。
γmax=420C-11.5Si+7Mn+23Ni-11.5Cr+9Cu-52Al+470N+189 (1)
Here, the content of the element expressed in mass % is substituted for the element symbol in the formula (1), and 0 is substituted for elements that are not added.
本発明の一態様によれば、安価かつ安定的に３９０ＨＶ以上のビッカース硬さを有する高強度複相ステンレス鋼を提供することができる。 According to one aspect of the present invention, it is possible to provide a high-strength duplex stainless steel having a Vickers hardness of 390 HV or more at low cost and in a stable manner.
以下、本発明の一実施形態について、図面を参照して詳細に説明する。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。 One embodiment of the present invention will be described in detail below with reference to the drawings. Note that the following description is provided to facilitate a better understanding of the gist of the invention, and does not limit the present invention unless otherwise specified. In addition, unless otherwise specified in this specification, "A to B" representing a numerical range means "greater than or equal to A and less than or equal to B."
〔化学組成〕
以下、本実施形態に係る高強度複相ステンレス鋼等のステンレス鋼について、化学組成に関する「％」は特に断らない限り「質量％」を意味する。
[Chemical composition]
Hereinafter, for stainless steels such as the high-strength duplex stainless steel according to this embodiment, "%" regarding the chemical composition means "mass %" unless otherwise specified.
Ｃは、オーステナイト相を生成しやすくする、オーステナイト生成元素である。Ｃはオーステナイト組織を安定化させると共に、焼鈍および／または冷却過程で生成するマルテンサイトの強度を向上させる。Ｃ含有量が高くなると、Ｃがマルテンサイト相の体積率を増加させ、Ｃがマルテンサイト中に固溶するため、ステンレス鋼の強度が向上する。そのため、Ｃはステンレス鋼の強度を確保するうえで重要な元素である。ただし、ステンレス鋼のＣ含有量が高くなりすぎると、マルテンサイト相のみからなるステンレス鋼になってしまい、複相組織が得られない。また、Ｃ含有量が高くなりすぎると、靭性および耐食性を低下させ、加工性が低下する。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼は０.０９～０．１５％のＣ含有量を有する。 C is an austenite-forming element that facilitates the formation of the austenite phase. C stabilizes the austenite structure and improves the strength of the martensite formed during the annealing and/or cooling process. When the C content is high, C increases the volume fraction of the martensite phase and dissolves in the martensite, improving the strength of the stainless steel. Therefore, C is an important element in ensuring the strength of stainless steel. However, if the C content of stainless steel is too high, it becomes stainless steel consisting only of the martensite phase, and a multi-phase structure cannot be obtained. In addition, if the C content is too high, toughness and corrosion resistance are reduced, and workability is reduced. Therefore, as a result of the investigation, the high-strength multi-phase stainless steel according to this embodiment has a C content of 0.09 to 0.15%.
Ｎｉは、オーステナイト生成元素であり、マルテンサイト相を生成させるのに必要な元素である。さらに、ステンレス鋼の靱性および耐食性の向上にも有効である。しかし、Ｎｉ含有量が高くなりすぎると、マルテンサイト相のみからなるステンレス鋼になってしまい、複相組織が得られない。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼は１．５～３．０％のＮｉ含有量を有する。 Ni is an austenite-forming element and is necessary for forming the martensite phase. It is also effective in improving the toughness and corrosion resistance of stainless steel. However, if the Ni content is too high, the stainless steel will consist only of the martensite phase, and a multi-phase structure will not be obtained. Therefore, as a result of investigation, the high-strength multi-phase stainless steel according to this embodiment has a Ni content of 1.5 to 3.0%.
Ｃｒは、ステンレス鋼の耐食性を高めるのに有効な成分である。しかし、Ｃｒはフェライト相を生成しやすくする、フェライト生成元素であるため、ステンレス鋼のＣｒ含有量が高くなりすぎると、マルテンサイト相の体積率を低下させる。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼は１５．０～１８.０％のＣｒ含有量を有する。なお、適切なＣｒ含有量は後述するγｍａｘの値によっても異なる。γｍａｘの値とＣｒ含有量との関係については後述する。 Cr is an effective component for improving the corrosion resistance of stainless steel. However, since Cr is a ferrite-forming element that makes it easier to form the ferrite phase, if the Cr content of stainless steel becomes too high, it will reduce the volume fraction of the martensite phase. As a result of our investigation, we have determined that the high-strength duplex stainless steel according to this embodiment has a Cr content of 15.0 to 18.0%. The appropriate Cr content also depends on the value of γmax, which will be described later. The relationship between the value of γmax and the Cr content will be described later.
Ｓｉは、ステンレス鋼の脱酸作用を有する元素であるが、ステンレス鋼はＳｉを多量に含有すると加工性および靱性が低下する。一方、過度の低Ｓｉ化は精錬コストの増大に繋がる。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では１.０％以下のＳｉ含有量が望ましい。 Si is an element that has a deoxidizing effect on stainless steel, but if stainless steel contains a large amount of Si, its workability and toughness decrease. On the other hand, excessively low Si content leads to increased refining costs. Therefore, as a result of investigation, it is desirable for the high-strength duplex stainless steel according to this embodiment to have a Si content of 1.0% or less.
Ｍｎは、オーステナイト生成元素であり、ステンレス鋼の溶製時に脱酸作用を有する。しかし、多量のＭｎ含有はステンレス鋼の加工性および耐食性の低下を招く。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では１.０％以下のＭｎ含有量が望ましい。 Mn is an austenite-forming element and has a deoxidizing effect when stainless steel is melted. However, the inclusion of a large amount of Mn leads to a decrease in the workability and corrosion resistance of stainless steel. Therefore, as a result of investigation, it is desirable for the high-strength duplex stainless steel according to this embodiment to have a Mn content of 1.0% or less.
Ｃｕは、オーステナイト生成元素であり、ステンレス鋼のマルテンサイト相の体積率増加に寄与する元素である。ただし、過剰のＣｕ含有は耐食性および熱間加工性の低下を招く。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では０．５％以下のＣｕ含有量が望ましい。 Cu is an austenite-forming element and contributes to increasing the volume fraction of the martensite phase in stainless steel. However, excessive Cu content leads to a decrease in corrosion resistance and hot workability. Therefore, as a result of investigation, it is desirable for the high-strength duplex stainless steel according to this embodiment to have a Cu content of 0.5% or less.
Ａｌは、ステンレス鋼溶製時の脱酸に有効な元素である。また、ＡｌはＮを固定する作用を有しており、高純度化にも寄与し、加工性を向上させる。ただし、Ａｌは強力なフェライト生成元素であり、過剰の添加は高温でのオーステナイト生成量を必要以上に低下させ、マルテンサイト相の体積率を低下させる要因となる。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では０.５％以下のＡｌ含有量が望ましい。 Al is an element that is effective in deoxidizing stainless steel during its production. In addition, Al has the effect of fixing N, which contributes to high purification and improves workability. However, Al is a strong ferrite-forming element, and excessive addition reduces the amount of austenite formed at high temperatures more than necessary, which causes a decrease in the volume fraction of the martensite phase. Therefore, as a result of investigation, an Al content of 0.5% or less is desirable for the high-strength duplex stainless steel according to this embodiment.
Ｎは、マルテンサイト相の体積率を増加させて、ステンレス鋼の強度向上に寄与する元素である。またＮは、マルテンサイト中に固溶することによっても、ステンレス鋼の強度を向上させる。ただし、Ｎ含有量が多くなると耐食性および靱性が低下しやすい。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では０.０３％以下のＮ含有量が望ましい。 N is an element that increases the volume fraction of the martensite phase and contributes to improving the strength of stainless steel. N also improves the strength of stainless steel by dissolving in martensite. However, if the N content is high, corrosion resistance and toughness tend to decrease. Therefore, as a result of investigation, it is desirable for the high-strength duplex stainless steel according to this embodiment to have an N content of 0.03% or less.
Ｂは、熱間加工性の向上に寄与する元素である。ただし、過剰のＢ含有はステンレス鋼の靭性の低下を招く。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では０．０１％以下のＢ含有量が望ましい。 B is an element that contributes to improving hot workability. However, excessive B content leads to a decrease in the toughness of the stainless steel. Therefore, as a result of investigation, it is desirable for the high-strength duplex stainless steel according to this embodiment to have a B content of 0.01% or less.
Ｖは、脱酸作用を有する元素であるが、多量に含有するとステンレス鋼の耐食性および靱性が低下する。よって、検討の結果、本実施形態に係る高強度複相ステンレス鋼では０．２％以下のＶ含有量が望ましい。 V is an element that has a deoxidizing effect, but if it is contained in large amounts, the corrosion resistance and toughness of stainless steel will decrease. Therefore, as a result of investigation, it is desirable for the V content of the high-strength duplex stainless steel according to this embodiment to be 0.2% or less.
本実施形態に係る高強度複相ステンレス鋼の残部は、Ｆｅおよび不可避的不純物である。不可避的不純物として混入するＰ、Ｓについては、従来の一般的なフェライト系ステンレス鋼と同様、Ｐ：０.０５％以下、Ｓ：０.０３％以下の含有量範囲であれば問題ない。 The remainder of the high-strength duplex stainless steel according to this embodiment is Fe and unavoidable impurities. As for P and S, which are mixed in as unavoidable impurities, there is no problem if the content ranges are P: 0.05% or less and S: 0.03% or less, similar to conventional general ferritic stainless steels.
（γｍａｘの値）
下記（１）式により定まるγｍａｘの値は、本実施形態に係る高強度複相ステンレス鋼の製造過程において、ステンレス鋼を１１００℃で等温保持し平衡状態に至った場合のオーステナイト量（体積％）について、成分組成から推定する指標である。
(value of γmax)
The value of γmax determined by the following formula (1) is an index estimated from the component composition for the amount of austenite (volume %) when the stainless steel is isothermally held at 1100°C and reaches an equilibrium state during the manufacturing process of the high-strength duplex stainless steel according to this embodiment.
γｍａｘ＝４２０Ｃ－１１．５Ｓｉ＋７Ｍｎ＋２３Ｎｉ－１１．５Ｃｒ＋９Ｃｕ－５２Ａｌ＋４７０Ｎ＋１８９ …（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が代入される。
γmax=420C-11.5Si+7Mn+23Ni-11.5Cr+9Cu-52Al+470N+189 ... (1)
Here, the content of the element expressed in mass % is substituted for the element symbol in formula (1), and 0 is substituted for elements that are not added.
オーステナイトは、冷却する過程においてマルテンサイトに変態する。そのため、γｍａｘの値はステンレス鋼におけるマルテンサイト相の生成のしやすさを表す指標でもある。つまりγｍａｘの値は、成分組成からマルテンサイト量を推定する指標となる。γｍａｘの値が１００以上である場合は、そのステンレス鋼の最大マルテンサイト量は１００％であると推定される。 Austenite transforms into martensite during the cooling process. Therefore, the γmax value is also an indicator of the ease with which the martensite phase forms in stainless steel. In other words, the γmax value is an indicator for estimating the amount of martensite from the chemical composition. If the γmax value is 100 or more, the maximum amount of martensite in that stainless steel is estimated to be 100%.
本実施形態では、γｍａｘの値が８５．０以上９８．０以下の範囲に入るように、ステンレス鋼における各成分元素の含有量を調整する。さらに、Ｃｒ含有量が１５．０％以上１６．５％未満の場合には、γｍａｘの値が８５．０以上９８．０以下となるように調整し、Ｃｒ含有量が１６．５％以上１８．０％以下の場合には、γｍａｘの値が９１．０以上９８．０以下となるように調整する。 In this embodiment, the content of each component element in the stainless steel is adjusted so that the value of γmax is in the range of 85.0 to 98.0. Furthermore, when the Cr content is 15.0% or more and less than 16.5%, the value of γmax is adjusted to be 85.0 to 98.0, and when the Cr content is 16.5% or more and 18.0% or less, the value of γmax is adjusted to be 91.0 to 98.0.
これまでステンレス鋼の強度は、Ｃ含有量およびマルテンサイト量（γｍａｘ）を調整することによって安定して得られると考えられてきた。しかし、実際にはＣ含有量およびマルテンサイト量を調整しても、ビッカース硬さが３９０ＨＶ以上とならないステンレス鋼もあった。 Until now, it has been thought that the strength of stainless steel can be stably achieved by adjusting the C content and the amount of martensite (γmax). However, in reality, even when the C content and the amount of martensite were adjusted, there were some stainless steels whose Vickers hardness did not reach 390 HV or more.
しかしながら、発明者らの研究によれば、Ｃｒ含有量がステンレス鋼の強度に大きく影響していることが分かった。本発明は特定の理論に制限されるものではないが、ステンレス鋼におけるＣｒ含有量が多い場合、Ｃｒ炭化物が生成されやすくなる。そのため、マルテンサイト中に固溶化するＣの量が減少し、ステンレス鋼の強度も減少すると発明者らは考えている。以上の知見から、発明者らは、γｍａｘとＣｒ含有量を調整することで、ビッカース硬さが安定して３９０ＨＶ以上となる高強度のステンレス鋼が得られることを見出した。ビッカース硬さは、ＪＩＳ Ｚ２２４４準拠のビッカース硬さ試験方法に基づいて測定できる。 However, according to the inventors' research, it has been found that the Cr content has a large effect on the strength of stainless steel. Although the present invention is not limited to a specific theory, when the Cr content in stainless steel is high, Cr carbides are more likely to be formed. As a result, the amount of C that dissolves in martensite decreases, and the strength of the stainless steel also decreases, the inventors believe. From the above findings, the inventors have found that by adjusting γmax and the Cr content, it is possible to obtain a high-strength stainless steel with a stable Vickers hardness of 390 HV or more. Vickers hardness can be measured based on the Vickers hardness test method in accordance with JIS Z2244.
また、フェライトとマルテンサイトとの複相組織であることで、高強度、プレス成型性、加工性および延性に優れた高強度複相ステンレス鋼となる。そのため、本実施形態では、前記のγｍａｘの値とも関連するが、８５体積％以上９８体積％以下のマルテンサイト相を含み、残部にフェライト相を含む複相組織を有している。マルテンサイト相の体積率については、ＪＩＳ Ｇ０５５５準拠の点算法によって求めることができる。 In addition, the multiphase structure of ferrite and martensite results in a high-strength multiphase stainless steel with excellent strength, press formability, workability, and ductility. Therefore, in this embodiment, which is also related to the above-mentioned value of γmax, the multiphase structure contains 85 volume % to 98 volume % of martensite phase, with the remainder containing ferrite phase. The volume fraction of the martensite phase can be determined by the point calculation method in accordance with JIS G0555.
以上をまとめると、本実施形態に係る高強度複相ステンレス鋼は、Ｃ：０．０９質量％以上０．１５質量％以下およびＮｉ：１．５質量％以上３．０質量％以下を含み、γｍａｘの値が８５．０以上９８．０以下である。そして、γｍａｘの値が８５．０以上９１．０未満の場合には、Ｃｒ：１５．０質量％以上１６．５質量％以下をさらに含み、γｍａｘの値が９１．０以上９８．０以下の場合には、Ｃｒ：１５．０質量％以上１８．０質量％以下をさらに含む。 In summary, the high-strength duplex stainless steel according to this embodiment contains C: 0.09% by mass to 0.15% by mass, Ni: 1.5% by mass to 3.0% by mass, and a γmax value of 85.0 to 98.0. When the γmax value is 85.0 to less than 91.0, it further contains Cr: 15.0% by mass to 16.5% by mass, and when the γmax value is 91.0 to 98.0, it further contains Cr: 15.0% by mass to 18.0% by mass.
また本実施形態に係る高強度複相ステンレス鋼は、８５体積％以上９８体積％以下のマルテンサイト相を含み、残部にフェライト相を含む複相組織を有することが好ましい。 In addition, the high-strength duplex stainless steel according to this embodiment preferably has a duplex structure containing 85% to 98% by volume of martensite phase, with the remainder being ferrite phase.
さらに、本実施形態に係る高強度複相ステンレス鋼は、Ｓｉ：１．０質量％以下、Ｍｎ：１．０質量％以下、Ｃｕ：１．０質量％以下、Ａｌ：０．５質量％以下およびＮ：０．０３質量％以下の少なくとも何れか１つの条件を満たすことが好ましい。 Furthermore, it is preferable that the high-strength duplex stainless steel according to this embodiment satisfies at least one of the following conditions: Si: 1.0 mass% or less, Mn: 1.0 mass% or less, Cu: 1.0 mass% or less, Al: 0.5 mass% or less, and N: 0.03 mass% or less.
また本実施形態に係る高強度複相ステンレス鋼は、Ｂ：０．０１質量％以下およびＶ：０．２質量％以下の少なくとも何れか１つの条件を満たすことがさらに好ましい。 Furthermore, it is further preferable that the high-strength duplex stainless steel according to this embodiment satisfies at least one of the conditions of B: 0.01 mass% or less and V: 0.2 mass% or less.
〔製造方法〕
本実施形態に係る高強度複相ステンレス鋼は、一般的なステンレス鋼の製造工程に、Ｃｒの含有量に基づいてγｍａｘの値が所定の範囲内となるように、各成分元素の添加量を調整する工程を含んでいる。一般的なステンレス鋼の製造工程とは、例えば、溶解、鋳造、熱間圧延、冷間圧延、焼鈍および酸洗等を含む工程であってよい。
〔Production method〕
The high-strength duplex stainless steel according to the present embodiment includes a process for adjusting the amount of each component element added so that the value of γmax falls within a predetermined range based on the Cr content in addition to the general stainless steel manufacturing process. The general stainless steel manufacturing process may include, for example, melting, casting, hot rolling, cold rolling, annealing, pickling, etc.
γｍａｘの値を調整する工程は、例えば溶解工程における二次精錬で行われる。γｍａｘの値の調整は、Ｃ、Ｓｉ、Ｍｎ、Ｎｉ、Ａｌ、Ｎの各成分元素の添加量を調整することで行われる。この二次精錬において、Ｃｒ含有量に基づいてγｍａｘの値を調整することが好ましい。Ｃｒ含有量が１５．０質量％以上１６．５質量％未満の場合には、γｍａｘの値が８５．０以上９８．０以下となるように、またＣｒ含有量が１６．５質量％以上１８．０質量％以下の場合には、γｍａｘの値が９１．０以上９８．０以下となるように、高強度複相ステンレス鋼に添加する各成分元素の添加量を調整する。 The process of adjusting the value of γmax is carried out, for example, in the secondary refining in the melting process. The adjustment of the value of γmax is carried out by adjusting the amount of each of the component elements C, Si, Mn, Ni, Al, and N added. In this secondary refining, it is preferable to adjust the value of γmax based on the Cr content. When the Cr content is 15.0 mass% or more and less than 16.5 mass%, the amount of each component element added to the high-strength duplex stainless steel is adjusted so that the value of γmax is 85.0 or more and 98.0 or less, and when the Cr content is 16.5 mass% or more and 18.0 mass% or less, the value of γmax is 91.0 or more and 98.0 or less.
二次精錬にて精錬された溶鋼は連続鋳造設備に送られ、溶鋼が所望の大きさの鋼片に成形される。得られた鋼片は、熱間圧延工程、冷間圧延工程、焼鈍、および酸洗等の工程を経て鋼材製品となる。 The molten steel refined in the secondary refining process is sent to a continuous casting facility, where the molten steel is formed into steel billets of the desired size. The resulting steel billets undergo processes such as hot rolling, cold rolling, annealing, and pickling to become steel products.
熱間圧延工程は、例えば粗圧延機および仕上圧延機等を用いて行うことができる。なお、本実施形態において、圧延されたステンレス鋼帯の端が割れてしまうのを防ぐ観点から、仕上圧延機はステッケル熱延機を用いるのが好ましい。 The hot rolling process can be carried out, for example, using a roughing mill and a finishing mill. In this embodiment, it is preferable to use a Steckel hot rolling mill as the finishing mill in order to prevent the ends of the rolled stainless steel strip from cracking.
また、本実施形態に係る高強度複相ステンレス鋼を得るためには、加熱して複相化処理を行い、その後冷間圧延工程を行うことで安定して強度を確保する。この冷間圧延工程の圧延率を調整し、３９０ＨＶ以上のビッカース硬さの高強度複相ステンレス鋼を製造する。 To obtain the high-strength duplex stainless steel according to this embodiment, the material is heated to undergo a duplex treatment, and then a cold rolling process is carried out to ensure stable strength. The reduction ratio in this cold rolling process is adjusted to produce high-strength duplex stainless steel with a Vickers hardness of 390 HV or more.
例えば、高強度複相ステンレス鋼をプレスプレートとして用いる場合、ビッカース硬さは３９０ＨＶ以上となるのが望ましい。一般にプレスプレートは、その消耗を低減するため高強度が求められる、実用上はビッカース硬さが３９０ＨＶ以上であることが好ましい。本実施形態に係る高強度複相ステンレス鋼は３９０ＨＶ以上のビッカース硬さを備えることから、プレスプレートとして好適に用いることができる。 For example, when using high-strength duplex stainless steel as a press plate, it is desirable for the Vickers hardness to be 390 HV or more. Generally, press plates are required to have high strength to reduce wear, and in practice, a Vickers hardness of 390 HV or more is preferable. The high-strength duplex stainless steel according to this embodiment has a Vickers hardness of 390 HV or more, and therefore can be suitably used as a press plate.
本実施形態に係る高強度複相ステンレス鋼の用途はプレスプレートに限られない。プレスプレート以外にも、スチールベルト、金具、フレーム、または工具等の一般的な高強度部材として用いることができる。 The use of the high-strength duplex stainless steel according to this embodiment is not limited to press plates. In addition to press plates, it can also be used as general high-strength components such as steel belts, metal fittings, frames, or tools.
以下に、本発明の実施例（本発明例）および比較例に係るステンレス鋼板を評価した結果について説明する。 The following describes the results of evaluating stainless steel sheets according to examples of the present invention (invention examples) and comparative examples.
下記表１に示す化学組成を有するステンレス鋼を用いて、厚さ１．７ｍｍ以下のステンレス鋼板を製造した。これにより得られた各ステンレス鋼板のマルテンサイト相の体積率（体積％）およびビッカース硬さ（ＨＶ）を表２に示す。なお、表１において下線が付された項目は、本発明の一実施形態に係る高強度複相ステンレス鋼の化学組成の範囲から外れた項目である。 Stainless steel sheets with a thickness of 1.7 mm or less were manufactured using stainless steel having the chemical composition shown in Table 1 below. The martensite phase volume fraction (volume %) and Vickers hardness (HV) of each stainless steel sheet obtained in this manner are shown in Table 2. Note that the underlined items in Table 1 are items that are outside the range of the chemical composition of the high-strength duplex stainless steel according to one embodiment of the present invention.
（マルテンサイト相の体積率）
各ステンレス鋼板のマルテンサイト相の体積率を測定した。各ステンレス鋼板を光学顕微鏡によって観察を行い、点算法（ＪＩＳ Ｇ０５５５）によってマルテンサイト相の体積率を求めた。評価結果について表２の「マルテンサイト量（体積％）」に示した。
(Volume fraction of martensite phase)
The volume fraction of the martensite phase of each stainless steel sheet was measured. Each stainless steel sheet was observed with an optical microscope, and the volume fraction of the martensite phase was calculated by the point counting method (JIS G0555). The evaluation results are shown in Table 2 under "Martensite content (volume %)."
（ビッカース硬さ）
各ステンレス鋼板のビッカース硬さを測定した。各ステンレス鋼板をビッカース硬さ試験機によって、ビッカース硬さ試験（ＪＩＳ Ｚ２２４４）を行い、ビッカース硬さを測定した。評価結果について表２の「硬さ（ＨＶ）」に示した。
(Vickers hardness)
The Vickers hardness of each stainless steel plate was measured. Each stainless steel plate was subjected to a Vickers hardness test (JIS Z2244) using a Vickers hardness tester to measure the Vickers hardness. The evaluation results are shown in Table 2 under "Hardness (HV)".
（評価結果）
表２に示すように、ステンレス鋼板の化学組成について、いずれか一つでも本発明の一実施形態に係る範囲から外れた場合、当該ステンレス鋼板はビッカース硬さが３９０ＨＶ以下となった（鋼Ｎｏ．８～１７を参照）。一方、本発明の一実施形態に係る化学組成を満たすステンレス鋼板は、いずれもビッカース硬さが３９０ＨＶ以上となった（鋼Ｎｏ．１～７を参照）。
(Evaluation results)
As shown in Table 2, when any one of the chemical compositions of the stainless steel sheets was out of the range according to one embodiment of the present invention, the Vickers hardness of the stainless steel sheets was 390 HV or less (see Steel Nos. 8 to 17). On the other hand, all of the stainless steel sheets that satisfied the chemical composition according to one embodiment of the present invention had a Vickers hardness of 390 HV or more (see Steel Nos. 1 to 7).
さらに、マルテンサイト相の体積率はγｍａｘの値と相関があることが示された。よって、ビッカース硬さが３９０ＨＶ以上となる高強度複相ステンレス鋼から得られたステンレス鋼板のマルテンサイト相の体積率はいずれも、８５体積％以上９８体積％以下となることが示された（鋼Ｎｏ．１～７を参照）。 Furthermore, it was shown that the volume fraction of the martensite phase correlates with the value of γmax. Therefore, it was shown that the volume fraction of the martensite phase in stainless steel sheets obtained from high-strength duplex stainless steels with a Vickers hardness of 390 HV or more is 85 volume % or more and 98 volume % or less (see Steels No. 1 to 7).
図１は、本発明例および比較例に係るステンレス鋼板のＣｒ含有量とγｍａｘとの値の関係を示す図である。図１のグラフ中における黒点が本発明例、白点が比較例のＣｒ含有量とγｍａｘの値との関係を、それぞれ示している。図１で示すように、一点鎖線で囲まれた領域に含まれるようなＣｒ含有量およびγｍａｘの値を持つステンレス鋼板は、いずれも３９０ＨＶ以上のビッカース硬さを持つことが示された。これにより、ステンレス鋼板の強度にはＣｒ含有量が密接に関係しており、Ｃｒ含有量によってγｍａｘの値を調整することで、３９０ＨＶ以上のビッカース硬さを有するステンレス鋼板を安定して得られることが示された。 Figure 1 shows the relationship between the Cr content and the γmax value of stainless steel sheets according to the present invention and the comparative example. The black dots in the graph of Figure 1 show the relationship between the Cr content and the γmax value of the present invention examples, and the white dots show the relationship between the Cr content and the γmax value of the comparative example. As shown in Figure 1, all stainless steel sheets having a Cr content and a γmax value included in the area surrounded by the dashed dotted line have a Vickers hardness of 390 HV or more. This shows that the strength of stainless steel sheets is closely related to the Cr content, and that by adjusting the γmax value according to the Cr content, stainless steel sheets having a Vickers hardness of 390 HV or more can be stably obtained.
さらに、γｍａｘの値が８５．０～９１．０の場合、Ｃｒ含有量が多すぎると、３９０ＨＶ以上のビッカース硬さが得られないことが示された。比較例である鋼Ｎｏ．１４～１６のステンレス鋼板は、γｍａｘの値が８５．０～９１．０であり、Ｃｒ含有量以外の化学組成は本発明の一実施形態に係る範囲から外れていない。しかし、これらのステンレス鋼板のビッカース硬さは３９０ＨＶ以下となっており、Ｃｒ含有量がステンレス鋼板のビッカース硬さに関係していることが示された。 Furthermore, it was shown that when the γmax value is 85.0 to 91.0, if the Cr content is too high, a Vickers hardness of 390 HV or more cannot be obtained. The stainless steel sheets of Steel Nos. 14 to 16, which are comparative examples, have γmax values of 85.0 to 91.0, and the chemical composition other than the Cr content does not deviate from the range according to one embodiment of the present invention. However, the Vickers hardness of these stainless steel sheets is 390 HV or less, indicating that the Cr content is related to the Vickers hardness of the stainless steel sheet.
以上より、Ｃｒ含有量によってγｍａｘの値を調整することで、ビッカース硬さが３９０ＨＶ以上の高強度複相ステンレス鋼板を安定して得られることが示された。 The above shows that by adjusting the γmax value through the Cr content, it is possible to stably obtain high-strength duplex stainless steel sheets with a Vickers hardness of 390 HV or more.
〔付記事項〕
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。
[Additional Notes]
The present invention is not limited to the above-described embodiments, and various modifications are possible within the scope of the claims. Embodiments obtained by appropriately combining the technical means disclosed in different embodiments are also included in the technical scope of the present invention.
Claims (2)
下記（１）式で表されるγｍａｘの値が８５．０以上９８．０以下であり、
前記γｍａｘの値が８５．０以上９１．０未満の場合には、Ｃｒ：１５．０質量％以上１６．５質量％以下をさらに含み、
前記γｍａｘの値が９１．０以上９８．０以下の場合には、Ｃｒ：１５．０質量％以上１８．０質量％以下をさらに含み、
８５体積％以上９８体積％以下のマルテンサイト相を含み、残部にフェライト相を含む複相組織を有する、高強度複相ステンレス鋼；
γｍａｘ＝４２０Ｃ－１１．５Ｓｉ＋７Ｍｎ＋２３Ｎｉ－１１．５Ｃｒ＋９Ｃｕ－５２Ａｌ＋４７０Ｎ＋１８９ （１）
ここで、前記（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が代入される。 C: 0.09% by mass or more and 0.15% by mass or less , Ni: 1.5% by mass or more and 3.0 % by mass or less, Si: 1.0% by mass or less, Mn: 1.0% by mass or less, Cu: 1.0% by mass or less, Al: 0.5% by mass or less, N: 0.03% by mass or less, P: 0.05% by mass or less, and S: 0.03% by mass or less , with the remainder being Fe and unavoidable impurities,
The value of γmax represented by the following formula (1) is 85.0 or more and 98.0 or less,
When the value of γmax is 85.0 or more and less than 91.0, Cr: 15.0 mass% or more and 16.5 mass% or less is further included,
When the value of γmax is 91.0 or more and 98.0 or less, Cr: 15.0 mass% or more and 18.0 mass% or less is further included,
A high-strength duplex stainless steel having a duplex structure containing 85 volume % or more and 98 volume % or less of a martensite phase, with the remainder being a ferrite phase ;
γmax=420C-11.5Si+7Mn+23Ni-11.5Cr+9Cu-52Al+470N+189 (1)
Here, the content of the element expressed in mass % is substituted for the element symbol in the formula (1), and 0 is substituted for elements that are not added.
Ｃｒ：１５．０質量％以上１６．５質量％未満の場合には、下記（１）式で表されるγｍａｘの値が８５．０以上９８．０以下となるように、Ｃｒ：１６．５質量％以上１８．０質量％以下の場合には、前記γｍａｘの値が９１．０以上９８．０以下となるように、前記高強度複相ステンレス鋼に含まれる各成分元素の添加量を調整する工程を含む、高強度複相ステンレス鋼の製造方法；
γｍａｘ＝４２０Ｃ－１１．５Ｓｉ＋７Ｍｎ＋２３Ｎｉ－１１．５Ｃｒ＋９Ｃｕ－５２Ａｌ＋４７０Ｎ＋１８９ （１）
ここで、前記（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が代入される。 1. A method for producing a high-strength duplex stainless steel having a duplex structure containing 85% by volume to 98% by volume of martensite phase and the remainder being a ferrite phase, the method comprising the steps of: C: 0.09% by mass or more and 0.15% by mass or less; Ni: 1.5% by mass or more and 3.0% by mass or less; Si: 1.0% by mass or less; Mn: 1.0% by mass or less; Cu: 1.0% by mass or less; Al: 0.5% by mass or less; N: 0.03% by mass or less; P: 0.05% by mass or less; S: 0.03% by mass or less; and Cr, the balance being Fe and unavoidable impurities, the method comprising the steps of:
a method for producing a high-strength duplex stainless steel, comprising a step of adjusting the amount of each component element contained in the high-strength duplex stainless steel so that the value of γmax represented by the following formula (1) is 85.0 to 98.0 when Cr is 15.0 mass% or more and less than 16.5 mass%, and so that the value of γmax is 91.0 to 98.0 when Cr is 16.5 mass% or more and 18.0 mass% or less;
γmax=420C-11.5Si+7Mn+23Ni-11.5Cr+9Cu-52Al+470N+189 (1)
Here, the content of the element expressed in mass % is substituted for the element symbol in the formula (1), and 0 is substituted for elements that are not added.
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| JP2001271140A (en) | 2000-01-21 | 2001-10-02 | Nisshin Steel Co Ltd | High strength and high toughness martensitic stainless steel sheet, method for suppressing edge cutting caused by cold rolling and method for producing steel sheet |
| JP2002105601A (en) | 2000-09-27 | 2002-04-10 | Nisshin Steel Co Ltd | High strength dual phase stainless steel and its production method |
| JP2018135571A (en) | 2017-02-22 | 2018-08-30 | 日新製鋼株式会社 | Dual-phase structure stainless steel sheet, member, and method for manufacturing brake disc |
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| JP2001271140A (en) | 2000-01-21 | 2001-10-02 | Nisshin Steel Co Ltd | High strength and high toughness martensitic stainless steel sheet, method for suppressing edge cutting caused by cold rolling and method for producing steel sheet |
| JP2002105601A (en) | 2000-09-27 | 2002-04-10 | Nisshin Steel Co Ltd | High strength dual phase stainless steel and its production method |
| JP2018135571A (en) | 2017-02-22 | 2018-08-30 | 日新製鋼株式会社 | Dual-phase structure stainless steel sheet, member, and method for manufacturing brake disc |
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