JP2007314816A - Thick-sized high strength stainless steel wire and wire rod having excellent ductility and method for producing the steel wire - Google Patents
Thick-sized high strength stainless steel wire and wire rod having excellent ductility and method for producing the steel wire Download PDFInfo
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- JP2007314816A JP2007314816A JP2006142660A JP2006142660A JP2007314816A JP 2007314816 A JP2007314816 A JP 2007314816A JP 2006142660 A JP2006142660 A JP 2006142660A JP 2006142660 A JP2006142660 A JP 2006142660A JP 2007314816 A JP2007314816 A JP 2007314816A
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 35
- 229910000831 Steel Inorganic materials 0.000 title claims description 29
- 239000010959 steel Substances 0.000 title claims description 29
- 238000004519 manufacturing process Methods 0.000 title claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910001566 austenite Inorganic materials 0.000 claims description 17
- 229910000859 α-Fe Inorganic materials 0.000 claims description 15
- 229910000734 martensite Inorganic materials 0.000 claims description 7
- 239000002184 metal Substances 0.000 claims description 7
- 229910052751 metal Inorganic materials 0.000 claims description 7
- 229910052749 magnesium Inorganic materials 0.000 claims description 5
- 229910052715 tantalum Inorganic materials 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- 229910052796 boron Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 238000005491 wire drawing Methods 0.000 description 28
- 230000000052 comparative effect Effects 0.000 description 16
- 239000000047 product Substances 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 208000010392 Bone Fractures Diseases 0.000 description 5
- 206010017076 Fracture Diseases 0.000 description 5
- 239000010935 stainless steel Substances 0.000 description 5
- 208000013201 Stress fracture Diseases 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 229910052721 tungsten Inorganic materials 0.000 description 4
- MUBZPKHOEPUJKR-UHFFFAOYSA-N Oxalic acid Chemical compound OC(=O)C(O)=O MUBZPKHOEPUJKR-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000003483 aging Methods 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000002542 deteriorative effect Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001039 duplex stainless steel Inorganic materials 0.000 description 1
- 238000000866 electrolytic etching Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 235000006408 oxalic acid Nutrition 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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Abstract
Description
本発明は、太径ステンレス鋼線の高強度化に関するものであり、例えば、軽伸線加工により製造される安価な太径の高強度鋼線製品に関するものである。 The present invention relates to increasing the strength of a large-diameter stainless steel wire, for example, an inexpensive large-diameter high-strength steel wire product manufactured by light drawing.
これまで高強度ステンレス鋼線は、オーステナイト系，準安定オーステナイト系ステンレス鋼線や２相系ステンレス鋼線を強伸線加工して得られていた（例えば、特許文献１〜４）。しかしながら、経済性から高強度ステンレス鋼線は、連続伸線機が使用できるφ４．５ｍｍ以下の細径サイズに限られていた。一方、太径ステンレス鋼線で高強度化するには、強伸線加工が必要であり不経済となるばかりか、伸線縦割れが発生し、また、延性が劣化するため、太径ステンレス鋼線では１６００Ｎ／ｍｍ2以下の低強度材に限定されていた。 Hitherto, high-strength stainless steel wires have been obtained by strongly drawing austenitic, metastable austenitic stainless steel wires or duplex stainless steel wires (for example, Patent Documents 1 to 4). However, high-strength stainless steel wires are limited to small diameters of φ4.5 mm or less that can be used by a continuous wire drawing machine because of economy. On the other hand, in order to increase the strength with a large diameter stainless steel wire, not only is the wire drawing work necessary and uneconomical, but also wire drawing vertical cracks occur, and the ductility deteriorates. The wire was limited to a low strength material of 1600 N / mm 2 or less.
一方、太径の高強度鋼線は、炭素鋼のオイルテンパー線が使用されていた。しかしながら、最近、軽量化・高耐久性の観点から太径ステンレス鋼線にも高強度化が求められるようになってきた。 On the other hand, carbon steel oil tempered wires have been used for large diameter high strength steel wires. However, recently, high-strength stainless steel wires have been required to have high strength from the viewpoint of weight reduction and high durability.
このように、これまで太径（線径≧４．５ｍｍ）のステンレス鋼線において、延性に優れて、引張強さを１６００Ｎ／ｍｍ2を超える高強度鋼線は提案されていない。とりわけ、延性については、ばね成形性等を考慮すると引張試験での破断絞り３０％以上が必要である。 Thus, a high-strength steel wire having excellent ductility and a tensile strength exceeding 1600 N / mm 2 has not been proposed so far in a stainless steel wire having a large diameter (wire diameter ≧ 4.5 mm). In particular, with regard to ductility, considering the spring formability and the like, it is necessary to have a fracture drawing of 30% or more in a tensile test.
本発明の目的は、耐久性に優れる太径の高強度製品を安価に得ることを主目的に、延性に優れた太径の高強度ステンレス鋼線を安価に提供することである。 An object of the present invention is to provide a large-diameter high-strength stainless steel wire excellent in ductility at a low cost, mainly for obtaining a large-diameter high-strength product excellent in durability at a low cost.
本発明者らは、上記課題を解決するために種々検討した結果、ＪＩＳに規程される２相系ステンレス鋼よりも低Ｃｒ，低Ｎｉ化して溶体化処理ままで組織バランスをオーステナイト相とフェライト相に調整し、更に、軽伸線加工（伸線減面率；２０〜５０％）により加工誘起マルテンサイトを生成させ、また、更には時効処理を施すことで、線径がφ４．５ｍｍ〜φ２０ｍｍの太径鋼線にて、縦割れが発生することなく、１６００Ｎ／ｍｍ2を超える引張強さが安価に得られることを見出した。本発明は、上記知見に基づいてなされたものであり、その要旨とするところは以下の通りである。
（１）質量％で、Ｃ：０．０１〜０．１３％，Ｓｉ：０．３〜４．０％，Ｍｎ：０．３〜８．０％，Ｎｉ：１．０〜６．０％，Ｃｒ：１４．０〜１８．０％，Ｎ：０．０５〜０．２０％を含有し、残部がＦｅおよび実質的に不可避的不純物で構成され、（Ａ）式で示されるＭｄ値が５０〜１２０，引張強さが１６００Ｎ／ｍｍ2を超え、線径がφ４．５ｍｍ〜φ１５ｍｍであることを特徴とする太径の高強度ステンレス鋼線である。
Ｍｄ値＝５５１−４６２（Ｃ＋Ｎ）−９．２Ｓｉ−８．１Ｍｎ−２９（Ｎｉ＋Ｃｕ＋Ｃｏ）−１３．７Ｃｒ−１８．５Ｍｏ −−（Ａ）
式中の元素名はその元素の含有量（質量％）を表す。
（２）さらに、質量％で、Ｃｏ：０．２〜３．０％を含有することを特徴とする前記（１）記載の太径の高強度ステンレス鋼線である。
（３）さらに、質量％で、Ｍｏ：０．２〜３．０％，Ｃｕ：０．２〜３．０％の１種以上を含有することを特徴とする前記（１），（２）記載の太径の高強度ステンレス鋼線である。
（４）さらに、質量％で、Ａｌ：０．０１〜１．０％，Ｎｂ：０．０５〜１．０％，Ｖ：０．０５〜１．０％，Ｔｉ：０．０５〜１．０％，Ｗ：０．０５〜１．０％，Ｔａ：０．０５〜１．０％，Ｚｒ：０．０５〜１．０％の１種類以上を含有することを特徴とする前記（１）〜（３）記載の太径の高強度ステンレス鋼線である。
（５）さらに、Ｂ：０．０００５〜０．０１５％を含有することを特徴とする前記（１）〜（４）記載の太径の高強度ステンレス鋼線である。
（６）さらに、Ｃａ：０．０００５〜０．０１％，Ｍｇ：０．０００５〜０．０１％，ＲＥＭ：０．０００５〜０．０５％の１種以上を含有することを特徴とする前記（１）〜（５）記載の太径の高強度ステンレス鋼線である。
（７）金属組織が、フェライト相，オーステナイト相，加工誘起マルテンサイト相からなり、フェライト相の体積率が２０〜７０％であることを特徴とする前記（１）〜（６）記載の太径の高強度ステンレス鋼線である。
（８）引張強さが８００Ｎ／ｍｍ2以上，破断絞りが５０％以上であることを特徴とする前記（１）〜（７）記載の高強度鋼線用のステンレス鋼線材である。
（９）減面率が２０〜５０％で伸線加工されて製造されることを特徴とする前記（１）〜（７）記載の太径の高強度ステンレス鋼線の製造方法である。
As a result of various studies to solve the above-mentioned problems, the present inventors have found that the structural balance of the austenite phase and the ferrite phase is reduced as a solution treatment with a lower Cr and lower Ni than the two-phase stainless steel regulated by JIS. The wire diameter is φ4.5 mm to φ20 mm by further forming a processing-induced martensite by light drawing (drawing area reduction ratio: 20 to 50%) and further applying an aging treatment. It was found that a tensile strength exceeding 1600 N / mm 2 can be obtained at a low cost without causing vertical cracks in the large-diameter steel wire. This invention is made | formed based on the said knowledge, The place made into the summary is as follows.
(1) By mass%, C: 0.01 to 0.13%, Si: 0.3 to 4.0%, Mn: 0.3 to 8.0%, Ni: 1.0 to 6.0% , Cr: 14.0 to 18.0%, N: 0.05 to 0.20%, the balance being composed of Fe and substantially inevitable impurities, and the Md value represented by the formula (A) is A high-strength stainless steel wire having a large diameter of 50 to 120, a tensile strength exceeding 1600 N / mm 2 and a wire diameter of φ4.5 mm to φ15 mm.
Md value = 551-462 (C + N) -9.2Si-8.1Mn-29 (Ni + Cu + Co) -13.7Cr-18.5Mo-(A)
The element name in the formula represents the content (mass%) of the element.
(2) The high-strength high-strength stainless steel wire according to (1), further containing Co: 0.2 to 3.0% by mass.
(3) The above (1), (2), further comprising at least one of Mo: 0.2-3.0% and Cu: 0.2-3.0% by mass% The large-diameter high-strength stainless steel wire described.
(4) Further, in terms of mass%, Al: 0.01 to 1.0%, Nb: 0.05 to 1.0%, V: 0.05 to 1.0%, Ti: 0.05 to 1. 1% or more of 0%, W: 0.05-1.0%, Ta: 0.05-1.0%, Zr: 0.05-1.0% ) To (3) are large diameter high strength stainless steel wires.
(5) The thick high-strength stainless steel wire according to (1) to (4) above, further containing B: 0.0005 to 0.015%.
(6) The above-mentioned, further comprising at least one of Ca: 0.0005 to 0.01%, Mg: 0.0005 to 0.01%, REM: 0.0005 to 0.05% It is a large-diameter high-strength stainless steel wire described in (1) to (5).
(7) The large diameter according to (1) to (6), wherein the metal structure is composed of a ferrite phase, an austenite phase, and a work-induced martensite phase, and the volume fraction of the ferrite phase is 20 to 70%. High strength stainless steel wire.
(8) The stainless steel wire for high-strength steel wires according to the above (1) to (7), wherein the tensile strength is 800 N / mm 2 or more and the fracture drawing is 50% or more.
(9) The method for producing a large-diameter high-strength stainless steel wire according to (1) to (7), wherein the reduction in area is 20 to 50% and the wire is drawn.
本発明による延性に優れる高強度ステンレス鋼線は、冷間でのばね成形性等を劣化させることなく高強度の太径製品（例えば、ばね製品等）を製造することができ、太径ステンレス鋼線加工品の軽量化に効果を発揮する。 The high-strength stainless steel wire excellent in ductility according to the present invention can produce a high-strength large-diameter product (for example, a spring product) without deteriorating cold spring formability and the like. Effective in reducing the weight of wire products.
以下に、先ず、本発明の請求項１記載の限定理由について説明する。 Below, the reason for limitation of Claim 1 of this invention is demonstrated first.
Ｃは、軽伸線加工後の鋼線の高引張強さを確保するために、０．０１％以上を添加する。しかしながら、０．１３％を超えて添加すると、粒界に炭化物が析出して、線材および鋼線での延性が低下するばかりか低応力破壊が発生する。そのため、上限を０．１３％に限定する。好ましい範囲は、０．０３〜０．１０％である。 C is added in an amount of 0.01% or more in order to ensure high tensile strength of the steel wire after light wire drawing. However, if added over 0.13%, carbide precipitates at the grain boundaries, resulting in low ductility as well as low ductility in the wire and steel wire. Therefore, the upper limit is limited to 0.13%. A preferable range is 0.03 to 0.10%.
Ｎは、軽伸線加工後、更にはその後の時効硬化後の高引張強さを確保するために０．０５％以上を添加する。しかしながら、０．２０％を超えて添加すると鋳造時に気泡が発生し、製造性が著しく劣化する。そのため、上限を０．２０％に限定する。好ましい範囲は、０．０６〜０．１５％である。
Ｓｉは、脱酸のため、また、時効硬化のために、０．３％以上を添加する。しかしながら、４．０％を超えて添加すると材質が脆化するため、上限を４．０％に限定する。好ましい範囲は、０．８〜３．５％である。
N is added in an amount of 0.05% or more in order to ensure high tensile strength after light wire drawing and further after age hardening. However, if added over 0.20%, bubbles are generated during casting, and the productivity is significantly deteriorated. Therefore, the upper limit is limited to 0.20%. A preferable range is 0.06 to 0.15%.
Si is added in an amount of 0.3% or more for deoxidation and for age hardening. However, if added over 4.0%, the material becomes brittle, so the upper limit is limited to 4.0%. A preferable range is 0.8 to 3.5%.
Ｍｎは、脱酸のため、または、組織調整のために０．３％以上を添加する。しかしながら、８．０％を超えて添加するとオーステナイト相の安定度が増し、軽伸線加工では高強度化しなくなる。そのため、上限を８．０％に限定する。好ましい範囲は、０．５〜３．０％である。 Mn is added in an amount of 0.3% or more for deoxidation or for structure adjustment. However, if added over 8.0%, the stability of the austenite phase increases, and the strength is not increased by light wire drawing. Therefore, the upper limit is limited to 8.0%. A preferable range is 0.5 to 3.0%.
Ｎｉは、組織調整と延性を改善する重要な元素であるため、１．０％以上を添加する。しかしながら、６．０％を超えて添加するとオーステナイト相の安定度が増し、軽伸線加工では高強度化しなくなる。そのため、上限を６．０％に限定する。好ましい範囲は、２．０〜５．０％である。 Since Ni is an important element for improving the structure adjustment and ductility, 1.0% or more is added. However, if added over 6.0%, the stability of the austenite phase increases, and the strength is not increased by light wire drawing. Therefore, the upper limit is limited to 6.0%. A preferable range is 2.0 to 5.0%.
Ｃｒは、組織調整し、耐食性を確保するために１４．０％以上添加する。しかしながら、１８．０％を超えて添加するとオーステナイト相の安定度が増し、軽伸線加工では高強度化しなくなる。そのため、上限を１８．０％に限定する。好ましい範囲は、１５．０〜１７．５％である。 Cr is added in an amount of 14.0% or more in order to adjust the structure and ensure corrosion resistance. However, if added over 18.0%, the stability of the austenite phase is increased, and the strength is not increased by light wire drawing. Therefore, the upper limit is limited to 18.0%. A preferable range is 15.0 to 17.5%.
前記（Ａ）式で表されるＭｄ値は、オーステナイト安定度の指標として知られている式に、さらにＣｏの項目を付加した式である。Ｃｏの影響度はＮｉ、Ｃｕと同等であるとした。本発明においてＭｄ値は、軽伸線後の加工誘起マルテンサイト量と強い相関がある指標であり、高強度と延性を確保するためにＭｄ値を制御する必要がある。Ｍｄ値が５０未満の場合、オーステナイト相の安定度が増し、軽伸線加工では高強度化しなくなる。一方、Ｍｄ値が１２０を超えると、軽伸線加工前の溶体化処理ままでマルテンサイト相が生成するため、軽伸線加工後の延性が低下する。そのため、Ｍｄ値を５０〜１２０に限定する。好ましい範囲は、７０〜１００である。 The Md value represented by the formula (A) is a formula obtained by adding an item of Co to a formula known as an austenite stability index. The influence of Co is assumed to be equivalent to Ni and Cu. In the present invention, the Md value is an index having a strong correlation with the amount of work-induced martensite after light drawing, and it is necessary to control the Md value in order to ensure high strength and ductility. When the Md value is less than 50, the stability of the austenite phase is increased, and the strength is not increased by light wire drawing. On the other hand, when the Md value exceeds 120, the martensite phase is generated as it is in the solution treatment before the light wire drawing, so that the ductility after the light wire drawing is lowered. Therefore, the Md value is limited to 50 to 120. A preferred range is 70-100.
引張強さは、１６００Ｎ／ｍｍ2以下では既存の太径ステンレス鋼線との優位性がなくなる。そのため、本発明では鋼線の引張強さを１６００Ｎ／ｍｍ2超に限定する。 If the tensile strength is 1600 N / mm 2 or less, the superiority with the existing large diameter stainless steel wire is lost. Therefore, in the present invention, the tensile strength of the steel wire is limited to more than 1600 N / mm 2 .
鋼線の線径がφ４．５ｍｍ未満の場合、従来の伸線加工による高強度ステンレス鋼線で対応できるため、本発明の効果が不明瞭になる。一方、線径がφ４．５ｍｍ以上に太い場合、従来の伸線加工材では強伸線加工が必要であり、不経済になるばかりか伸線縦割れが発生する。そのため、φ４．５ｍｍ以上に限定する。しかしながら、φ１５ｍｍを超えると伸線加工時の応力が大きくなり伸線縦割れが生成しやすくなる。そのため、φ１５ｍｍ以下に限定する。好ましい範囲は、φ５〜φ１２ｍｍである。 If the wire diameter of the steel wire is less than φ4.5 mm, the effect of the present invention becomes unclear because it can be handled by a conventional high-strength stainless steel wire by wire drawing. On the other hand, when the wire diameter is thicker than φ4.5 mm, the conventional wire drawing material requires strong wire drawing, which is not economical and causes wire drawing vertical cracks. Therefore, it is limited to φ4.5 mm or more. However, if it exceeds φ15 mm, the stress at the time of wire drawing increases and wire drawing vertical cracks are likely to be generated. Therefore, it is limited to φ15 mm or less. A preferable range is φ5 to φ12 mm.
次に、本発明の請求項２記載の限定理由について説明する。 Next, the reason for limitation according to claim 2 of the present invention will be described.
Ｃｏは、マトリックスの靱性を向上させ、延性が向上するため、必要に応じて０．２％以上を添加する。しかしながら、３．０％を超えて添加すると、オーステナイト相の安定度が増し、軽伸線加工では高強度化しなくなるばかりか、経済的でない。そのため、上限を３．０％に限定する。好ましい範囲は、０．５〜２．０％である。 Co improves the toughness of the matrix and improves the ductility, so 0.2% or more is added as necessary. However, if added over 3.0%, the stability of the austenite phase increases, and not only does the strength not increase in light drawing, but it is not economical. Therefore, the upper limit is limited to 3.0%. A preferable range is 0.5 to 2.0%.
次に、本発明の請求項３記載の限定理由について説明する。 Next, the reason for limitation according to claim 3 of the present invention will be described.
Ｍｏは、素材の耐食性を向上させるため、必要に応じて、０．２％以上を添加する。しかしながら、３．０％を超えて添加すると、オーステナイト相の安定度が増し、軽伸線加工では高強度化しなくなる。そのため、上限を３．０％に限定する。好ましい範囲は、０．５〜２．５％である。 In order to improve the corrosion resistance of the material, Mo is added in an amount of 0.2% or more as necessary. However, if added over 3.0%, the stability of the austenite phase increases, and the strength is not increased by light wire drawing. Therefore, the upper limit is limited to 3.0%. A preferable range is 0.5 to 2.5%.
Ｃｕは、素材の耐食性を向上させるため、必要に応じて、０．２％以上を添加する。しかしながら、３．０％を超えて添加してもその効果は飽和するし、逆にオーステナイト相の加工硬化量が低減し、軽伸線加工では高強度化しなくなる。そのため、上限を３．０％に限定する。 In order to improve the corrosion resistance of the material, Cu is added in an amount of 0.2% or more as necessary. However, even if added over 3.0%, the effect is saturated, and conversely, the work hardening amount of the austenite phase is reduced, and the strength is not increased by light wire drawing. Therefore, the upper limit is limited to 3.0%.
次に、本発明の請求項４記載の限定理由について説明する。 Next, the reason for limitation according to claim 4 of the present invention will be described.
Ａｌは、脱酸のため、また、窒化物を形成して結晶粒径を微細にして強度・延性バランスを改善するため、必要に応じて、０．０１％以上を添加する。しかしながら、１．０％を超えて添加すると、粗大介在物が生成し、強度・延性バランスが低下する。そのため、上限を１．０％に限定する。好ましい範囲は、０．０１５〜０．５％である。 Al is added in an amount of 0.01% or more, if necessary, for deoxidation or to form a nitride to reduce the crystal grain size and improve the strength / ductility balance. However, if added over 1.0%, coarse inclusions are generated, and the strength / ductility balance is lowered. Therefore, the upper limit is limited to 1.0%. A preferred range is 0.015 to 0.5%.
Ｎｂ，Ｖ，Ｔｉ，Ｗ，Ｔａ，Ｚｒは、炭窒化物を形成して結晶粒径を微細にして強度・延性バランスを改善するため、必要に応じて、Ｎｂ：０．０５〜１．０％，Ｖ：０．０５〜１．０％，Ｔｉ：０．０５〜１．０％，Ｗ：０．０５〜１．０％，Ｔａ：０．０５〜１．０％，Ｚｒ：０．０５〜１．０％を添加する。しかしながら、上限を超えて添加すると粗大介在物が生成し、強度・延性バランスが低下する。 Nb, V, Ti, W, Ta, and Zr form carbonitrides to reduce the crystal grain size and improve the strength / ductility balance. Therefore, Nb: 0.05 to 1.0 as necessary. %, V: 0.05 to 1.0%, Ti: 0.05 to 1.0%, W: 0.05 to 1.0%, Ta: 0.05 to 1.0%, Zr: 0. Add 05-1.0%. However, if added over the upper limit, coarse inclusions are formed, and the strength / ductility balance is lowered.
次に、本発明の請求項５記載の限定理由について説明する。 Next, the reason for limitation according to claim 5 of the present invention will be described.
Ｂは、熱間製造性および靱性を向上させるため、必要に応じて、０．０００５％以上を添加する。しかしながら、０．０１５％を超えて添加するとボライドが生成するため、逆に靱性が低下して、延性が低下する。そのため、上限を０．０１５％にする。好ましい範囲は、０．００１〜０．０１％である。 In order to improve hot manufacturability and toughness, B is added in an amount of 0.0005% or more as necessary. However, if added over 0.015%, boride is generated, so that the toughness is lowered and the ductility is lowered. Therefore, the upper limit is made 0.015%. A preferred range is 0.001 to 0.01%.
次に、本発明の請求項６記載の限定理由について説明する。 Next, the reason for limitation according to claim 6 of the present invention will be described.
Ｃａ，Ｍｇ，ＲＥＭは、脱酸のため、必要に応じて、Ｃａ：０．０００５〜０．０１％，Ｍｇ：０．０００５〜０．０１％，ＲＥＭ：０．０００５〜０．０５％の１種以上を添加する。しかしながら、各上限を超えて添加すると粗大介在物が生成して延性が低下する。 Ca, Mg, and REM are for deoxidation, and if necessary, Ca: 0.0005 to 0.01%, Mg: 0.0005 to 0.01%, REM: 0.0005 to 0.05% Add one or more. However, when it exceeds each upper limit, a coarse inclusion will produce | generate and ductility will fall.
次に、本発明の請求項７記載の限定理由について説明する。 Next, the reason for limitation according to claim 7 of the present invention will be described.
金属組織は、前述したように、本発明鋼では溶体化処理ままでオーステナイト相とフェライト相の組織を有し、軽伸線加工により加工誘起マルテンサイト相が生成して３相混合組織となるが、フェライト相が体積分率で２０％未満の場合、延性が劣化する。一方で、フェライト相が体積分率で７０％を超えると軽伸線加工では高強度が得られなくなる。そのため、フェライト相の体積分率を２０〜７０％に限定する。好ましくは、３０〜６０％である。 As described above, the steel of the present invention has a structure of an austenite phase and a ferrite phase as it is in a solution treatment, and a work-induced martensite phase is generated by light wire drawing to form a three-phase mixed structure. When the ferrite phase is less than 20% in volume fraction, ductility deteriorates. On the other hand, if the ferrite phase exceeds 70% in volume fraction, high strength cannot be obtained by light drawing. Therefore, the volume fraction of the ferrite phase is limited to 20 to 70%. Preferably, it is 30 to 60%.
次に、本発明の請求項８記載の限定理由について説明する。 Next, the reason for limitation according to claim 8 of the present invention will be described.
請求項１〜６の鋼線は、引張強さが１６００Ｎ／ｍｍ2超の強度を有するが、軽伸線加工により鋼線に製造するためには、素材である線材の引張強さが８００Ｎ／ｍｍ2以上にし、破断絞りが５０％以上の高延性を有することが好ましい。そのため、必要に応じて、素材である線材の引張強さを８００／ｍｍ2以上，破断絞りを５０％以上に限定する。 The steel wires of claims 1 to 6 have a tensile strength of more than 1600 N / mm 2, but in order to produce a steel wire by light wire drawing, the tensile strength of the wire material is 800 N / mm. It is preferable that the thickness is not less than 2 mm and the fracture drawing has a high ductility of 50% or more. Therefore, if necessary, the tensile strength of the wire material is limited to 800 / mm 2 or more and the fracture drawing is limited to 50% or more.
次に、本発明の請求項９記載の限定理由について説明する。 Next, the reason for limitation according to claim 9 of the present invention will be described.
鋼線の伸線加工時の伸線減面率は、１６００Ｎ／ｍｍ2超の強度を得るために２０％以上が必要であるが、５０％を超えると低応力破壊が発生する。そのため、上限を５０％にする。 In order to obtain a strength of more than 1600 N / mm 2 , the drawing area reduction rate during drawing of the steel wire needs to be 20% or more, but if it exceeds 50%, low stress fracture occurs. Therefore, the upper limit is made 50%.
請求項１に規定した鋼成分を含有する線材について、上記請求項９に規定する項目以外については通常の軽伸線加工を行ってφ４．５ｍｍ〜φ１５ｍｍのステンレス鋼線とすることにより、鋼線の引張強さ１６００Ｎ／ｍｍ2超、鋼線の引張破断絞り３０％以上の材質を実現することができる。また、請求項７に規定する金属組織を得ることができる。 About the wire containing the steel component specified in claim 1, except for the items specified in claim 9, the steel wire is formed by performing a normal light wire drawing to obtain a stainless steel wire of φ4.5 mm to φ15 mm. A material having a tensile strength of more than 1600 N / mm 2 and a tensile breakage of steel wire of 30% or more can be realized. Moreover, the metal structure prescribed | regulated to Claim 7 can be obtained.
以下に本発明の実施例について説明する。 Examples of the present invention will be described below.
表１、２に実施例の鋼の化学組成を示す。 Tables 1 and 2 show the chemical compositions of the steels of the examples.
これらの化学組成の鋼は、１００ｋｇの真空溶解炉にて溶解し、φ１８０ｍｍの鋳片に鋳造し、その鋳片をφ２０〜５ｍｍまで熱間の線材圧延を行い、１０００℃で熱間圧延を終了した。その後、１０５０℃で３０分，水冷の溶体化処理を施し、酸洗を行い線材製品とした。その後、φ１６〜３．５ｍｍまで冷間で軽伸線加工（伸線減面率≦５０％）を施し、引き続き４５０℃で３０分の時効処理を行い、高強度のステンレス鋼線とした。 Steel of these chemical compositions is melted in a 100 kg vacuum melting furnace, cast into a slab of φ180 mm, the slab is hot-wire rolled to φ20-5 mm, and hot rolling is finished at 1000 ° C. did. Thereafter, a solution cooling treatment with water cooling was performed at 1050 ° C. for 30 minutes, and pickling was performed to obtain a wire product. Then, light wire drawing (drawing area reduction ratio ≦ 50%) was applied to φ16 to 3.5 mm in a cold state, followed by aging treatment at 450 ° C. for 30 minutes to obtain a high-strength stainless steel wire.
そして、線材および鋼線の機械的性質および金属組織を評価した。その評価結果を表３、４に示す。 And the mechanical property and metal structure of a wire and a steel wire were evaluated. The evaluation results are shown in Tables 3 and 4.
機械的性質は、ＪＩＳ Ｚ ２２４１の引張試験での引張強さと破断絞りにて評価した。本発明例の線材では、全て１２００Ｎ／ｍｍ2以下であり、本発明例の鋼線では、全て１６００Ｎ／ｍｍ2超，破断絞りが３０％以上であり、強度と延性に優れていた。 The mechanical properties were evaluated by the tensile strength and breaking drawing in the tensile test of JIS Z 2241. All of the wires of the examples of the present invention were 1200 N / mm 2 or less, and all of the steel wires of the examples of the present invention were over 1600 N / mm 2 and the fracture drawing was 30% or more, and the strength and ductility were excellent.
金属組織は、鋼線を縦断面中心面に埋め込み・鏡面研磨し、ＪＩＳ Ｇ ０５７１ に従い、蓚酸電解エッチを行い、金属組織を判定した。そして、中心部付近のフェライト相について画像解析を行い、フェライト相の分率（Ｖｏｌ．％）を算出した。本発明の金属組織は、フェライト相，オーステナイト相，加工誘起マルテンサイト相の混合組織であり、フェライト分率は２０〜６５Ｖｏｌ．％の範囲内にあった。 For the metal structure, a steel wire was embedded in the center plane of the longitudinal section and mirror-polished, and oxalic acid electrolytic etching was performed according to JIS G 0571 to determine the metal structure. Then, image analysis was performed on the ferrite phase near the center, and the fraction (Vol.%) Of the ferrite phase was calculated. The metal structure of the present invention is a mixed structure of a ferrite phase, an austenite phase, and a work-induced martensite phase, and the ferrite fraction is 20 to 65 Vol. %.
一方、比較例Ｎｏ．２５，２７は、それぞれ、Ｃ，Ｎ量が低く、線材および鋼線の引張強さが低い。 On the other hand, Comparative Example No. 25 and 27 have low C and N contents, respectively, and the tensile strength of the wire and the steel wire is low.
比較例Ｎｏ．２６は、Ｃ量が高く、線材の延性が低いばかりか、伸線後の延性が低く、低応力破壊が発生している。 Comparative Example No. No. 26 has a high C content and a low ductility of the wire, and also has a low ductility after the drawing, resulting in low stress fracture.
比較例Ｎｏ．２８は、Ｎ量が高いため、鋳片で気泡が発生し、製品に製造できない。 Comparative Example No. In No. 28, since the N amount is high, bubbles are generated in the slab and cannot be manufactured into a product.
比較例Ｎｏ．２９は、Ｓｉ量が高いため、鋼線の延性が劣化し、低応力破壊が発生している。 Comparative Example No. Since No. 29 has a high Si content, the ductility of the steel wire is deteriorated and low stress fracture occurs.
比較例Ｎｏ．３０は、Ｍｎ量が高いため、Ｍｄ値が低く、オーステナイト相の安定度が増し、軽伸線加工で高強度化していない。 Comparative Example No. Since No. 30 has a high Mn content, the Md value is low, the stability of the austenite phase is increased, and the strength is not increased by light wire drawing.
比較例Ｎｏ．３１は、Ｎｉ量が低いため、延性が劣化している。 Comparative Example No. No. 31 has a low amount of Ni, so the ductility is degraded.
比較例Ｎｏ．３２は、Ｎｉ量が高いため、Ｍｄ値が低く、オーステナイト相の安定度が増し、軽伸線加工で高強度化していない。 Comparative Example No. No. 32 has a high Ni content, so the Md value is low, the stability of the austenite phase is increased, and the strength is not increased by light wire drawing.
比較例Ｎｏ．３３は、Ｃｒ量が低いため、Ｍｄ値が高く、フェライト分率が低いため、延性に劣るばかりか、耐食性に劣る。 Comparative Example No. Since No. 33 has a low Cr content, the Md value is high and the ferrite fraction is low, so it is not only inferior in ductility but also inferior in corrosion resistance.
比較例Ｎｏ．３４，３５は、それぞれ、Ｃｒ，Ｍｏ量が高いため、Ｍｄ値が低く、オーステナイト相の安定度が増し、また、フェライト分率が高いため、軽伸線加工で高強度化していない。 Comparative Example No. Since 34 and 35 have high Cr and Mo contents, respectively, the Md value is low, the stability of the austenite phase is increased, and since the ferrite fraction is high, the strength is not increased by light wire drawing.
比較例Ｎｏ．３６，３７は、それぞれＣｕ，Ｃｏ量が高いため、Ｍｄ値が低く、オーステナイト相の安定度が増し、軽伸線加工で高強度化していない。 Comparative Example No. Since 36 and 37 have high amounts of Cu and Co, respectively, the Md value is low, the stability of the austenite phase is increased, and the strength is not increased by light wire drawing.
比較例Ｎｏ．３８は、Ａｌ量が高すぎるため粗大介在物が生成し、強度・延性バランスが劣化している。 Comparative Example No. In No. 38, since the amount of Al is too high, coarse inclusions are generated, and the strength / ductility balance is deteriorated.
比較例Ｎｏ．３９〜４８は、それぞれ、Ａｌ，Ｎｂ，Ｖ，Ｔｉ，Ｗ，Ｔａ，Ｚｒ，Ｂ，Ｃａ，Ｍｇ，ＲＥＭが高過ぎるため、強度延性バランスが劣化している。 Comparative Example No. In Nos. 39 to 48, Al, Nb, V, Ti, W, Ta, Zr, B, Ca, Mg, and REM are too high, and the strength ductility balance is deteriorated.
比較例Ｎｏ．４９は、鋼線の線径が太過ぎるため、鋼線で伸線縦割れが発生している。 Comparative Example No. In No. 49, since the wire diameter of the steel wire is too large, a longitudinal crack is drawn in the steel wire.
比較例Ｎｏ．５０は、鋼線の線径が細過ぎるため、従来の高強度鋼線と差別化ができず、本発明の効果が発揮できていない。 Comparative Example No. No. 50 cannot differentiate from the conventional high-strength steel wire because the wire diameter of the steel wire is too thin, and the effect of the present invention cannot be exhibited.
比較例Ｎｏ．５１は、伸線加工の伸線減面率が小さいため高強度化していない。 Comparative Example No. No. 51 is not increased in strength because the drawing area reduction rate of drawing is small.
比較例Ｎｏ．５２は、伸線加工の伸線減面率が大きいため延性が劣化し、低応力破壊が発生している。 Comparative Example No. No. 52 has a large wire-drawing area reduction rate, so that ductility is deteriorated and low-stress fracture occurs.
以上の各実施例から明らかなように、本発明により、延性に優れる太径の高強度ステンレス鋼線を安価に製造でき、冷間でのばね成形性を劣化させることなくばね等の製品加工が可能であり、軽量化・耐久性に優れる太径製品を安価に提供することができ、産業上極めて有用である。 As is clear from the above examples, according to the present invention, a large-diameter high-strength stainless steel wire excellent in ductility can be manufactured at low cost, and product processing such as springs can be performed without deteriorating cold spring formability. It is possible to provide a large-diameter product excellent in weight reduction and durability at low cost, and is extremely useful in industry.
Claims (9)
Ｍｄ値＝５５１−４６２（Ｃ＋Ｎ）−９．２Ｓｉ−８．１Ｍｎ−２９（Ｎｉ＋Ｃｕ＋Ｃｏ）−１３．７Ｃｒ−１８．５Ｍｏ −−（Ａ）
式中の元素名はその元素の含有量（質量％）を表す。 In mass%, C: 0.01 to 0.13%, Si: 0.3 to 4.0%, Mn: 0.3 to 8.0%, Ni: 1.0 to 6.0%, Cr: 14.0 to 18.0%, N: 0.05 to 0.20%, the balance is substantially composed of Fe and inevitable impurities, and the Md value represented by the formula (A) is 50 to 120 A high-strength stainless steel wire with a large diameter, characterized by a tensile strength exceeding 1600 N / mm 2 and a wire diameter of φ4.5 mm to φ15 mm.
Md value = 551-462 (C + N) -9.2Si-8.1Mn-29 (Ni + Cu + Co) -13.7Cr-18.5Mo-(A)
The element name in the formula represents the content (mass%) of the element.
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| JP2015196870A (en) * | 2014-03-31 | 2015-11-09 | 新日鐵住金ステンレス株式会社 | High strength dual-phase stainless steel wire rod excellent in spring fatigue characteristic and production method therefor, and high strength dual-phase stainless steel wire excellent in spring fatigue characteristic |
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| JPH08246106A (en) * | 1995-03-10 | 1996-09-24 | Nippon Steel Corp | Austenitic stainless steel wire, excellent in stress corrosion cracking resistance and having high strength and high proof stress, and its production |
| JP2005298932A (en) * | 2004-04-14 | 2005-10-27 | Nippon Steel & Sumikin Stainless Steel Corp | Metastable austenitic stainless steel wire used for high strength steel wire for spring excellent in rigidity |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08246106A (en) * | 1995-03-10 | 1996-09-24 | Nippon Steel Corp | Austenitic stainless steel wire, excellent in stress corrosion cracking resistance and having high strength and high proof stress, and its production |
| JP2005298932A (en) * | 2004-04-14 | 2005-10-27 | Nippon Steel & Sumikin Stainless Steel Corp | Metastable austenitic stainless steel wire used for high strength steel wire for spring excellent in rigidity |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009221554A (en) * | 2008-03-17 | 2009-10-01 | Nisshin Steel Co Ltd | Stainless steel for low nickel vehicle body member excellent in workability and impulse absorption performance |
| JP2009221553A (en) * | 2008-03-17 | 2009-10-01 | Nisshin Steel Co Ltd | Stainless steel for low nickel springs excellent in settling resistance and bendability |
| JP2014185367A (en) * | 2013-03-22 | 2014-10-02 | Nippon Steel & Sumikin Stainless Steel Corp | Stainless steel wire excellent in twisting processability and manufacturing method therefor, and stainless steel wire and manufacturing method therefor |
| JP2015196870A (en) * | 2014-03-31 | 2015-11-09 | 新日鐵住金ステンレス株式会社 | High strength dual-phase stainless steel wire rod excellent in spring fatigue characteristic and production method therefor, and high strength dual-phase stainless steel wire excellent in spring fatigue characteristic |
| WO2015190422A1 (en) * | 2014-06-11 | 2015-12-17 | 新日鐵住金ステンレス株式会社 | High strength duplex stainless steel wire rod, high strength duplex stainless steel wire and manufacturing method therefor as well as spring component |
| JPWO2015190422A1 (en) * | 2014-06-11 | 2017-04-20 | 新日鐵住金ステンレス株式会社 | High-strength duplex stainless steel wire, high-strength duplex stainless steel wire and its manufacturing method, and spring parts |
| JP2018021260A (en) * | 2016-07-25 | 2018-02-08 | 新日鐵住金ステンレス株式会社 | Thick-sized high-strength stainless steel wire and method for producing the same, and spring component |
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| Publication number | Publication date |
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| JP4772588B2 (en) | 2011-09-14 |
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