TW202106409A - Austenitic stainless steel and manufacturing method thereof - Google Patents
Austenitic stainless steel and manufacturing method thereof Download PDFInfo
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- TW202106409A TW202106409A TW109119946A TW109119946A TW202106409A TW 202106409 A TW202106409 A TW 202106409A TW 109119946 A TW109119946 A TW 109119946A TW 109119946 A TW109119946 A TW 109119946A TW 202106409 A TW202106409 A TW 202106409A
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- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims description 61
- 238000004519 manufacturing process Methods 0.000 title claims description 30
- 238000005098 hot rolling Methods 0.000 claims abstract description 68
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 42
- 239000010959 steel Substances 0.000 claims abstract description 42
- 238000001816 cooling Methods 0.000 claims abstract description 19
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 15
- 238000000034 method Methods 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims abstract description 7
- 238000009749 continuous casting Methods 0.000 claims abstract description 4
- 238000009826 distribution Methods 0.000 claims description 33
- 229910052757 nitrogen Inorganic materials 0.000 claims description 17
- 239000000203 mixture Substances 0.000 claims description 15
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 15
- 150000002910 rare earth metals Chemical class 0.000 claims description 15
- 239000000126 substance Substances 0.000 claims description 14
- 230000005291 magnetic effect Effects 0.000 claims description 13
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 12
- 230000009467 reduction Effects 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 8
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052749 magnesium Inorganic materials 0.000 claims description 7
- 229910052758 niobium Inorganic materials 0.000 claims description 7
- 229910052760 oxygen Inorganic materials 0.000 claims description 7
- 230000035699 permeability Effects 0.000 claims description 7
- 229910052721 tungsten Inorganic materials 0.000 claims description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- 229910052787 antimony Inorganic materials 0.000 claims description 6
- 229910052796 boron Inorganic materials 0.000 claims description 6
- 229910052791 calcium Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052717 sulfur Inorganic materials 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052727 yttrium Inorganic materials 0.000 claims description 6
- 229910052726 zirconium Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052745 lead Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 229910052718 tin Inorganic materials 0.000 claims description 5
- 238000005096 rolling process Methods 0.000 description 23
- 230000000694 effects Effects 0.000 description 19
- 229910001220 stainless steel Inorganic materials 0.000 description 15
- 239000010935 stainless steel Substances 0.000 description 15
- 239000011572 manganese Substances 0.000 description 11
- 230000007797 corrosion Effects 0.000 description 10
- 238000005260 corrosion Methods 0.000 description 10
- 230000007423 decrease Effects 0.000 description 10
- 239000011777 magnesium Substances 0.000 description 10
- 239000010936 titanium Substances 0.000 description 10
- 239000011651 chromium Substances 0.000 description 9
- 239000010955 niobium Substances 0.000 description 9
- 239000011575 calcium Substances 0.000 description 8
- 239000010949 copper Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 239000006104 solid solution Substances 0.000 description 7
- 238000010273 cold forging Methods 0.000 description 6
- 238000010586 diagram Methods 0.000 description 6
- 238000004806 packaging method and process Methods 0.000 description 5
- 230000000704 physical effect Effects 0.000 description 5
- 238000005554 pickling Methods 0.000 description 5
- 238000005482 strain hardening Methods 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- 230000002411 adverse Effects 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 238000009628 steelmaking Methods 0.000 description 4
- 239000002344 surface layer Substances 0.000 description 4
- 238000003483 aging Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005097 cold rolling Methods 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 206010070834 Sensitisation Diseases 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000005294 ferromagnetic effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- QEFYFXOXNSNQGX-UHFFFAOYSA-N neodymium atom Chemical compound [Nd] QEFYFXOXNSNQGX-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 1
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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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
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- 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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- 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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- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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Abstract
Description
本發明係關於奧氏體系不銹鋼及其製造方法。The present invention relates to austenitic stainless steel and its manufacturing method.
因為以智慧手機作為代表的攜帶型電子設備具有小型輕量化及設計性提升之需要，故在用於此等攜帶型電子設備之金屬製外包裝部件的製造中通常使用以下方法：為了能夠對應地加工成複雜的形狀，於施加嚴苛條件的冷鍛後藉由切削加工來成形。又，根據攜帶型電子設備的設計，亦有在切削後進行鏡面研磨的情形。此處，為了避免對設備本身內建的地磁感應器等產生不利影響，攜帶型電子設備的外包裝部件不僅需要是非磁性的，且還需要具有高強度。另外，由於上述電子設備為攜帶型，因此經常在室外環境中使用，故相較於以在室內使用作為前提的電子設備用部件，上述電子設備的外包裝部件被要求具有更高的耐腐蝕性。Because portable electronic devices represented by smart phones have the need to be smaller, lighter, and better in design, the following methods are usually used in the manufacture of metal outer packaging parts for these portable electronic devices: It is processed into complex shapes and formed by cutting after cold forging under severe conditions. Also, depending on the design of portable electronic devices, mirror polishing may be performed after cutting. Here, in order to avoid adverse effects on the geomagnetic sensor built in the device itself, the outer packaging components of the portable electronic device not only need to be non-magnetic, but also need to have high strength. In addition, since the above-mentioned electronic equipment is portable and is often used in outdoor environments, the outer packaging parts of the above-mentioned electronic equipment are required to have higher corrosion resistance than components for electronic equipment that are premised on indoor use. .
就用於上述外包裝部件的製造之金屬材料而言，舉例來說，專利文獻1揭示一種非磁性奧氏體系不銹鋼鋼板(以下，簡稱為「不銹鋼鋼板」)，其係經冷鍛及切削加工而成為非磁性部件。Regarding the metal materials used in the manufacture of the above-mentioned outer packaging parts, for example, Patent Document 1 discloses a non-magnetic austenitic stainless steel plate (hereinafter referred to as "stainless steel plate"), which is cold forged and cut Processed into non-magnetic parts.
[先前技術文獻] [專利文獻] [專利文獻1] 日本國公開專利公報「特開2018-109215號公報」[Prior Technical Literature] [Patent Literature] [Patent Document 1] Japanese Patent Publication "JP 2018-109215"
[發明所欲解決問題] 雖然專利文獻1所記載的不銹鋼鋼板的製造方法在製造非磁性且高強度的部件上係為良好的方法，但其具有以下問題點：製造步驟複雜且成本高以及無法根據產品的形狀來利用製造之不銹鋼鋼板。[The problem is solved by the invention] Although the method for manufacturing a stainless steel sheet described in Patent Document 1 is a good method for manufacturing non-magnetic and high-strength parts, it has the following problems: the manufacturing steps are complicated, the cost is high, and the manufacturing cannot be used according to the shape of the product. The stainless steel plate.
接著，在圖8中顯示了以下例子：當對退火材料進行冷軋時，或者當對板厚較厚的材料進行冷軋(調質軋延)時，應變集中在表面層上並使在板厚方向的硬度分布變得不均勻。具體而言，圖8顯示了將不銹鋼鋼板的板厚方向上的硬度分布調整成板厚為8mm及平均截面硬度為300HV。在一般的冷軋中，由於表層的應變大且板厚中央的應變小，因此表層的硬度為332HV，而在板厚中央的硬度僅為275HV。換言之，在專利文獻1的不銹鋼鋼板中具有以下問題：如果將板厚增加到一定程度以上，則板厚方向的硬度變得不均勻。Next, the following example is shown in Fig. 8: When cold rolling is performed on an annealed material, or when cold rolling is performed on a thicker plate (tempered and tempered rolling), the strain is concentrated on the surface layer and makes the plate The hardness distribution in the thickness direction becomes uneven. Specifically, FIG. 8 shows that the hardness distribution in the thickness direction of the stainless steel steel plate is adjusted to a thickness of 8 mm and an average cross-sectional hardness of 300 HV. In general cold rolling, since the strain of the surface layer is large and the strain in the center of the plate thickness is small, the hardness of the surface layer is 332HV, while the hardness in the center of the plate thickness is only 275HV. In other words, the stainless steel sheet of Patent Document 1 has the following problem: If the sheet thickness is increased to a certain level or more, the hardness in the sheet thickness direction becomes non-uniform.
本發明的一態樣係有鑒於前述問題點所完成者，其目的為：即使厚度為一定程度以上，也能夠實現一種奧氏體系不銹鋼及其製造方法，其係能夠降低厚度方向上的截面硬度分布的不均勻。One aspect of the present invention is accomplished in view of the foregoing problems, and its purpose is to realize an austenitic stainless steel and a manufacturing method thereof even if the thickness is greater than a certain level, which can reduce the cross section in the thickness direction. Uneven hardness distribution.
[解決問題之手段] 為了解決上述課題，本發明一態樣之奧氏體系不銹鋼，其係包含：以質量%計，碳(C)與氮(N)的合計含量為0.08%以上；厚度方向的平均截面硬度分布為250HV以上，且變動範圍為30HV以下；及厚度為3mm以上。[Means to Solve the Problem] In order to solve the above-mentioned problems, an austenitic stainless steel of one aspect of the present invention includes: in terms of mass %, the total content of carbon (C) and nitrogen (N) is 0.08% or more; the average cross-sectional hardness distribution in the thickness direction It is 250HV or more, and the variation range is 30HV or less; and the thickness is 3mm or more.
根據前述構成，即使厚度為3mm以上，但在厚度方向上的平均截面硬度分布為250HV以上，且變動範圍為30HV以下。因此，即使厚度為一定程度以上，也能夠提供一種奧氏體系不銹鋼及其製造方法，其係能夠降低厚度方向上的截面硬度分布的不均勻。According to the aforementioned configuration, even if the thickness is 3 mm or more, the average cross-sectional hardness distribution in the thickness direction is 250 HV or more, and the variation range is 30 HV or less. Therefore, even if the thickness is greater than a certain level, it is possible to provide an austenitic stainless steel and a method of manufacturing the same, which can reduce the unevenness of the cross-sectional hardness distribution in the thickness direction.
[1]本發明一態樣的奧氏體系不銹鋼，其中，以質量%計，前述奧氏體系不銹鋼的化學組成係包括：C：0.003~0.12%、Si：2.00%以下、Mn：2.00%以下、P：0.04%以下、S：0.030%以下、Ni：6.0~15.0%、Cr：16.0~22.0%、N：0.005~0.20%以及其餘為Fe與不可避免的雜質。[1] The austenitic stainless steel according to one aspect of the present invention, wherein, in terms of mass %, the chemical composition of the aforementioned austenitic stainless steel includes: C: 0.003 to 0.12%, Si: 2.00% or less, and Mn: 2.00 % Or less, P: 0.04% or less, S: 0.030% or less, Ni: 6.0~15.0%, Cr: 16.0~22.0%, N: 0.005~0.20%, and the rest are Fe and unavoidable impurities.
[2]如[1]所述之奧氏體系不銹鋼，其中，在前述化學組成的基礎上，以質量%計，還包含下述成分的一種或兩種以上：Mo：0.01~3.00%、Cu：0.01~3.50%、Al：0.0080%以下、O：0.0040~0.0100%、V：0.01~0.5%、B：0.001~0.01%、Ti：0.01~0.50%。[2] The austenitic stainless steel as described in [1], wherein, based on the aforementioned chemical composition, in terms of mass %, it further contains one or more of the following components: Mo: 0.01 to 3.00%, Cu: 0.01~3.50%, Al: 0.0080% or less, O: 0.0040~0.0100%, V: 0.01~0.5%, B: 0.001~0.01%, Ti: 0.01~0.50%.
[3]如[1]或[2]所述之奧氏體系不銹鋼，其中，在前述化學組成的基礎上，以質量%計，還包含下述成分的一種或兩種以上：Co：0.01~0.50%、Zr：0.01~0.10%、Nb：0.01~0.10%、Mg：0.0005~0.0030%、Ca：0.0003~0.0030%、Y：0.01~0.20%、稀土類金屬(REM)：0.01~0.10%、Sn：0.001~0.500%及Sb：0.001~0.500%、Pb：0.01~0.10%、W：0.01~0.50%。[3] The austenitic stainless steel according to [1] or [2], wherein, on the basis of the aforementioned chemical composition, in terms of mass %, it further contains one or more of the following components: Co: 0.01 ~0.50%, Zr: 0.01~0.10%, Nb: 0.01~0.10%, Mg: 0.0005~0.0030%, Ca: 0.0003~0.0030%, Y: 0.01~0.20%, rare earth metals (REM): 0.01~0.10% , Sn: 0.001~0.500%, Sb: 0.001~0.500%, Pb: 0.01~0.10%, W: 0.01~0.50%.
本發明一態樣的奧氏體系不銹鋼，其相對磁導率μ較佳為1.1以下。根據前述構成，即使厚度為一定程度以上，也能夠提供一種非磁性的奧氏體系不銹鋼，其係能夠降低厚度方向上的截面硬度分布的不均勻。The austenitic stainless steel of one aspect of the present invention preferably has a relative permeability μ of 1.1 or less. According to the aforementioned configuration, even if the thickness is greater than a certain level, it is possible to provide a non-magnetic austenitic stainless steel which can reduce the unevenness of the cross-sectional hardness distribution in the thickness direction.
[4]本發明一態樣的奧氏體系不銹鋼的製造方法，其係包含：粗熱軋步驟，其係將經由連續鑄造所製造之鋼胚(slab)加熱至1000~1300℃後，施加粗熱軋，且前述鋼胚係由下述化學組成所構成：以質量%計，C：0.003~0.12%、Si：2.00%以下、Mn：2.00%以下、P：0.04%以下、S：0.030%以下、Ni：6.0~15.0%、Cr：16.0~22.0%、N：0.005~0.20%，其中，C與N的合計含量為0.08%以上，且其餘為Fe與不可避免的雜質；精緻熱軋步驟，其係於前述粗熱軋步驟後，針對所製造的鋼帶施加精緻熱軋；冷卻步驟，其係於前述精緻熱軋步驟後，使前述鋼帶冷卻；在前述精緻熱軋步驟中，前述精緻熱軋的壓下率為60%以上；前述精緻熱軋的輥直徑為300mm以上；前述精緻熱軋的溫度為600~1100℃；前述精緻熱軋的最終通過溫度為600~950℃；又，在前述冷卻步驟中，於前述精緻熱軋的最終通過溫度為750℃以上的情況下，以5℃/秒(s)以上的冷卻速度，使前述鋼帶冷卻至750℃以下。根據前述構成，即使厚度為一定程度以上，也能夠製造一種奧氏體系不銹鋼以及實現一種奧氏體系不銹鋼的製造方法，其係能夠降低厚度方向上的截面硬度分布的不均勻。[4] A method of manufacturing austenitic stainless steel according to one aspect of the present invention includes: a rough hot rolling step, which is to heat a slab manufactured through continuous casting to 1000 to 1300°C and apply Rough hot rolling, and the aforementioned steel blank system is composed of the following chemical composition: in terms of mass%, C: 0.003~0.12%, Si: 2.00% or less, Mn: 2.00% or less, P: 0.04% or less, S: 0.030 % Or less, Ni: 6.0~15.0%, Cr: 16.0~22.0%, N: 0.005~0.20%, where the total content of C and N is more than 0.08%, and the rest is Fe and inevitable impurities; fine hot rolling The step is to apply fine hot rolling to the manufactured steel strip after the aforementioned rough hot rolling step; the cooling step is to cool the aforementioned steel strip after the aforementioned fine hot rolling step; in the aforementioned fine hot rolling step, The reduction rate of the aforementioned exquisite hot rolling is more than 60%; the diameter of the aforementioned exquisite hot rolling is more than 300mm; the temperature of the aforementioned exquisite hot rolling is 600~1100°C; the final passing temperature of the aforementioned exquisite hot rolling is 600~950°C; In the cooling step, when the final passing temperature of the fine hot rolling is 750°C or higher, the steel strip is cooled to 750°C or lower at a cooling rate of 5°C/sec (s) or higher. According to the aforementioned configuration, even if the thickness is greater than a certain level, it is possible to manufacture an austenitic stainless steel and realize a method of manufacturing an austenitic stainless steel, which can reduce the unevenness of the cross-sectional hardness distribution in the thickness direction.
[5]如[4]所述之奧氏體系不銹鋼的製造方法，其中，以質量%計，前述鋼胚還進一步包含下述成分的一種或兩種以上：Mo：0.01~3.00%、Cu：0.01~3.50%、Al：0.0080%以下、O：0.0040~0.0100%、V：0.01~0.5%、B：0.001~0.01%、Ti：0.01~0.50%。[5] The method for producing austenitic stainless steel as described in [4], wherein, in terms of mass %, the steel blank further contains one or two or more of the following components: Mo: 0.01 to 3.00%, Cu : 0.01~3.50%, Al: less than 0.0080%, O: 0.0040~0.0100%, V: 0.01~0.5%, B: 0.001~0.01%, Ti: 0.01~0.50%.
[6]如[4]或[6]所述之奧氏體系不銹鋼的製造方法，其中，以質量%計，前述鋼胚還進一步包含下述成分的一種或兩種以上：Co：0.01~0.50%、Zr：0.01~0.10%、Nb：0.01~0.10%、Mg：0.0005~0.0030%、Ca：0.0003~0.0030%、Y：0.01~0.20%、稀土類金屬(REM)：0.01~0.10%、Sn：0.001~0.500%及Sb：0.001~0.500%、Pb：0.01~0.10%、W：0.01~0.50%。[6] The method for producing austenitic stainless steel as described in [4] or [6], wherein, in terms of mass %, the steel blank further contains one or two or more of the following components: Co: 0.01~ 0.50%, Zr: 0.01~0.10%, Nb: 0.01~0.10%, Mg: 0.0005~0.0030%, Ca: 0.0003~0.0030%, Y: 0.01~0.20%, rare earth metals (REM): 0.01~0.10%, Sn: 0.001~0.500%, Sb: 0.001~0.500%, Pb: 0.01~0.10%, W: 0.01~0.50%.
[發明功效] 根據本發明的一態樣，能夠產生以下效果：即使厚度為一定程度以上，也能夠提供一種奧氏體系不銹鋼，其係能夠降低厚度方向上的截面硬度分布的不均勻。[Efficacy of invention] According to one aspect of the present invention, it is possible to produce the following effect: even if the thickness is greater than a certain level, it is possible to provide an austenitic stainless steel which can reduce the unevenness of the cross-sectional hardness distribution in the thickness direction.
以下，針對本發明的一實施形態進行詳細說明。又，以下的記載係為了更方便理解本發明的意旨者，在並未特別指定的情況下，並非用於限定本發明。Hereinafter, an embodiment of the present invention will be described in detail. In addition, the following description is for making it easier to understand the meaning of the present invention, and is not intended to limit the present invention unless otherwise specified.
[本發明的要點及目的] 要點(i)：即使厚度為一定程度以上(3mm以上)，也能夠實現一種奧氏體系不銹鋼，其係能夠降低厚度方向上的截面硬度分布的不均勻；要點(ii)：本發明人們發現，若將奧氏體系不銹鋼加熱至高溫並使用大直徑的軋輥進行大幅壓下，且在壓下後的精緻熱軋的最終通過溫度為750°C以上的情況下，以5°C/秒(s)以上的冷卻速率將其冷卻至750°C以下時，在厚度為3mm以上的奧氏體系不銹鋼中，能夠降低厚度方向上的截面硬度分布的不均勻。又，本說明書所載的「奧氏體系不銹鋼」係包括奧氏體系不銹鋼鋼帶及奧氏體系不銹鋼鋼板。換言之，本發明能夠適用於奧氏體系不銹鋼鋼帶及奧氏體系不銹鋼鋼板兩者。[Gist and purpose of the present invention] Point (i): Even if the thickness is greater than a certain level (3mm or more), it is possible to realize an austenitic stainless steel, which can reduce the unevenness of the cross-sectional hardness distribution in the thickness direction; Point (ii): The present inventors found If the austenitic stainless steel is heated to a high temperature and large-diameter rolls are used for substantial reduction, and the final pass temperature of the refined hot rolling after reduction is 750°C or more, 5°C/sec (s) When it is cooled to 750°C or less at the cooling rate above, in austenitic stainless steel with a thickness of 3 mm or more, the unevenness of the cross-sectional hardness distribution in the thickness direction can be reduced. In addition, the "austenitic stainless steel" in this specification includes austenitic stainless steel strip and austenitic stainless steel steel plate. In other words, the present invention can be applied to both austenitic stainless steel strips and austenitic stainless steel steel sheets.
又，舉例來說，本發明係以實現一種奧氏體系不銹鋼及其製造方法作為目的，且前述奧氏體系不銹鋼係能夠在未施加複雜的鍛造加工而是以切削、蝕刻及放電加工等之情況下，來製造智慧手機等的電子設備的結構部件。Also, for example, the present invention aims to realize an austenitic stainless steel and its manufacturing method, and the aforementioned austenitic stainless steel can be processed by cutting, etching, and electrical discharge processing without complicated forging processing. In this case, it is used to manufacture structural parts of electronic devices such as smartphones.
(降低厚度方向上的截面硬度分布的不均勻之優點) 在將本發明實施形態的奧氏體系不銹鋼適用於作為智慧手機的結構部件之情況下，若存在較軟質的部分(例如，厚度方向上的中央部分)，則容易產生裂紋。故使其作為產品的價值變低。又，即使是軟質的部分，雖然可以藉由使它們變得充份堅硬以作為對應策略，但反過來說，若產生硬度超出必要範圍的過硬部分，則切削性下降。(The advantage of reducing the unevenness of the cross-sectional hardness distribution in the thickness direction) When the austenitic stainless steel according to the embodiment of the present invention is applied as a structural component of a smartphone, if there is a softer part (for example, the central part in the thickness direction), cracks are likely to occur. Therefore, its value as a product becomes lower. In addition, even soft parts can be made sufficiently hard as a countermeasure, but conversely, if an excessively hard part with a hardness exceeding the necessary range is generated, the machinability will decrease.
[流程] 如圖1所示，能夠經由製鋼、粗熱軋、精緻熱軋及冷卻等各步驟，來製造本發明一實施形態的奧氏體系不銹鋼。更具體而言，將經由連續鑄造所製造之鋼胚(slab)加熱至1000~1300℃後，施加粗熱軋，以形成厚度為25mm的粗條(bar)(鋼帶)(粗熱軋步驟)。之後，在600℃以上且1100℃以下的條件下，針對上述粗條施加精緻熱軋(精緻熱軋步驟)。在精緻熱軋步驟中，精緻熱軋的壓下率為60%以上，精緻熱軋的輥直徑為300mm以上，精緻熱軋的最終通過溫度為600~950℃。在精緻熱軋步驟後，於精緻熱軋的最終通過溫度為750℃以上的情況下，以5℃/秒(s)以上的冷卻速度，使製造的鋼帶冷卻至750℃以下(冷卻步驟)。藉由滿足此等條件，能夠獲得一種不銹鋼，其係具有所欲之厚度方向上的截面硬度分布及所欲之硬度分布的變動範圍。[Process] As shown in FIG. 1, the austenitic stainless steel according to an embodiment of the present invention can be manufactured through the various steps of steel making, rough hot rolling, fine hot rolling, and cooling. More specifically, the slab manufactured by continuous casting is heated to 1000 to 1300° C., and then subjected to rough hot rolling to form a bar (steel strip) with a thickness of 25 mm (rough hot rolling step) ). After that, under the conditions of 600° C. or higher and 1100° C. or lower, fine hot rolling (fine hot rolling step) is applied to the thick strip. In the fine hot rolling step, the reduction rate of the fine hot rolling is more than 60%, the diameter of the fine hot rolling roll is more than 300mm, and the final passing temperature of the fine hot rolling is 600~950°C. After the fine hot rolling step, when the final passing temperature of the fine hot rolling is 750°C or higher, the manufactured steel strip is cooled to below 750°C at a cooling rate of 5°C/sec (s) or higher (cooling step) . By satisfying these conditions, it is possible to obtain a stainless steel that has a desired cross-sectional hardness distribution in the thickness direction and a desired variation range of the hardness distribution.
又，針對獲得之不銹鋼，能夠因應必要，以去除熱軋步驟中所生成之氧化垢作為目的，來進行酸洗處理。一般來說，酸洗處理係在與退火步驟及酸洗步驟連接的退火酸洗生產線上實施的。當進行酸洗處理時，可以在不會使不銹鋼的硬度降低的溫度範圍內(具體而言，900℃以下)，針對不銹鋼施加熱量。In addition, for the obtained stainless steel, it is possible to perform pickling treatment for the purpose of removing the oxide scale generated in the hot rolling step as necessary. Generally, the pickling treatment is implemented on the annealing and pickling production line connected to the annealing step and the pickling step. When performing the pickling treatment, it is possible to apply heat to the stainless steel within a temperature range (specifically, 900° C. or lower) that does not reduce the hardness of the stainless steel.
根據以上的各步驟，即使在厚度為3mm以上的情況下，亦能夠使奧氏體系不銹鋼之厚度方向上的平均截面硬度分布為250HV以上，且變動寬度為30HV以下。因此，能夠提供一種奧氏體系不銹鋼，其係能夠降低厚度方向上的截面硬度分布的不均勻。According to the above steps, even when the thickness is 3 mm or more, the average cross-sectional hardness distribution in the thickness direction of the austenitic stainless steel can be 250 HV or more, and the variation width can be 30 HV or less. Therefore, it is possible to provide an austenitic stainless steel which can reduce the unevenness of the cross-sectional hardness distribution in the thickness direction.
(厚度方向的截面硬度分布) 厚度方向上的截面硬度分布係指，針對垂直於軋製寬度方向的截面，在1kg的荷重下，於複數個點處所測量的維氏硬度，以此而能夠理解在厚度方向上的截面硬度的變化。舉例來說，厚度為8mm且將厚度方向上的平均截面硬度調整為300HV之實施例A3的不銹鋼(參照圖4)，係具有如圖2所示之在厚度方向上的截面硬度分布為294~308HV的範圍；由此可以看出，相較於習知技術，降低了在厚度方向上的截面硬度分布的不均勻。圖2係顯示本發明一實施形態中奧氏體系不銹鋼的厚度方向上的截面硬度分布之圖。(Sectional hardness distribution in the thickness direction) The cross-sectional hardness distribution in the thickness direction refers to the Vickers hardness measured at multiple points under a load of 1 kg for a cross-section perpendicular to the rolling width direction, so that the cross-sectional hardness in the thickness direction can be understood. Variety. For example, the stainless steel of Example A3 with a thickness of 8mm and the average cross-sectional hardness in the thickness direction adjusted to 300HV (refer to FIG. 4) has a cross-sectional hardness distribution in the thickness direction as shown in FIG. 2 of 294~ The range of 308HV; it can be seen that compared with the conventional technology, the unevenness of the cross-sectional hardness distribution in the thickness direction is reduced. Fig. 2 is a diagram showing the cross-sectional hardness distribution in the thickness direction of an austenitic stainless steel in an embodiment of the present invention.
(C+N) 因為碳(C)及氮(N)對奧氏體相的固溶強化與加工硬化係產生有效的作用，故需要一定的量。作為各種探討的結果，為了穩定地獲得250HV以上的硬度，發現需要將C+N的量調整至0.08%以上(參照圖3)。又，圖3係顯示C+N的合計量與不銹鋼的厚度方向上的平均截面硬度分布的關係之圖。又，C+N量係指C及N的總含量。又，C+N的量係包括C為0%或N為0%的情況。(C+N) Because carbon (C) and nitrogen (N) have an effective effect on the solid solution strengthening and work hardening of the austenite phase, a certain amount is required. As a result of various studies, in order to stably obtain a hardness of 250 HV or more, it was found that the amount of C+N needs to be adjusted to 0.08% or more (see FIG. 3). 3 is a graph showing the relationship between the total amount of C+N and the average cross-sectional hardness distribution in the thickness direction of stainless steel. In addition, the amount of C+N refers to the total content of C and N. In addition, the amount of C+N includes the case where C is 0% or N is 0%.
圖3係顯示針對實施例A1~A4以及比較例B1、B2的平均截面硬度所繪製之圖，且前述各實施例及比較例係在870℃之精緻熱軋的最終通過溫度下進行軋製，且以40℃/s的冷卻速度冷卻至750℃以下並進行捲繞的(針對實施例A1~A4以及比較例B1、B2中各鋼種的化學組成請參照圖4)。雖然C+N的量為0.08%以上之A1~A4的平均截面硬度為250HV以上，但C+N的量小於0.08%之B1及B2鋼的平均截面硬度小於250HV。Figure 3 shows a graph drawn for the average cross-sectional hardness of Examples A1 to A4 and Comparative Examples B1 and B2, and the foregoing Examples and Comparative Examples were rolled at the final passing temperature of fine hot rolling at 870°C. And it was cooled to 750°C or less at a cooling rate of 40°C/s and wound (for the chemical composition of each steel type in Examples A1 to A4 and Comparative Examples B1 and B2, please refer to Figure 4). Although the average cross-sectional hardness of A1~A4 with a C+N content of 0.08% or more is 250HV or more, the average cross-sectional hardness of B1 and B2 steels with a C+N content of less than 0.08% is less than 250HV.
(相對磁導率) 因為在本發明實施形態的製造方法中係在600℃以上進行軋製，故雖然沒有生成經由加工所引起的馬氏體，但如果殘留δ鐵素體，則相對磁導率變高；且在本發明實施形態的製造方法中，於使奧氏體系不銹鋼具有特徵點的情況下，一般來說，相對磁導率μ較佳為1.1以下，更佳為1.05以下。(Relative permeability) Because rolling is performed at 600°C or higher in the manufacturing method of the embodiment of the present invention, although martensite caused by processing is not formed, if δ ferrite remains, the relative magnetic permeability becomes higher; and In the manufacturing method of the embodiment of the present invention, when the austenitic stainless steel has characteristic points, in general, the relative magnetic permeability μ is preferably 1.1 or less, and more preferably 1.05 or less.
因為調整成上述化學組成之奧氏體系不銹鋼，在一般的鋼板製造步驟及其後的冷鍛步驟中不會生成馬氏體相，故能夠避免起因於加工引起之馬氏體相所導致的磁性化。然而，因為有在熔化製造時的高溫下生成δ-鐵素體相之情形，且如果其殘留，則無法獲得磁導率為1.010以下的非磁性者。又，如果將δ鐵素體相作為不同相而混合在產品中，則可能會損害鏡面研磨產品的外觀。因此，有必要在作為冷鍛用原料的鋼板階段使δ鐵素體相消失。因為δ鐵素體相係具有強磁性的，故藉由磁導率來評價其存在。Because the austenitic stainless steel adjusted to the above chemical composition does not form a martensite phase in the general steel plate manufacturing process and the subsequent cold forging process, it is possible to avoid the martensite phase caused by processing. Magnetized. However, because there are cases where the δ-ferrite phase is formed at a high temperature during melting and manufacturing, and if it remains, a non-magnetic one with a permeability of 1.010 or less cannot be obtained. In addition, if the δ ferrite phase is mixed in the product as a different phase, the appearance of the mirror polished product may be impaired. Therefore, it is necessary to eliminate the delta ferrite phase at the stage of the steel sheet as a raw material for cold forging. Because the delta ferrite phase is ferromagnetic, its existence is evaluated by its magnetic permeability.
(目標特性) 奧氏體系不銹鋼的厚度方向上的平均截面硬度分布係期望在250HV以上(SUS304CSP-1/2H的規格)。又，舉例來說，因為特殊金屬Excel公司製的SUS301CSP的厚度範圍為2.5mm以下左右，故奧氏體系不銹鋼的厚度係期望在3mm以上。(Target characteristics) The average cross-sectional hardness distribution in the thickness direction of the austenitic stainless steel is desirably 250 HV or more (standard of SUS304CSP-1/2H). Also, for example, since the thickness range of SUS301CSP manufactured by Special Metal Excel Corporation is approximately 2.5 mm or less, the thickness of austenitic stainless steel is desirably 3 mm or more.
(壓下率) 精緻熱軋的壓下率較佳係60%以上。如圖6中的條件No. D001~D006所示般，當精緻熱軋的壓下率(總軋製率)小於60%時，無法充分地賦予軋製應變，故無法獲得目標平均截面硬度。又，當軋製輥的入口的厚度為h1且出口的厚度為h2時，成立了壓下率＝(h1-h2)/h1的關係式。(Reduction rate) The reduction rate of fine hot rolling is preferably above 60%. As shown in condition Nos. D001 to D006 in Fig. 6, when the reduction ratio (total rolling ratio) of fine hot rolling is less than 60%, the rolling strain cannot be sufficiently imparted, and the target average cross-sectional hardness cannot be obtained. In addition, when the thickness of the entrance of the rolling roll is h1 and the thickness of the exit is h2, the relational expression of reduction ratio=(h1-h2)/h1 is established.
(輥直徑) 精緻熱軋的輥直徑較佳係300mm以上。如圖6中的條件No. F01~F19所示般，當輥直徑較小時，無法賦予軋製應變至厚度方向的中心為止，故在任何的軋製溫度中，截面硬度的變動範圍變大。又，輥直徑係指垂直於軋製輥的旋轉軸之截面的直徑。(Roller diameter) The diameter of the fine hot rolling roll is preferably 300mm or more. As shown in condition Nos. F01 to F19 in Fig. 6, when the roll diameter is small, the rolling strain cannot be imparted to the center of the thickness direction, so at any rolling temperature, the variation range of the cross-sectional hardness increases. . In addition, the roll diameter refers to the diameter of the cross section perpendicular to the rotation axis of the rolling roll.
(精緻熱軋的溫度及精緻熱軋的最終通過溫度) 精緻熱軋的溫度較佳係600~1100℃。又，精緻熱軋的最終通過溫度(最終通過軋製溫度)較佳係600~950℃。當精緻熱軋的溫度及最終通過溫度小於600℃時，即使輥直徑變大，且相較於厚度方向的中心施加於板表層的應變量變大，而使截面硬度的變動範圍變大。另一方面，當精緻熱軋的溫度大於1100℃時，軋製應變成為再結晶的驅動力，且在軋製後立即產生再結晶而無法獲得期望的截面硬度分布，同時，溫度過高而難以將最終通過軋製溫度調整至950℃以下。又，當最終通過軋製溫度大於950℃時，軋製應變成為再結晶的驅動力，在軋製後立即產生再結晶而無法獲得期望的截面硬度分布。(The temperature of exquisite hot rolling and the final passing temperature of exquisite hot rolling) The temperature of fine hot rolling is preferably 600~1100°C. In addition, the final passing temperature (final passing rolling temperature) of the fine hot rolling is preferably 600 to 950°C. When the temperature of fine hot rolling and the final passing temperature are less than 600°C, even if the roll diameter becomes larger, the amount of strain applied to the surface layer of the plate becomes larger than the center of the thickness direction, and the variation range of the section hardness becomes larger. On the other hand, when the temperature of fine hot rolling is greater than 1100°C, the rolling strain becomes the driving force for recrystallization, and recrystallization occurs immediately after rolling and the desired cross-sectional hardness distribution cannot be obtained. At the same time, the temperature is too high to be difficult. The final rolling temperature is adjusted to 950°C or lower. In addition, when the final passing rolling temperature exceeds 950°C, the rolling strain becomes the driving force for recrystallization, and recrystallization occurs immediately after rolling, and the desired cross-sectional hardness distribution cannot be obtained.
(冷卻步驟) 於施加精緻熱軋後的鋼帶之精緻熱軋的最終通過溫度為750℃以上的情況下，較佳係在前述精緻熱軋步驟後實施冷卻步驟，其係以5℃/s以上的冷卻速度，使前述鋼帶冷卻至750℃以下。當不銹鋼保持在高溫的情況下，在精緻熱軋過程的材料中所累積的軋製應變係自精緻熱軋後立即減少。為了降低軋製應變的減少，較佳係迅速地冷卻至不會產生軋製應變的減少之溫度範圍。(Cooling step) When the final passing temperature of the fine hot rolling of the steel strip after the fine hot rolling is 750°C or higher, it is preferable to implement the cooling step after the aforementioned fine hot rolling step, which is at a cooling rate of 5°C/s or higher , The aforementioned steel strip is cooled to below 750°C. When stainless steel is kept at a high temperature, the rolling strain accumulated in the material in the delicate hot rolling process decreases immediately after the delicate hot rolling. In order to reduce the reduction in rolling strain, it is preferable to quickly cool to a temperature range where the reduction in rolling strain does not occur.
圖5係顯示本發明實施例的奧氏體系不銹鋼的物性等之圖。又，圖6及圖7係顯示比較例的奧氏體系不銹鋼的物性等之圖。又，圖5、圖6及圖7中的軋製溫度係進行軋製時鋼板的溫度。如圖5所示，滿足上述製造方法的條件之No. C01~C25的製造方法所製造之奧氏體系不銹鋼，其厚度方向上的平均截面硬度分布為250HV以上，且截面硬度分布的變動範圍為30HV以下。另一方面，如圖6及圖7所示，未滿足上述製造方法的條件(具體而言，板厚、輥直徑、C+N的量及冷卻速度等條件中的至少一者未滿足上述製造方法的條件)之No. D01~H06的製造方法所製造之奧氏體系不銹鋼，其厚度方向上的平均截面硬度分布小於250HV及/或截面硬度分布的變動範圍大於30HV。Fig. 5 is a graph showing the physical properties and the like of the austenitic stainless steel according to the embodiment of the present invention. 6 and 7 are graphs showing the physical properties of the austenitic stainless steel of the comparative example. In addition, the rolling temperature in FIG. 5, FIG. 6, and FIG. 7 is the temperature of the steel sheet when rolling is performed. As shown in Figure 5, the austenitic stainless steel manufactured by the manufacturing method of No. C01~C25 that meets the conditions of the above manufacturing method has an average cross-sectional hardness distribution in the thickness direction of 250HV or more, and the variation range of the cross-sectional hardness distribution Below 30HV. On the other hand, as shown in FIGS. 6 and 7, the conditions of the above-mentioned manufacturing method (specifically, at least one of the plate thickness, roll diameter, amount of C+N, and cooling rate) is not satisfied. Method condition) The austenitic stainless steel manufactured by the manufacturing methods of No. D01~H06 has an average cross-sectional hardness distribution in the thickness direction of less than 250HV and/or the variation range of the cross-sectional hardness distribution is greater than 30HV.
(鋼的化學組成) 本發明一實施形態的奧氏體系不銹鋼的化學組成係包括：以質量%計，C：0.003~0.12%、Si：2.00%以下、Mn：2.00%以下、P：0.04%以下、S：0.030%以下、Ni：6.0~15.0%、Cr：16.0~22.0%、N：0.005~0.20%以及其餘為Fe與不可避免的雜質。以下，在未特別限定的情況下，鋼組成中的「%」係指質量%。(Chemical composition of steel) The chemical composition system of the austenitic stainless steel according to an embodiment of the present invention includes: C: 0.003~0.12%, Si: 2.00% or less, Mn: 2.00% or less, P: 0.04% or less, S: 0.030 in mass% % Or less, Ni: 6.0~15.0%, Cr: 16.0~22.0%, N: 0.005~0.20%, and the rest are Fe and unavoidable impurities. Hereinafter, unless specifically limited, the "%" in the steel composition means mass %.
在本發明一實施形態的奧氏體系不銹鋼中，在前述化學組成的基礎上，以質量%計，還可包含下述成分的一種或兩種以上：Mo：0.01~3.00%、Cu：0.01~3.50%、Al：0.0080%以下、O：0.0040~0.0100%、V：0.01~0.5%、B：0.001~0.01%、Ti：0.01~0.50%。In the austenitic stainless steel of one embodiment of the present invention, based on the aforementioned chemical composition, in terms of mass %, one or more of the following components may be included: Mo: 0.01 to 3.00%, Cu: 0.01 ~3.50%, Al: less than 0.0080%, O: 0.0040~0.0100%, V: 0.01~0.5%, B: 0.001~0.01%, Ti: 0.01~0.50%.
在本發明一實施形態的奧氏體系不銹鋼中，作為可任意添加的成分，以質量%計，還包含下述成分的一種或兩種以上：Co：0.01~0.50%、Zr：0.01~0.10%、Nb：0.01~0.10%、Mg：0.0005~0.0030%、Ca：0.0003~0.0030%、Y：0.01~0.20%、稀土類金屬(REM)：0.01~0.10%、Sn：0.001~0.500%及Sb：0.001~0.500%、Pb：0.01~0.10%、W：0.01~0.50%。In the austenitic stainless steel according to an embodiment of the present invention, as a component that can be added arbitrarily, one or two or more of the following components are included in terms of mass %: Co: 0.01 to 0.50%, Zr: 0.01 to 0.10 %, Nb: 0.01~0.10%, Mg: 0.0005~0.0030%, Ca: 0.0003~0.0030%, Y: 0.01~0.20%, rare earth metals (REM): 0.01~0.10%, Sn: 0.001~0.500% and Sb : 0.001~0.500%, Pb: 0.01~0.10%, W: 0.01~0.50%.
碳(C)是間隙元素，並且藉由加工硬化及應變時效而有助於使材料高強度化。又，碳也是穩定奧氏體相並有效地保持非磁性的元素。在本發明中，確保C含量為0.003%以上。然而，過量的C會成為使鋼硬化並使冷鍛性降低的因素。C含量被限制在0.012%以下。Carbon (C) is an interstitial element and contributes to high strength of the material through work hardening and strain aging. In addition, carbon is also an element that stabilizes the austenite phase and effectively maintains non-magnetic properties. In the present invention, it is ensured that the C content is 0.003% or more. However, excessive C becomes a factor that hardens steel and lowers cold forgeability. The C content is limited to 0.012% or less.
矽(Si)是在製鋼過程中作為鋼的脫氧劑來使用之元素。在去除應變的熱處理中，Si具有提升時效硬化性的作用。另一方面，因為Si具有大的固溶強化作用，且還具有降低堆垛層錯能量(stacking fault energy)以提升加工硬化的作用，故過量的Si成為冷鍛性降低的因素。因此，Si含量被限制在2.0%以下。Silicon (Si) is an element used as a deoxidizer for steel in the steel making process. In the heat treatment to remove strain, Si has the effect of improving age hardenability. On the other hand, because Si has a large solid solution strengthening effect, and also has the effect of reducing stacking fault energy to improve work hardening, excessive Si becomes a factor in reducing cold forgeability. Therefore, the Si content is limited to 2.0% or less.
錳(Mn)係作為MnO來形成氧化物系夾雜物的元素。又，Mn具有小的固溶強化作用且為奧氏體生成元素，並且具有抑制加工所引起之馬氏體相變的作用，故錳係確保冷鍛性及有效地維持非磁性的元素。然而，過量的Mn會成為耐腐蝕性降低的因素。Mn含量被限制在2.00%以下。Manganese (Mn) is an element that forms oxide-based inclusions as MnO. In addition, Mn has a small solid solution strengthening effect, is an austenite-forming element, and has an effect of suppressing martensite transformation caused by working, so the manganese-based element ensures cold forgeability and effectively maintains non-magnetic properties. However, excessive Mn can become a factor in the reduction of corrosion resistance. The Mn content is limited to 2.00% or less.
磷(P)係為使耐腐蝕性下降的元素，且因為過度地降低P含量會成為製鋼負荷增加的因素，故其必須為0.040%以下。Phosphorus (P) is an element that lowers the corrosion resistance, and because excessively reducing the P content will cause an increase in the steelmaking load, it must be 0.040% or less.
硫(S)係形成MnS並成為使耐腐蝕性降低的因素，且過度地脫硫(S)會成為製鋼負荷增加的因素，故其被限制為0.030%以下。Sulfur (S) forms MnS and becomes a factor that reduces corrosion resistance, and excessive desulfurization (S) becomes a factor that increases steelmaking load, so it is limited to 0.030% or less.
鉻(Cr)係提升耐腐蝕性的元素。為了確保適用於攜帶型電子設備的外包裝部件之耐腐蝕性，在本發明中係以Cr含量為16.0%以上的鋼作為對象。然而，大量的Cr會成為冷鍛性降低的因素。Cr含量的上限值被限制為22.0%。Chromium (Cr) is an element that improves corrosion resistance. In order to ensure the corrosion resistance of outer packaging parts suitable for portable electronic devices, steel with a Cr content of 16.0% or more is used as the object in the present invention. However, a large amount of Cr can become a factor of lowering cold forgeability. The upper limit of the Cr content is limited to 22.0%.
氮(N)與C相同，也是間隙元素，且藉由加工硬化及應變時效而有助於使材料高強度化。又，氮也是穩定奧氏體相並有效地保持非磁性的元素。在本發明中，確保N含量為0.005%以上。然而，過量的N會成為使鋼硬化並使冷鍛性降低的因素。N含量被限制在0.20%以下。Nitrogen (N), like C, is also an interstitial element, and contributes to higher strength of the material through work hardening and strain aging. In addition, nitrogen is also an element that stabilizes the austenite phase and effectively maintains non-magnetic properties. In the present invention, it is ensured that the N content is 0.005% or more. However, excessive N becomes a factor that hardens steel and lowers cold forgeability. The N content is limited to less than 0.20%.
鉬(Mo)係有效地提高不銹鋼的耐腐蝕性之元素。在本發明中，在確保前述Cr含量的情況下，因應必要來添加鉬；但是，由於大量添加Mo會導致成本增加，故在含有Mo的情況下，Mo含量為0.01%~3.00%以下。Molybdenum (Mo) is an element that effectively improves the corrosion resistance of stainless steel. In the present invention, when the aforementioned Cr content is ensured, molybdenum is added as necessary; however, since adding a large amount of Mo will increase the cost, when Mo is contained, the Mo content is 0.01% to 3.00% or less.
眾所周知，銅(Cu)係抑制奧氏體相的加工硬化並有效地提升冷鍛性製之元素。又，在冷鍛後所進行之去除應變的熱處理的加熱溫度範圍內，銅係引起時效硬化的元素。作為各種探討的結果，當含有Cu時，Cu含量為0.01%~3.5%。As we all know, copper (Cu) is an element that inhibits the work hardening of the austenite phase and effectively improves the cold forgeability. In addition, in the heating temperature range of the heat treatment to remove strain after cold forging, copper is an element that causes age hardening. As a result of various investigations, when Cu is contained, the Cu content is 0.01% to 3.5%.
鋁(Al)具有比Si及Mn更高的氧親和力，且當Al含量為0.0030%以上時，變得容易形成作為冷鍛中的內部裂紋的起點之粗大氧化物系夾雜物。又，因為過度地降低Al含量會導致成本增加，故作為各種探討的結果，當含有Al時，Al含量為0.0001%以上~0.0080%。Aluminum (Al) has a higher oxygen affinity than Si and Mn, and when the Al content is 0.0030% or more, it becomes easy to form coarse oxide-based inclusions that are the starting points of internal cracks in cold forging. In addition, since excessively reducing the Al content leads to an increase in cost, as a result of various studies, when Al is contained, the Al content is 0.0001% or more to 0.0080%.
當氧(O)含量低時，Mn及Si等變得難以被氧化，且在夾雜物中Al2 O3 的比例變高。又，若O的含量過高，則容易形成粒徑大於5μm的粗大夾雜物，故在經過各種探討的結果，當含有O時，O含量為40ppm(0.0040%)~100ppm(0.0100%)，較佳係80ppm以下。When the oxygen (O) content is low, Mn, Si, etc. become difficult to be oxidized, and the proportion of Al 2 O 3 in the inclusions becomes higher. In addition, if the O content is too high, coarse inclusions with a particle size greater than 5 μm are likely to be formed. Therefore, after various investigations, the O content is 40 ppm (0.0040%) to 100 ppm (0.0100%) when O is contained. The best is below 80ppm.
吾人確認到，在冷鍛後所進行之去除應變的熱處理的加熱中，釩(V)具有提高時效硬化能力的作用。雖然釩具有時效硬化作用，但是大量的V會導致成本增加。當含有V時，V含量為0.01%~0.05%。We have confirmed that vanadium (V) has the effect of improving the age hardening ability in the heating of the heat treatment to remove strain after cold forging. Although vanadium has an age-hardening effect, a large amount of V will increase the cost. When V is contained, the content of V is 0.01%~0.05%.
大量的硼(B)係成為因硼化物的生成所導致之加工性下降的因素。因此，當含有B時，B含量為0.001~0.0100%，較佳為0.0050%以下。A large amount of boron (B) is a factor in the decrease in workability due to the formation of boride. Therefore, when B is contained, the B content is 0.001 to 0.0100%, preferably 0.0050% or less.
鈦(Ti)係碳氮化物的形成元素，其固定C及N，並抑制因為敏化所引起的耐腐蝕性下降。當Ti含量為0.01%以上時，能夠發揮上述效果。因此，Ti含量為0.01%以上。另一方面，當Ti含量大於0.50%時，Ti係作為碳化物且以不均勻的尺寸在鋼中不均勻地局部析出，此係妨礙了再結晶晶粒的均勻晶粒生長且使成本變高，故Ti含量的上限值為0.50%。Titanium (Ti) is a carbonitride forming element that fixes C and N and suppresses the deterioration of corrosion resistance caused by sensitization. When the Ti content is 0.01% or more, the above-mentioned effects can be exerted. Therefore, the Ti content is 0.01% or more. On the other hand, when the Ti content is greater than 0.50%, the Ti system acts as a carbide and is unevenly localized in the steel with an uneven size. This system prevents the uniform grain growth of the recrystallized grains and increases the cost. , So the upper limit of Ti content is 0.50%.
鈷(Co)係具有提升耐縫隙間腐蝕性的作用。另一方面，若Co的含量過多，則鋼會硬化且彎曲性會受到不良影響。因此，當含有Co時，Co含量為0.01~0.50%，較佳為0.10%以下。Cobalt (Co) has the effect of improving the resistance to crevice corrosion. On the other hand, if the content of Co is too large, the steel will harden and the bendability will be adversely affected. Therefore, when Co is contained, the Co content is 0.01 to 0.50%, preferably 0.10% or less.
鋯(Zr)係與C及N具有高親和力的元素，且在熱軋時，鋯係以碳化物或氮化物的形式析出並減少母相(parent phase)中的固溶體C及固溶體N，而具有提升加工性的效果。另一方面，如果Zr的含量過多，則鋼會硬化且彎曲性受到不良影響。因此，含有Zr時，Zr含量為0.01~0.10%，較佳為0.05%以下。Zirconium (Zr) is an element with high affinity for C and N, and during hot rolling, zirconium is precipitated in the form of carbides or nitrides and reduces the solid solution C and solid solution in the parent phase N, and has the effect of improving processability. On the other hand, if the content of Zr is too large, the steel will harden and bendability will be adversely affected. Therefore, when Zr is contained, the Zr content is 0.01 to 0.10%, preferably 0.05% or less.
鈮(Nb)係與C和N具有高親和性的元素，且在熱軋時，鈮以碳化物或氮化物的形式析出並減少母相中的固溶體C及固溶體N，而具有提升加工性的效果。另一方面，如果Nb的含量過多，則鋼會硬化且彎曲性受到不良影響。因此，當含有Nb時，Nb含量為0.01~0.10%，較佳為0.05%以下。Niobium (Nb) is an element with high affinity for C and N, and during hot rolling, niobium precipitates in the form of carbides or nitrides and reduces the solid solution C and solid solution N in the parent phase, and has The effect of improving processability. On the other hand, if the Nb content is too large, the steel will harden and the bendability will be adversely affected. Therefore, when Nb is contained, the Nb content is 0.01 to 0.10%, preferably 0.05% or less.
鎂(Mg)與熔鋼中的Al一起形成Mg氧化物，且鎂作為脫氧劑來產生作用。另一方面，如果Mg的含量過多，則鋼的韌性下降且製造性下降。因此，當含有Mg時，Mg含量為0.0005~0.0030%，較佳為0.0020%以下。Magnesium (Mg) forms Mg oxide together with Al in molten steel, and magnesium acts as a deoxidizer. On the other hand, if the content of Mg is too large, the toughness of the steel decreases and the manufacturability decreases. Therefore, when Mg is contained, the Mg content is 0.0005 to 0.0030%, preferably 0.0020% or less.
鈣(Ca)係提升熱加工性的元素。另一方面，如果Ca的含量過多，則鋼的韌性下降且製造性下降，同時，CaS的析出會使耐腐蝕性降低。因此，當含有Ca時，Ca含量為0.0003~0.0030%，較佳為0.0020%以下。Calcium (Ca) is an element that improves hot workability. On the other hand, if the content of Ca is too large, the toughness of the steel decreases and the manufacturability decreases, and at the same time, the precipitation of CaS decreases the corrosion resistance. Therefore, when Ca is contained, the Ca content is 0.0003 to 0.0030%, preferably 0.0020% or less.
釔(Y)係減少熔鋼的黏度下降並提高清潔度的元素。另一方面，如果Y的含量過多，則其效果飽和，且加工性下降。因此，當含有Y時，Y含量為0.01~0.20%，較佳為0.10%以下。Yttrium (Y) is an element that reduces the viscosity drop of molten steel and improves cleanliness. On the other hand, if the content of Y is too large, the effect is saturated and workability is reduced. Therefore, when Y is contained, the Y content is 0.01 to 0.20%, preferably 0.10% or less.
REM(稀土類金屬：鑭(La)、鈰(Ce)、釹(Nd)等原子序號為57~71的元素)係提升耐高溫氧化性的元素。另一方面，如果REM的含量過多，則其效果飽和，且會在熱軋時產生表面缺陷，進而導致製造性下降。因此，當包含REM時，REM含量為0.01~0.10%，較佳為0.05%以下。REM (rare earth metals: lanthanum (La), cerium (Ce), neodymium (Nd) and other elements with atomic numbers 57 to 71) is an element that improves high temperature oxidation resistance. On the other hand, if the content of REM is too large, the effect will be saturated, and surface defects will be generated during hot rolling, resulting in a decrease in manufacturability. Therefore, when REM is included, the REM content is 0.01 to 0.10%, preferably 0.05% or less.
錫(Sn)係藉由促進軋製時變形區域的產生，而有效地提升加工性。另一方面，如果Sn的含量過多，則其效果飽和，且加工性下降。因此，當含有Sn時，Sn含量為0.001~0.500%，較佳為0.200%以下。Tin (Sn) promotes the generation of deformed regions during rolling, thereby effectively improving workability. On the other hand, if the content of Sn is too large, the effect is saturated and workability is reduced. Therefore, when Sn is contained, the Sn content is 0.001 to 0.500%, preferably 0.200% or less.
銻(Sb)係藉由促進軋製時變形區域的產生，而有效地提升加工性。另一方面，如果Sb的含量過多，則其效果飽和，且加工性下降。因此，當含有Sb時，Sb含量為0.001~0.500%，較佳為0.200%以下。Antimony (Sb) promotes the formation of deformed regions during rolling, thereby effectively improving workability. On the other hand, if the content of Sb is too large, the effect is saturated and workability is reduced. Therefore, when Sb is contained, the Sb content is 0.001 to 0.500%, preferably 0.200% or less.
因為鉛(Pb)係降低晶界的熔點及晶界的結合力，且具有基於晶界的熔融而引起例如液化裂紋等的熱加工性劣化之擔憂，故將其設定為0.10%以下。The lead (Pb) system lowers the melting point of the grain boundary and the bonding force of the grain boundary, and the melting of the grain boundary may cause deterioration of hot workability such as liquefaction cracking, so it is set to 0.10% or less.
鎢(W)具有在不損害室溫的延展性之情況下提升高溫強度的作用。然而，過量添加鎢會導致形成粗大的共晶碳化物並導致延展性的下降，故其添加量為0.50以下。Tungsten (W) has the effect of improving high-temperature strength without compromising ductility at room temperature. However, excessive addition of tungsten will result in the formation of coarse eutectic carbides and a decrease in ductility, so the addition amount is 0.50 or less.
[附記事項] 本發明並不限於上述各實施形態，於請求項所示範圍內可進行各種變更，且將不同實施形態中所分別揭示的技術手段適當地組合後所獲得之實施形態亦包含在本發明的技術範圍內。又，能夠藉由組合各實施形態所個別揭示的技術手段，來形成新穎的技術特徵。[Additional matters] The present invention is not limited to the above-mentioned embodiments, various changes can be made within the scope shown in the claim, and the embodiments obtained by appropriately combining the technical means disclosed in the different embodiments are also included in the technology of the present invention. Within range. In addition, it is possible to form novel technical features by combining the technical means separately disclosed in each embodiment.
[產業利用性] 本發明係能夠應用於例如智慧手機等電子設備的結構部件、鋼帶(Steel belt)、壓板(Press plate)等；且本發明適合於需要具有相對較大的厚度之高強度不銹鋼的應用，例如奧氏體系不銹鋼鋼帶等。[Industrial Utilization] The present invention can be applied to structural parts, steel belts, press plates, etc. of electronic devices such as smart phones; and the present invention is suitable for applications that require high-strength stainless steel with a relatively large thickness, such as Austenitic stainless steel strip, etc.
無。no.
[圖1]係顯示本發明一實施形態中奧氏體系不銹鋼的製造方法的各步驟流程之工程圖。 [圖2]係顯示本發明一實施形態中奧氏體系不銹鋼的厚度方向上的截面硬度分布之圖。 [圖3]係顯示碳(C)+氮(N)的合計量與不銹鋼的厚度方向上的平均截面硬度分布的關係之圖。 [圖4]係顯示針對奧氏體系不銹鋼的化學成分，本發明的實施例與比較例的比較結果之圖。 [圖5]係顯示本發明實施例的奧氏體系不銹鋼的物性等之圖。 [圖6]係顯示比較例的奧氏體系不銹鋼的物性等之圖。 [圖7]係顯示比較例的奧氏體系不銹鋼的物性等之圖。 [圖8]係顯示習知的奧氏體系不銹鋼的厚度方向上的截面硬度分布之圖。[Fig. 1] is an engineering diagram showing the flow of each step of a method of manufacturing austenitic stainless steel in an embodiment of the present invention. Fig. 2 is a diagram showing the cross-sectional hardness distribution in the thickness direction of an austenitic stainless steel in an embodiment of the present invention. Fig. 3 is a graph showing the relationship between the total amount of carbon (C) + nitrogen (N) and the average cross-sectional hardness distribution in the thickness direction of stainless steel. Fig. 4 is a graph showing the results of comparison between the examples of the present invention and the comparative examples with respect to the chemical composition of austenitic stainless steel. [Fig. 5] A diagram showing the physical properties and the like of the austenitic stainless steel in the example of the present invention. [Fig. 6] is a graph showing the physical properties and the like of the austenitic stainless steel of the comparative example. [Fig. 7] A diagram showing the physical properties and the like of the austenitic stainless steel of the comparative example. [Fig. 8] is a diagram showing the cross-sectional hardness distribution in the thickness direction of a conventional austenitic stainless steel.
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