EP4343013A1 - Austenitic stainless steel and manufacturing method thereof - Google Patents
Austenitic stainless steel and manufacturing method thereof Download PDFInfo
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- EP4343013A1 EP4343013A1 EP22828661.3A EP22828661A EP4343013A1 EP 4343013 A1 EP4343013 A1 EP 4343013A1 EP 22828661 A EP22828661 A EP 22828661A EP 4343013 A1 EP4343013 A1 EP 4343013A1
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- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 30
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 238000005452 bending Methods 0.000 claims abstract description 23
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 16
- 230000003746 surface roughness Effects 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 238000000137 annealing Methods 0.000 claims description 20
- 238000000034 method Methods 0.000 claims description 18
- 229910000831 Steel Inorganic materials 0.000 claims description 14
- 239000010959 steel Substances 0.000 claims description 14
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 claims description 12
- 238000005098 hot rolling Methods 0.000 claims description 8
- 238000005097 cold rolling Methods 0.000 claims description 7
- 239000011780 sodium chloride Substances 0.000 claims description 6
- 239000010960 cold rolled steel Substances 0.000 claims description 5
- 230000000052 comparative effect Effects 0.000 description 43
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 20
- 239000011572 manganese Substances 0.000 description 19
- 239000010955 niobium Substances 0.000 description 18
- 239000011651 chromium Substances 0.000 description 12
- 239000000463 material Substances 0.000 description 10
- 238000005275 alloying Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 229910001220 stainless steel Inorganic materials 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 235000019592 roughness Nutrition 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 5
- 230000002542 deteriorative effect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000001887 electron backscatter diffraction Methods 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 101001112005 Homo sapiens N-acyl-phosphatidylethanolamine-hydrolyzing phospholipase D Proteins 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 102100023896 N-acyl-phosphatidylethanolamine-hydrolyzing phospholipase D Human genes 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 208000003443 Unconsciousness Diseases 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
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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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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- 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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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- 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
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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
- C21D8/0273—Final recrystallisation annealing
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Definitions
- the present disclosure relates to an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method thereof.
- austenitic stainless steels have been applied for various uses to manufacture components for transportation and construction due to excellent formability, work hardenability, and weldability.
- 304 series stainless steels or 301 series stainless steels have low yield strengths of 200 to 350 MPa, there are limits to apply these stainless steels to structural materials.
- a skin pass rolling process is generally conducted to increase yield strength of 300 series stainless steels for common use.
- the skin pass rolling process may cause problems in increasing manufacturing costs and significantly deteriorating elongation of materials.
- Patent Document 0001 discloses a method of performing heat treatment for a long time over 48 hours in a temperature range of 600 to 700°C to obtain an average grain size of 10 ⁇ m or less.
- the method disclosed in Patent Document 0001 may cause problems of deteriorating productivity in the case of implementing the method in an actual production line and increasing manufacturing costs.
- Patent Document 0001 Japanese Patent Laid-open Publication No. 2020-050940A (Publication Date: April 2, 2020 )
- an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method thereof by presenting a ultra-fine grain manufacturing technology that realizes bending formability and sound surface properties in the bent portion.
- an austenitic stainless steel includes, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, wherein an average grain size (d) of a central portion in a thickness direction is 5 ⁇ m or less, and a martensite area fraction measured in a bent portion after a 180° bending test may be 10% or less.
- the austenitic stainless steel according to an embodiment of the present disclosure may have a center line average height Ra of 0.5 ⁇ m or less and a ten point average roughness Rz of 3 ⁇ m or less in the bent portion as surface roughness.
- the austenitic stainless steel according to an embodiment of the present disclosure may have a pitting potential of 250 mV or more when measured by a 3.5% NaCl solution at 30°C.
- a method of manufacturing an austenitic stainless steel includes hot rolling a slab including, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, cold rolling the hot-rolled steel sheet at room temperature, and cold annealing the cold-rolled steel sheet to satisfy a ⁇ value represented by Equation (1) below to at least -10 but not more than 10.
- ⁇ 406 ⁇ 2127 ⁇ C ⁇ 26.2 ⁇ Mn ⁇ 31.5 ⁇ Ni ⁇ 127 ⁇ N ⁇ 48.2 ⁇ Nb ⁇ 0.108 ⁇ Temp
- Equation (1) [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C).
- the cold rolling may be performed after the hot rolling without performing hot annealing.
- an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a method of manufacturing the same may be provided by applying a ultra-fine grain manufacturing technology that realizes bending formability and sound surface properties in the bent portion.
- An austenitic stainless steel may include, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, wherein an average grain size (d) of a central portion in a thickness direction may be 5 ⁇ m or less, and a martensite area fraction measured in the bent portion after a 180° bending test may be 10% or less.
- An austenitic stainless steel may include, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities.
- the content of carbon (C) may be from 0.005 to 0.03%.
- C is an austenite phase-stabilizing element.
- C may be added in an amount of 0.005% or more.
- an excess of C may cause a problem of forming a chromium carbide during low-temperature annealing to deteriorate grain boundary corrosion resistance.
- an upper limit of the C content may be controlled to 0.03 wt%.
- the content of silicon (Si) may be from 0.1 to 1.0%.
- Si is an element added as a deoxidizer during a steel-making process and has an effect on improving corrosion resistance of a steel by forming an Si oxide in a passivated layer in the case of performing a bright annealing process.
- Si may be added in an amount of 0.1 wt% or more.
- an excess of Si may cause a problem of deteriorating ductility.
- an upper limit of the Si content may be controlled to 1.0 wt%.
- the content of manganese (Mn) may be from 0.1 to 2.0%.
- Mn is an austenite phase-stabilizing element.
- Mn may be added in an amount of 0.1% or more.
- an excess of Mn may cause a problem of deteriorating corrosion resistance.
- an upper limit of the Mn content may be controlled to 2.0%.
- the content of nickel (Ni) may be from 6.0 to 12.0%.
- Ni is an austenite phase-stabilizing element and has an effect on softening a steel material.
- Ni may be added in an amount of 6.0% or more.
- an excess of Ni may cause a problem of increasing manufacturing costs.
- an upper limit of Ni may be controlled to 12.0%.
- the content of chromium (Cr) may be from 16.0 to 20.0%.
- Cr is a major element for improving corrosion resistance of a stainless steel.
- Cr may be added in an amount of 16.0 wt% or more.
- an excess of Cr may cause problems of hardening a steel material and inhibiting strain-induced martensite transformation during cold rolling.
- an upper limit of the Cr content may be controlled to 20.0%.
- the content of nitrogen (N) may be from 0.01 to 0.2%.
- N is an austenite phase-stabilizing element and enhances strength of a steel material.
- N may be added in an amount of 0.01% or more.
- an excess of N may cause problems such as hardening of a steel material and deterioration of hot workability.
- an upper limit of the N content may be controlled to 0.2%.
- the content of niobium (Nb) may be from 0.25% or less. Addition of Nb that induces formation of Nb-based Z-phase precipitates has an effect on inhibiting the growth of crystal grains. However, an excess of Nb may cause a problem of increasing manufacturing costs. In consideration thereof, an upper limit of the Nb content may be controlled to 0.25%.
- the remaining component of the composition of the present disclosure is iron (Fe).
- the composition may include unintended impurities inevitably incorporated from raw materials or surrounding environments, and thus addition of other alloy components is not excluded.
- the impurities are not specifically mentioned in the present disclosure, as they are known to any person skilled in the art of manufacturing.
- the average grain size (d) of a central portion in a thickness direction may be 5 ⁇ m or less, and a martensite area fraction measured in the bent portion after a 180° bending test may be 10% or less.
- a method of promoting TRIP transformation to transform an austenite phase to a martensite phase is used to implement a ultra-fine grain microstructure.
- an amount of strain-induced martensite transformation increases during cold deformation.
- a hardness of a material increases, and surface properties of a processed portion may deteriorate in the case of processing the material.
- a ultra-fine grain microstructure may be implemented and a martensite area fraction measured in a bent portion may be reduced, so that an austenitic stainless steel with excellent surface properties may be provided.
- the austenitic stainless steel according to an embodiment of the present disclosure may have a center line average height Ra of 0.5 ⁇ m or less and a ten point average roughness Rz of 3 ⁇ m or less in a bent portion after a 180° bending test.
- the 180° bending test may be performed by setting a curvature R value of a bent portion to be identical to a thickness of a material and conducting a bending process once.
- the pitting potential is a critical potential at which corrosion occurs in the form of holes in a passivated metal material
- the austenitic stainless steel according to an embodiment of the present disclosure may have a pitting potential of 250 mV or more when measured by immersing the stainless steel in a NaCl solution and applying a potential thereto.
- a temperature of the NaCl may be 30°C and a concentration thereof may be 3.5%.
- a method of manufacturing an austenitic stainless steel according to an embodiment of the present disclosure may include hot rolling a slab including, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, cold rolling the hot-rolled slab at room temperature, and cold annealing the cold-rolled steel sheet to satisfy a ⁇ value represented by Equation (1) below to at least -10 but not more than 10.
- ⁇ 406 ⁇ 2127 ⁇ C ⁇ 26.2 ⁇ Mn ⁇ 31.5 ⁇ Ni ⁇ 127 ⁇ N ⁇ 48.2 ⁇ Nb ⁇ 0.108 ⁇ Temp
- Equation (1) [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C).
- a slab having the composition of alloying elements may be processed to prepare a hot-rolled steel sheet by a hot rolling process. Then, the hot-rolled steel sheet may be cold-rolled at room temperature to prepare a cold-rolled steel sheet.
- the prepared cold-rolled steel sheet may be cold-annealed.
- the cold annealing may be performed in a temperature range of 700 to 850°C such that the ⁇ value represented by Equation (1) above satisfies at least -10 but not more than 10.
- the cold rolling process may be performed after the hot rolling process without performing a hot annealing process.
- productivity may be increased and manufacturing costs may be reduced.
- Equation (1) of the prepared cold-annealed steel sheets are shown in Table 1 below.
- Equation (1) [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C).
- Table 1 Category Composition of alloying elements (wt%) Equati on (1) ⁇ Tern p (°C) C Si Mn Cr Ni Cu Mo N Nb Inventive Example 1 0.02 0.31 0.5 18.2 8.02 0.27 0.1 0.041 0.053 9.8 742 Inventive Example 2 0.02 0.31 0.5 18.2 8.02 0.27 0.1 0.041 0.053 8.9 751 Inventive Example 3 0.02 0.31 0.5 18.2 8.02 0.27 0.1 0.041 0.053 3.5 801 Inventive Example 4 0.019 0.31 0.5 18.1 8.05 0.25 0.1 0.1 0 5.2 750 Inventive Example 5 0.019 0.31 0.5 18.1 8.05 0.25 0.1 0.1 0 0 798 Inventive Example 6 0.019 0.31 0.5 18.1 8.05 0.25 0.1
- the prepared cold-annealed steel sheet were cut into samples with a thickness of 0.1 to 3.0 mm. Then, for each sample, an average grain size (d) of a central portion in a thickness direction, a pitting potential, a martensite area fraction of a bent portion, cracks in the bent portion, surface properties of the bent portion, a center line average height Ra of the bent portion, and a ten point average roughness Rz of the bent portion were measured and the results are shown in Table 2 below.
- the average grain size (d) was measured by electron backscatter diffraction (EBSD) (model no. e-Flash FS) by analyzing an orientation of the central portion.
- EBSD electron backscatter diffraction
- the pitting potential refers to a potential value at which pits are formed after immersing the sample in a NaCl solution and applying a potential thereto.
- a NaCl solution maintained at 30°C and having a concentration of 3.5% was used.
- the martensite area fraction of the bent portion (%) refers to an area fraction of martensite in the bent portion after the 180° bending test.
- the martensite area fraction (%) was measured by using a ferrite content measuring device (model no. FMP30).
- the cracks in the bent portion, the surface properties of the bent portion, the center line average height Ra of the bent portion, and the ten point average roughness Rz of the bent portion were measured after the 180° bending test.
- the 180° bending test was performed by setting a curvature R value of a bent portion to be identical to the thickness of the cold-annealed steel sheet and conducting a bending process once.
- 'O' indicates a fine state of cracks in bent portion.
- 'X' indicates occurrence of cracks in the bent portion.
- the S2 values of Equation (1) satisfied the range of at least -10 but not more than 10, and the average grain size (d) satisfied 5 ⁇ m or less.
- the martensite area fraction (%) measured in the bent portion after the 180° bending test satisfied 10% or less in Inventive Examples 1 to 13.
- Comparative Examples 12 to 14 Because the contents of Ni, which softens steel materials, of Comparative Examples 12 to 14 were more than that of Comparative Examples 1 to 11, surface cracks did not occur in the bent portion. However, bend-shaped uncrystallized portions were formed in Comparative Examples 12 to 14 due to low cold annealing temperatures. Therefore, Comparative Examples 12 to 14 exhibited poor surface properties because the center line average heights Ra were 1.16 to 3.92 ⁇ m and the ten point average roughnesses Rz were 7.05 to 16.20 ⁇ m in the bent portion as surface roughnesses.
- FIGS. 1 and 2 are photographs for comparison of occurrence of cracks in a bent portion after a 180° bending test between an inventive example and a comparative example.
- FIG. 1 is a photograph of Inventive Example 5
- FIG. 2 is a photograph Comparative Example 4.
- FIGS. 1 and 2 it was confirmed that surface cracks did not occur in the austenitic stainless steel according to an embodiment of the present disclosure.
- FIGS. 3 and 4 are photographs for comparison of surface properties of a bent portion after a 180° bending test between an inventive example and a comparative example.
- FIG. 3 is a photograph of Inventive Example 5
- FIG. 4 is a photograph of Comparative Example 14. Upon comparison between FIGS. 3 and 4 , it was confirmed that the austenitic stainless steel according to an embodiment of the present disclosure had excellent surface properties.
- FIGS. 5 and 6 are photographs of a central portion in the thickness direction of an inventive example and a comparative example measured by electron backscatter diffraction (EBSD).
- FIG. 5 is a photograph of Inventive Example 5
- FIG. 6 is a photograph of Comparative Example 14.
- EBSD electron backscatter diffraction
- an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method may be provided by presenting a ultra-fine grain manufacturing technology that realizes bending formability and sound surface properties in the bent portion.
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Abstract
Disclosed are aa austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method thereof.The austenitic stainless steel according to an embodiment of the present disclosure includes, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, wherein an average grain size (d) of a central portion in a thickness direction is 5 µm or less, and a martensite area fraction measured in the bent portion after a 180° bending test is 10% or less.
Description
- The present disclosure relates to an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method thereof.
- In general, austenitic stainless steels have been applied for various uses to manufacture components for transportation and construction due to excellent formability, work hardenability, and weldability. However, because 304 series stainless steels or 301 series stainless steels have low yield strengths of 200 to 350 MPa, there are limits to apply these stainless steels to structural materials. Thus, a skin pass rolling process is generally conducted to increase yield strength of 300 series stainless steels for common use. However, the skin pass rolling process may cause problems in increasing manufacturing costs and significantly deteriorating elongation of materials.
- Patent Document 0001 discloses a method of performing heat treatment for a long time over 48 hours in a temperature range of 600 to 700°C to obtain an average grain size of 10 µm or less. However, the method disclosed in Patent Document 0001 may cause problems of deteriorating productivity in the case of implementing the method in an actual production line and increasing manufacturing costs.
- (Patent Document 0001)
Japanese Patent Laid-open Publication No. 2020-050940A (Publication Date: April 2, 2020 - To solve the problem as described above, provided are an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method thereof by presenting a ultra-fine grain manufacturing technology that realizes bending formability and sound surface properties in the bent portion.
- In accordance with an aspect of the present disclosure, an austenitic stainless steel includes, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, wherein an average grain size (d) of a central portion in a thickness direction is 5 µm or less, and a martensite area fraction measured in a bent portion after a 180° bending test may be 10% or less.
- In addition, the austenitic stainless steel according to an embodiment of the present disclosure may have a center line average height Ra of 0.5 µm or less and a ten point average roughness Rz of 3 µm or less in the bent portion as surface roughness.
- In addition, the austenitic stainless steel according to an embodiment of the present disclosure may have a pitting potential of 250 mV or more when measured by a 3.5% NaCl solution at 30°C.
- In accordance with another aspect of the present disclosure, a method of manufacturing an austenitic stainless steel includes hot rolling a slab including, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, cold rolling the hot-rolled steel sheet at room temperature, and cold annealing the cold-rolled steel sheet to satisfy a Ω value represented by Equation (1) below to at least -10 but not more than 10.
- Meanwhile, in Equation (1), [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C).
- In addition, according to the method of manufacturing an austenitic stainless steel according to an embodiment of the present disclosure, the cold rolling may be performed after the hot rolling without performing hot annealing.
- According to an embodiment of the present disclosure, an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a method of manufacturing the same may be provided by applying a ultra-fine grain manufacturing technology that realizes bending formability and sound surface properties in the bent portion.
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FIG. 1 is a photograph of Inventive Example 5 showing surface properties and occurrence of surface cracks in a bent portion after a 180° bending test. -
FIG. 2 is a photograph of Comparative Example 4 showing surface properties and occurrence of surface cracks in a bent portion after a 180° bending test. -
FIG. 3 is a photographs of Inventive Example 5 showing surface roughness of a bent portion after a 180° bending test. -
FIG. 4 is a photographs of Comparative Example 14 showing surface roughness of a bent portion after a 180° bending test. -
FIG. 5 is a photograph of Inventive Example 5 showing a microstructure of a central portion in the thickness direction measured by electron backscatter diffraction (EBSD). -
FIG. 6 is a photograph of Comparative Example 14 showing a microstructure of a central portion in the thickness direction measured by EBSD. - An austenitic stainless steel according to an embodiment of the present disclosure may include, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, wherein an average grain size (d) of a central portion in a thickness direction may be 5 µm or less, and a martensite area fraction measured in the bent portion after a 180° bending test may be 10% or less.
- Hereinafter, preferred embodiments of the present disclosure will now be described. However, the present disclosure may be embodied in many different forms and should not be construed as being limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the scope of the disclosure to those skilled in the art.
- The terms used herein are merely used to describe particular embodiments. Thus, an expression used in the singular encompasses the expression of the plural, unless it has a clearly different meaning in the context. In addition, it is to be understood that the terms such as "including" or "having" are intended to indicate the existence of features, processes, functions, components, or combinations thereof disclosed in the specification, and are not intended to preclude the possibility that one or more other features, processes, functions, components, or combinations thereof may exist or may be added.
- Meanwhile, unless otherwise defined, all terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this disclosure belongs. Thus, these terms should not be interpreted in an idealized or overly formal sense unless expressly so defined herein. As used herein, the singular forms are intended to include the plural forms as well, unless the context clearly indicates otherwise.
- In addition, the terms "about", "substantially", etc. used throughout the specification mean that when a natural manufacturing and substance allowable error are suggested, such an allowable error corresponds a value or is similar to the value, and such values are intended for the sake of clear understanding of the present invention or to prevent an unconscious infringer from illegally using the disclosure of the present invention.
- An austenitic stainless steel according to an embodiment of the present disclosure may include, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities.
- Hereinafter, reasons for numerical limitations on the contents of the alloying elements will be described.
- The content of carbon (C) may be from 0.005 to 0.03%.
- C is an austenite phase-stabilizing element. In consideration thereof, C may be added in an amount of 0.005% or more. However, an excess of C may cause a problem of forming a chromium carbide during low-temperature annealing to deteriorate grain boundary corrosion resistance. In consideration thereof, an upper limit of the C content may be controlled to 0.03 wt%.
- The content of silicon (Si) may be from 0.1 to 1.0%.
- Si is an element added as a deoxidizer during a steel-making process and has an effect on improving corrosion resistance of a steel by forming an Si oxide in a passivated layer in the case of performing a bright annealing process. In consideration thereof, Si may be added in an amount of 0.1 wt% or more. However, an excess of Si may cause a problem of deteriorating ductility. In consideration thereof, an upper limit of the Si content may be controlled to 1.0 wt%.
- The content of manganese (Mn) may be from 0.1 to 2.0%.
- Mn is an austenite phase-stabilizing element. In consideration thereof, Mn may be added in an amount of 0.1% or more. However, an excess of Mn may cause a problem of deteriorating corrosion resistance. In consideration thereof, an upper limit of the Mn content may be controlled to 2.0%.
- The content of nickel (Ni) may be from 6.0 to 12.0%.
- Ni is an austenite phase-stabilizing element and has an effect on softening a steel material. In consideration thereof, Ni may be added in an amount of 6.0% or more. However, an excess of Ni may cause a problem of increasing manufacturing costs. In consideration thereof, an upper limit of Ni may be controlled to 12.0%.
- The content of chromium (Cr) may be from 16.0 to 20.0%.
- Cr is a major element for improving corrosion resistance of a stainless steel. In consideration thereof, Cr may be added in an amount of 16.0 wt% or more. However, an excess of Cr may cause problems of hardening a steel material and inhibiting strain-induced martensite transformation during cold rolling. In consideration thereof, an upper limit of the Cr content may be controlled to 20.0%.
- The content of nitrogen (N) may be from 0.01 to 0.2%.
- N is an austenite phase-stabilizing element and enhances strength of a steel material. In consideration thereof, N may be added in an amount of 0.01% or more. However, an excess of N may cause problems such as hardening of a steel material and deterioration of hot workability. In consideration thereof, an upper limit of the N content may be controlled to 0.2%.
- The content of niobium (Nb) may be from 0.25% or less. Addition of Nb that induces formation of Nb-based Z-phase precipitates has an effect on inhibiting the growth of crystal grains. However, an excess of Nb may cause a problem of increasing manufacturing costs. In consideration thereof, an upper limit of the Nb content may be controlled to 0.25%.
- The remaining component of the composition of the present disclosure is iron (Fe). However, the composition may include unintended impurities inevitably incorporated from raw materials or surrounding environments, and thus addition of other alloy components is not excluded. The impurities are not specifically mentioned in the present disclosure, as they are known to any person skilled in the art of manufacturing.
- By adjusting the composition of the alloying elements of the austenitic stainless steel according to an embodiment of the present disclosure, the average grain size (d) of a central portion in a thickness direction may be 5 µm or less, and a martensite area fraction measured in the bent portion after a 180° bending test may be 10% or less.
- In general, a method of promoting TRIP transformation to transform an austenite phase to a martensite phase is used to implement a ultra-fine grain microstructure. However, in the case of using the method of promoting TRIP transformation, an amount of strain-induced martensite transformation increases during cold deformation. As a result, a hardness of a material increases, and surface properties of a processed portion may deteriorate in the case of processing the material.
- Therefore, according to an embodiment of the present disclosure, by adjusting the composition of the alloying elements such as C, Mn, Ni, N, and Nb, a ultra-fine grain microstructure may be implemented and a martensite area fraction measured in a bent portion may be reduced, so that an austenitic stainless steel with excellent surface properties may be provided.
- Hereinafter, physical properties of the austenitic stainless steel according to an embodiment of the present disclosure will be described in detail.
- The austenitic stainless steel according to an embodiment of the present disclosure may have a center line average height Ra of 0.5 µm or less and a ten point average roughness Rz of 3 µm or less in a bent portion after a 180° bending test. The 180° bending test may be performed by setting a curvature R value of a bent portion to be identical to a thickness of a material and conducting a bending process once.
- The pitting potential is a critical potential at which corrosion occurs in the form of holes in a passivated metal material, and the austenitic stainless steel according to an embodiment of the present disclosure may have a pitting potential of 250 mV or more when measured by immersing the stainless steel in a NaCl solution and applying a potential thereto. In this regard, a temperature of the NaCl may be 30°C and a concentration thereof may be 3.5%.
- Hereinafter, a method of manufacturing the austenitic stainless steel according to an embodiment of the present disclosure will be described in detail.
- A method of manufacturing an austenitic stainless steel according to an embodiment of the present disclosure may include hot rolling a slab including, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities, cold rolling the hot-rolled slab at room temperature, and cold annealing the cold-rolled steel sheet to satisfy a Ω value represented by Equation (1) below to at least -10 but not more than 10.
- Meanwhile, in Equation (1), [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C).
- Reasons for numerical limitations on the contents of the alloying elements are as described above and will be described in more detail.
- A slab having the composition of alloying elements may be processed to prepare a hot-rolled steel sheet by a hot rolling process. Then, the hot-rolled steel sheet may be cold-rolled at room temperature to prepare a cold-rolled steel sheet.
- Then, the prepared cold-rolled steel sheet may be cold-annealed. The cold annealing may be performed in a temperature range of 700 to 850°C such that the Ω value represented by Equation (1) above satisfies at least -10 but not more than 10.
- When the cold annealing temperature is below 700°C, recrystallization does not sufficiently occur to decrease elongation. On the contrary, when the cold annealing temperature is above 850°C, crystal grains coarsen making it difficult to form ultra-fine grains with a size of 5 µm or less, thereby causing problems of occurrence of surface cracks and deterioration of surface roughness in a bent portion of the austenitic stainless steel.
- In addition, according to the method of manufacturing an austenitic stainless steel according to an embodiment of the present disclosure, the cold rolling process may be performed after the hot rolling process without performing a hot annealing process. In the case where a separate annealing process is not conducted after a hot rolling process, productivity may be increased and manufacturing costs may be reduced.
- Hereinafter, the present disclosure will be described in more detail through examples.
- Slabs having the compositions of alloying elements shown in Table 1 below were hot-rolled and then cold-rolled at room temperature with a total reduction rate of 40% or more after performing a hot annealing process at a temperature of 1000 to 1150°C or without performing the hot annealing process. Then, a cold annealing process was performed in temperature range of 700 to 850°C to prepare cold-annealed steel sheets.
- Values of Equation (1) of the prepared cold-annealed steel sheets are shown in Table 1 below. In Table 1, the values of Equation (1) refer to values derived from parameters defined by Equation (1): S2 = 406 - 2127*[C] - 26.2*[Mn] - 31.5*[Ni] - 127*[N] - 48.2*[Nb] - 0.108*Temp.
- In Equation (1), [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C).
Table 1 Category Composition of alloying elements (wt%) Equati on (1) Ω Tern p (°C) C Si Mn Cr Ni Cu Mo N Nb Inventive Example 1 0.02 0.31 0.5 18.2 8.02 0.27 0.1 0.041 0.053 9.8 742 Inventive Example 2 0.02 0.31 0.5 18.2 8.02 0.27 0.1 0.041 0.053 8.9 751 Inventive Example 3 0.02 0.31 0.5 18.2 8.02 0.27 0.1 0.041 0.053 3.5 801 Inventive Example 4 0.019 0.31 0.5 18.1 8.05 0.25 0.1 0.1 0 5.2 750 Inventive Example 5 0.019 0.31 0.5 18.1 8.05 0.25 0.1 0.1 0 0 798 Inventive Example 6 0.019 0.31 0.5 18.1 8.05 0.25 0.1 0.1 0 -5.6 850 Inventive Example 7 0.023 0.53 1.24 17.5 6.4 0 0 0.17 0 9.6 850 Inventive Example 8 0.017 0.32 1.79 16.7 6.85 0.25 0.1 0.15 0 7.1 750 Inventive Example 9 0.017 0.32 1.79 16.7 6.85 0.25 0.1 0.15 0 1.7 800 Inventive Example 10 0.017 0.32 1.79 16.7 6.85 0.25 0.1 0.15 0 -3.6 849 Inventive Example 11 0.022 0.31 0.29 18.2 8.09 0.25 0.1 0.02 0 7.8 800 Inventive Example 12 0.022 0.31 0.29 18.2 8.09 0.25 0.1 0.02 0 2.4 850 Inventive Example 13 0.018 0.3 0.3 18.1 7.96 0.24 0.1 0.021 0.1 9.6 850 Comparative Example 1 0.023 0.53 1.24 17.5 6.4 0 0 0.17 0 20.4 750 Comparative Example 2 0.023 0.53 1.24 17.5 6.4 0 0 0.17 0 15.1 799 Comparative Example 3 0.02 0.51 0.98 17.3 6.3 0 0 0.1 0 45.6 750 Comparative Example 4 0.02 0.51 0.98 17.3 6.3 0 0 0.1 0 40.2 800 Comparative Example 5 0.02 0.51 0.98 17.3 6.3 0 0 0.1 0 34.8 850 Comparative Example 6 0.019 0.3 0.46 17.3 6.3 0.25 0.1 0.15 0.21 44.9 750 Comparative Example 7 0.019 0.3 0.46 17.3 6.3 0.25 0.1 0.15 0.21 39.5 800 Comparative Example 8 0.019 0.3 0.46 17.3 6.3 0.25 0.1 0.15 0.21 34.1 850 Comparative Example 9 0.02 0.29 0.49 16.6 5.98 0.25 0.1 0.18 0 58.3 750 Comparative Example 10 0.02 0.29 0.49 16.6 5.98 0.25 0.1 0.18 0 52.9 801 Comparative Example 11 0.02 0.29 0.49 16.6 5.98 0.25 0.1 0.18 0 47.5 850 Comparative Example 12 0.022 0.31 0.29 18.2 8.09 0.25 0.1 0.02 0 13.2 750 Comparative Example 13 0.018 0.3 0.3 18.1 7.96 0.24 0.1 0.021 0.1 20.6 750 Comparative Example 14 0.018 0.3 0.3 18.1 7.96 0.24 0.1 0.021 0.1 15.8 795 - The prepared cold-annealed steel sheet were cut into samples with a thickness of 0.1 to 3.0 mm. Then, for each sample, an average grain size (d) of a central portion in a thickness direction, a pitting potential, a martensite area fraction of a bent portion, cracks in the bent portion, surface properties of the bent portion, a center line average height Ra of the bent portion, and a ten point average roughness Rz of the bent portion were measured and the results are shown in Table 2 below.
- The average grain size (d) was measured by electron backscatter diffraction (EBSD) (model no. e-Flash FS) by analyzing an orientation of the central portion.
- The pitting potential refers to a potential value at which pits are formed after immersing the sample in a NaCl solution and applying a potential thereto. A NaCl solution maintained at 30°C and having a concentration of 3.5% was used.
- The martensite area fraction of the bent portion (%) refers to an area fraction of martensite in the bent portion after the 180° bending test. The martensite area fraction (%) was measured by using a ferrite content measuring device (model no. FMP30).
- The cracks in the bent portion, the surface properties of the bent portion, the center line average height Ra of the bent portion, and the ten point average roughness Rz of the bent portion were measured after the 180° bending test. The 180° bending test was performed by setting a curvature R value of a bent portion to be identical to the thickness of the cold-annealed steel sheet and conducting a bending process once.
- In the cracks in the bent portion of Table 2 below, 'O' indicates a fine state of cracks in bent portion. 'X' indicates occurrence of cracks in the bent portion.
- In the surface properties of the bent portion of Table 2 below, 'O' indicates fine surface properties of the bent portion. 'X' indicates poor surface properties of the bent portion.
Table 2 d (µm ) Pitting potential (mV) Martensite area fraction of bent portion (%) Cracks in bent portion Surface properti es of bent portion Ra (µm) Rz (µm) Inventive Example 1 2.8 301 4.0 O O 0.42 2.95 Inventive Example 2 3.6 309 10.0 O O 0.39 1.95 Inventive Example 3 4.2 314 4.0 O O 0.25 1.80 Inventive Example 4 3.8 325 1.0 O O 0.35 2.54 Inventive Example 5 4.2 372 1.0 O O 0.28 1.92 Inventive Example 6 4.6 392 1.0 O O 0.22 1.82 Inventive Example 7 4.5 292 0.0 O O 0.45 2.89 Inventive Example 8 3.9 257 2.0 O O 0.32 2.05 Inventive Example 9 4.2 273 1.0 O O 0.22 1.92 Inventive Example 10 4.7 293 1.0 O O 0.21 1.82 Inventive 3.4 325 3.0 O O 0.41 2.22 Example 11 Inventive Example 12 4.1 327 2.0 O O 0.32 1.80 Inventive Example 13 4.1 305 5.0 O O 0.48 2.98 Comparative Example 1 1.2 287 25.0 X X Occurren ce of cracks Occurre nce of cracks Comparative Example 2 4.2 290 15.0 X X Comparative Example 3 3.7 272 45.0 X X Comparative Example 4 4.0 281 40.0 X X Comparative Example 5 4.2 283 39.0 X X Comparative Example 6 0.5 274 44.0 X X Comparative Example 7 2.2 280 44.0 X X Comparative Example 8 3.2 292 31.0 X X Comparative Example 9 1.1 255 61.0 X X Comparative Example 10 3.5 262 52.0 X X Comparative Example 11 3.8 267 45.0 X X Comparative Example 12 1.3 342 16.0 O X 1.16 7.05 Comparative Example 13 2.5 298 21.0 O X 3.92 16.20 Comparative Example 14 3.2 301 19.0 O X 1.57 8.74 - Referring to Tables 1 and 2, in all of Inventive Examples 1 to 13, the S2 values of Equation (1) satisfied the range of at least -10 but not more than 10, and the average grain size (d) satisfied 5 µm or less. In addition, the martensite area fraction (%) measured in the bent portion after the 180° bending test satisfied 10% or less in Inventive Examples 1 to 13.
- Accordingly, no surface cracks occurred in the bent portion in all of Inventive Examples 1 to 13, and as the surface roughness, the center line average height Ra of 0.5 µm or less and the ten point average roughness Rz of 3 µm or less were obtained, indicating excellent surface properties.
- On the contrary, in Comparative Examples 1 to 11, the S2 values of Equation (1) did not satisfy the range of at least -10 but not more than 10 and the martensite area fraction (%) measured in the bent portion after the 180° bending test exceeded 10%. Accordingly, surface cracks occurred in the bent portion of Comparative Examples 1 to 11.
- Because the contents of Ni, which softens steel materials, of Comparative Examples 12 to 14 were more than that of Comparative Examples 1 to 11, surface cracks did not occur in the bent portion. However, bend-shaped uncrystallized portions were formed in Comparative Examples 12 to 14 due to low cold annealing temperatures. Therefore, Comparative Examples 12 to 14 exhibited poor surface properties because the center line average heights Ra were 1.16 to 3.92 µm and the ten point average roughnesses Rz were 7.05 to 16.20 µm in the bent portion as surface roughnesses.
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FIGS. 1 and2 are photographs for comparison of occurrence of cracks in a bent portion after a 180° bending test between an inventive example and a comparative example.FIG. 1 is a photograph of Inventive Example 5, andFIG. 2 is a photograph Comparative Example 4. Upon comparison betweenFIGS. 1 and2 , it was confirmed that surface cracks did not occur in the austenitic stainless steel according to an embodiment of the present disclosure. -
FIGS. 3 and 4 are photographs for comparison of surface properties of a bent portion after a 180° bending test between an inventive example and a comparative example.FIG. 3 is a photograph of Inventive Example 5, andFIG. 4 is a photograph of Comparative Example 14. Upon comparison betweenFIGS. 3 and 4 , it was confirmed that the austenitic stainless steel according to an embodiment of the present disclosure had excellent surface properties. -
FIGS. 5 and6 are photographs of a central portion in the thickness direction of an inventive example and a comparative example measured by electron backscatter diffraction (EBSD).FIG. 5 is a photograph of Inventive Example 5, andFIG. 6 is a photograph of Comparative Example 14. Upon comparison betweenFIGS. 5 and6 , it was confirmed that the austenitic stainless steel according to an embodiment of the present disclosure had ultra-fine grains without band-shaped uncrystallized portions. - While the present disclosure has been particularly described with reference to exemplary embodiments, it should be understood by those of skilled in the art that various changes in form and details may be made without departing from the spirit and scope of the present disclosure.
- According to an embodiment of the present disclosure, an austenitic stainless steel free of surface cracks and having excellent surface roughness in a bent portion and a manufacturing method may be provided by presenting a ultra-fine grain manufacturing technology that realizes bending formability and sound surface properties in the bent portion.
Claims (5)
- An austenitic stainless steel comprising, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities,
wherein an average grain size (d) of a central portion in a thickness direction is 5 µm or less, and a martensite area fraction measured in a bent portion after a 180° bending test is 10% or less. - The austenitic stainless steel according to claim 1, wherein the bent portion has a center line average height Ra of 0.5 µm or less and a ten point average roughness Rz of 3 µm or less as surface roughness.
- The austenitic stainless steel according to claim 1, wherein a pitting potential value measured by a 3.5% NaCl solution at 30°C is 250 mV or more.
- A method of manufacturing an austenitic stainless steel, the method comprising:hot rolling a slab including, in percent by weight (wt%), 0.005 to 0.03% of C, 0.1 to 1% of Si, 0.1 to 2% of Mn, 6 to 12% of Ni, 16 to 20% of Cr, 0.01 to 0.2% of N, 0.25% or less of Nb, and the balance of Fe and inevitable impurities;cold rolling the hot-rolled steel sheet at room temperature with a reduction ratio of 40% or more; and(wherein in Equation (1), [C], [Mn], [Ni], [N], and [Nb] represent weight percentages (wt%) of respective elements and Temp refers to cold annealing temperature (°C))
- The method according to claim 4, wherein the cold rolling is performed after the hot rolling without performing hot annealing.
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SG11201702136YA (en) * | 2014-09-25 | 2017-04-27 | Nippon Steel & Sumitomo Metal Corp | Austenitic stainless steel sheet and method for manufacturing the same |
KR101550738B1 (en) * | 2015-04-29 | 2015-09-08 | 성기천 | Stainless steel with excellent in ductility and stainless pipe for refrigerant piping of using the same |
KR20170069338A (en) * | 2015-12-10 | 2017-06-21 | 주식회사 포스코 | Duplex stainless steel with improved bending property and manufacturing method there of |
KR101735007B1 (en) * | 2015-12-23 | 2017-05-15 | 주식회사 포스코 | Austenitic stainless steel pipe having exceelent wrinkle resistance |
KR101964314B1 (en) * | 2017-08-21 | 2019-08-07 | 주식회사포스코 | Austenitic stainless steel with excellent workability and resistant of season cracking, and drawing product using the same |
JP2020050940A (en) | 2018-09-28 | 2020-04-02 | 国立研究開発法人日本原子力研究開発機構 | Method for producing austenitic fine-grained stainless steel |
-
2021
- 2021-06-21 KR KR1020210080002A patent/KR20220169655A/en unknown
-
2022
- 2022-06-15 EP EP22828661.3A patent/EP4343013A1/en active Pending
- 2022-06-15 CN CN202280043970.2A patent/CN117529571A/en active Pending
- 2022-06-15 WO PCT/KR2022/008454 patent/WO2022270814A1/en active Application Filing
Also Published As
Publication number | Publication date |
---|---|
WO2022270814A1 (en) | 2022-12-29 |
CN117529571A (en) | 2024-02-06 |
KR20220169655A (en) | 2022-12-28 |
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