WO2023075391A1 - Hot-rolled ferritic stainless steel sheet having excellent formability and method for manufacturing same - Google Patents
Hot-rolled ferritic stainless steel sheet having excellent formability and method for manufacturing same Download PDFInfo
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- WO2023075391A1 WO2023075391A1 PCT/KR2022/016420 KR2022016420W WO2023075391A1 WO 2023075391 A1 WO2023075391 A1 WO 2023075391A1 KR 2022016420 W KR2022016420 W KR 2022016420W WO 2023075391 A1 WO2023075391 A1 WO 2023075391A1
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 31
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 238000000034 method Methods 0.000 title claims abstract description 10
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 39
- 239000010959 steel Substances 0.000 claims abstract description 39
- 238000005096 rolling process Methods 0.000 claims abstract description 32
- 238000005098 hot rolling Methods 0.000 claims abstract description 20
- 238000000137 annealing Methods 0.000 claims abstract description 15
- 239000012535 impurity Substances 0.000 claims abstract description 12
- 238000003303 reheating Methods 0.000 claims abstract description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 12
- 229910052804 chromium Inorganic materials 0.000 claims description 11
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- 229910052758 niobium Inorganic materials 0.000 claims description 9
- 229910052719 titanium Inorganic materials 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 238000005266 casting Methods 0.000 claims description 4
- 229910000859 α-Fe Inorganic materials 0.000 claims description 3
- 238000004458 analytical method Methods 0.000 claims description 2
- 238000009749 continuous casting Methods 0.000 abstract 1
- 239000000463 material Substances 0.000 description 32
- 230000000052 comparative effect Effects 0.000 description 16
- 239000011651 chromium Substances 0.000 description 15
- 239000011572 manganese Substances 0.000 description 12
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 12
- 229910052799 carbon Inorganic materials 0.000 description 10
- 239000010949 copper Substances 0.000 description 10
- 239000010955 niobium Substances 0.000 description 10
- 239000010936 titanium Substances 0.000 description 10
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 239000013078 crystal Substances 0.000 description 7
- 238000005097 cold rolling Methods 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- 239000000047 product Substances 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 239000010960 cold rolled steel Substances 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 230000001747 exhibiting effect Effects 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003517 fume Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/0247—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
-
- 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
- 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
-
- 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
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
-
- 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
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C21D2211/005—Ferrite
Definitions
- the present invention relates to a ferritic stainless steel hot-rolled steel sheet with excellent formability and a manufacturing method.
- Ferritic stainless steel cold-rolled products have excellent high-temperature properties such as thermal expansion coefficient and thermal fatigue, are resistant to stress corrosion cracking, and have excellent high-temperature strength. Based on these characteristics, ferritic stainless steel is applied to automobile exhaust systems, household appliances, structures, home appliances, and elevators. It is important to secure formability in order to expand the application field of ferritic stainless steel.
- the deformation mechanism of ferritic stainless steel is by plastic induced transformation, and unlike austenitic stainless steel with high workability, deformation occurs by generation and movement of dislocations. It is characterized in that the formability of ferritic stainless steel is changed by controlling the impurities that hinder the movement of the ferritic stainless steel.
- the present invention controls the band structure formed in the hot-rolled material by rolling it at a predetermined reduction ratio before annealing the hot-rolled steel sheet and further activates the generation of dislocations to refine the crystal grains after the hot-rolled annealing and at the same time form
- An object of the present invention is to manufacture a stainless steel hot-rolled steel sheet that exhibits formability similar to that of cold-rolled steel even though it is a hot-rolled steel by increasing its properties.
- Ferritic stainless steel hot-rolled steel sheet with excellent formability according to an embodiment of the present invention, in weight%, C: 0.001 ⁇ 0.1%, Cr: 10.0 ⁇ 14.0%, Ti: 0.001 ⁇ 0.5%, Nb: 0.001 ⁇ 0.5% , Ni: 0.001 ⁇ 1.5%, Mn: 0.001 ⁇ 1.5%, Cu: 0.001 ⁇ 1.0%, Si 0.001 ⁇ 2.0%, N: 0.001 ⁇ 0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities
- the R-bar value after pre-rolling with a reduction ratio of 30% or more is 1.08 or more, and satisfies TS / YS ⁇ 1.5, which represents the ratio of yield strength (YS) and tensile strength (TS).
- Method for manufacturing a ferritic stainless steel hot-rolled steel sheet excellent in formability in weight%, C: 0.001 ⁇ 0.1%, Cr: 10.0 ⁇ 14.0%, Ti: 0.001 ⁇ 0.5%, Nb: 0.001 ⁇ 0.5%, Ni: 0.001 ⁇ 1.5%, Mn: 0.001 ⁇ 1.5%, Cu: 0.001 ⁇ 1.0%, Si 0.001 ⁇ 2.0%, N: 0.001 ⁇ 0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities
- the band structure formed in the hot-rolled material is controlled and the generation of dislocations is additionally activated to refine the crystal grains after hot-rolling annealing and at the same time increase formability to heat Despite being a soft steel, it is possible to manufacture a stainless steel hot-rolled steel sheet exhibiting formability similar to that of a cold-rolled steel.
- Example 1 shows the microstructure of Example 1 (ferritic stainless steel 35% pre-rolling annealed material).
- Figure 2 shows the microstructure of Example 2 (ferritic stainless steel 50% pre-rolling annealed material).
- Figure 3 shows the microstructure of Comparative Example 1 (ferritic stainless steel hot-rolled annealed material (2.0t)).
- Figure 4 shows the microstructure of Comparative Example 2 (a conventional cold-rolled annealed material of ferritic stainless steel).
- Ferritic stainless steel hot-rolled steel sheet with excellent formability according to an embodiment of the present invention, in weight%, C: 0.001 ⁇ 0.1%, Cr: 10.0 ⁇ 14.0%, Ti: 0.001 ⁇ 0.5%, Nb: 0.001 ⁇ 0.5% , Ni: 0.001 ⁇ 1.5%, Mn: 0.001 ⁇ 1.5%, Cu: 0.001 ⁇ 1.0%, Si 0.001 ⁇ 2.0%, N: 0.001 ⁇ 0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities
- the R-bar value after pre-rolling with a reduction ratio of 30% or more is 1.08 or more, and satisfies TS / YS ⁇ 1.5, which represents the ratio of yield strength (YS) and tensile strength (TS).
- the hot-rolled steel sheet is rolled at a predetermined reduction ratio before annealing to control the band structure formed in the hot-rolled material and additionally activates the generation of dislocations to refine the crystal grains after hot-rolling annealing and at the same time formability It is intended to provide a method for producing ferritic stainless steel exhibiting formability similar to that of cold-rolled steel by increasing the
- Ferritic stainless steel hot-rolled steel sheet with excellent formability in weight%, C: 0.001 ⁇ 0.1%, Cr: 10.0 ⁇ 14.0%, Ti: 0.001 ⁇ 0.5%, Nb: 0.001 ⁇ 0.5% , Ni: 0.001 ⁇ 1.5%, Mn: 0.001 ⁇ 1.5%, Cu: 0.001 ⁇ 1.0%, Si 0.001 ⁇ 2.0%, N: 0.001 ⁇ 0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities
- the R-bar value after pre-rolling with a reduction of 30% or more is 1.08 or more, and satisfies TS / YS ⁇ 1.5, which represents the ratio of yield strength (YS) and tensile strength (TS),
- the pre-rolling reduction ratio may be 35% or more.
- the ferritic stainless steel hot-rolled steel sheet having excellent formability is ferrite grain size when the crystal grain size is measured by EBSD (ELECTRON BACKSCATTERING DIFFRACTION) analysis method in the range of 15 ° to 180 ° between grain orientation differences may be 60 ⁇ m or less.
- the amount of chromium (Cr) is preferably 10.0% or more and 14.0% or less. Chromium (Cr) is the most important element added to secure corrosion resistance of stainless steel, and in the present invention, 10.0% or more of chromium (Cr) is added to increase corrosion resistance. When the amount of chromium (Cr) exceeds 14.0%, it causes hot rolling sticking defects, so it is preferably 14.0% or less.
- the amount of titanium (Ti) is preferably 0.001% or more and 0.5% or less. If the amount of titanium (Ti) is less than 0.001%, the amount of crystallization of TiN is reduced, and the equiaxed crystallization rate of the slab is lowered, and the amount of dissolved C and N elements increases, resulting in a decrease in elongation. There is a problem of deterioration of workability.
- Niobium (Nb) is preferably 0.001% or more and 0.5% or less.
- Niobium (Nb) preferentially combines with carbon (C) and nitrogen (N) to form a precipitate that suppresses the deterioration of corrosion resistance.
- the content is limited to 0.001% or more and 0.5% or less.
- the amount of nickel (Ni) is preferably 0.001% or more and 1.5% or less.
- Nickel (Ni) is an element that improves corrosion resistance, but when a large amount is added, it is preferably 1.5% or less because there is a risk of not only hardening but also stress corrosion cracking.
- the amount of manganese (Mn) is preferably 0.001% or more and 1.5% or less.
- Manganese (Mn) has the effect of increasing the strength of the steel, but when it is excessively contained, the generation of Mn-based fume rapidly decreases weldability, and the ductility of the steel decreases due to the formation of excessive MnS precipitates.
- the amount of copper (Cu) is preferably 1.0% or less. Copper (Cu) has an effect of improving corrosion resistance, but when it exceeds 1.0%, there is a problem in that workability is lowered.
- Silicon (Si) is an element added for deoxidation and ferrite stabilization of molten steel during steelmaking, and it is preferably 0.001% or more, but if its content is excessive, it causes hardening of the material and lowers the ductility of the steel. Limit it to 2.0% or less.
- the amount of nitrogen (N) is preferably 0.001% or more and 0.1% or less.
- Nitrogen (N), like carbon (C), has the effect of increasing the strength of the material. If the amount of nitrogen (N) is less than 0.001%, TiN crystallization is lowered and the equiaxed crystallization rate of the slab is lowered, and if it exceeds 0.1%, impurities in the material increase and the elongation rate decreases.
- the amount of aluminum (Al) is preferably 0.1% or less. When the amount of aluminum (Al) exceeds 0.1%, there is a problem in that the elongation rate decreases due to an increase in impurities in the material.
- the hot rolling reheating temperature is in the range of 1100 ° C to 1280 ° C. If the slab is reheated to a temperature of 1280°C or higher, there is a high possibility of a coarse band structure remaining, which may reduce formability. there is
- a slab was prepared by continuously casting steel having the composition shown in Table 1 below, and after reheating the slab, hot rolling was performed, with a hot-rolled thickness of 2.0 to 5.0 t, a thickness after pre-rolling of 2.0 t, and a reduction ratio of 0 to 50%.
- grain size For ferritic stainless steel hot-rolled steel sheets that were pre-rolled and then hot-rolled and annealed, grain size, R value (R 0 , R 45 , R 90 , R-bar), yield strength, tensile strength, TS/YS, and Elongation was measured.
- Comparative Example 1 is a conventional 2.0t hot-rolled steel and has an average grain size of about 120 ⁇ m, which is very coarse.
- Example 1 shows the microstructure of a material hot-rolled after pre-rolling a 3.1t thick hot-rolled steel sheet at a reduction rate of about 35%, and as shown in Table 2, the grain size is about 60 ⁇ m, Compared to the microstructure of Comparative Example 1 in which the conventional hot-rolled 2.0t steel sheet was annealed, it was found that the crystal grains were finer to a level of 50%.
- Example 2 shows the microstructure of a material obtained by pre-rolling a 4.0t thick hot-rolled steel sheet at a reduction rate of about 35% and then hot-rolling and annealing, and the grain size is fine to about 50 ⁇ m, increasing the pre-rolling reduction rate It can be seen that the crystal grains become finer as time goes on.
- Comparative Example 2 is a conventional cold-rolled annealed material obtained by cold-rolling and cold-rolling a 5.0t hot-rolled material after hot-rolling/pickling and then cold-rolling at a reduction ratio of about 60%. It shows a grain size similar to the rolling Example 2.
- Table 3 shows the formability (R value) of hot-rolled annealed materials according to the pre-rolling reduction ratio and the formability of conventional cold-rolled annealed materials.
- Table 4 shows the tensile properties of each material, and the tensile strength value of Example 2 (2.0t material hot-rolled after about 50% pre-rolling) is the tensile strength value of Comparative Example 2 (normal cold-rolled material) There is no significant difference in contrast, but the yield strength value appears as high as about 10% or more in Example 2.
- pre-rolling materials Compared to normal cold-rolled products that undergo a total of two or more annealing processes of hot-rolling and cold-rolling annealing, pre-rolling materials have higher yield strength than conventional cold-rolled annealing materials because they additionally introduce dislocation and undergo only one hot-rolling annealing process. It is considered to represent These characteristics can be applied to products that require high-strength materials, but it is considered to be helpful in extending the lifespan of existing products.
- ferritic stainless steel hot-rolled steel sheet according to an embodiment of the present invention is a hot-rolled material, it exhibits formability similar to that of a cold-rolled material, and thus industrial applicability is recognized.
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Abstract
The present invention pertains to a hot-rolled ferritic stainless steel sheet having excellent formability, which has an R-bar value of at least 1.08 and satisfies TS/YS≤1.5 representing the ratio of tensile strength (TS) to yield strength (YS) after a steel, containing 0.001-0.1% of C, 10.0-14.0% of Cr, 0.001-0.5% of Ti, 0.001-0.5% of Nb, 0.001-1.5% of Ni, 0.001-1.5% of Mn, 0.001-1.0% of Cu, 0.001-2.0% of Si, 0.001-0.1% of N, and 0.1% or less of Al, with the remainder comprising Fe and inevitable impurities, is hot-rolled and then pre-rolled at a reduction ratio of 30% or more. In addition, the present invention pertains to a method for manufacturing a hot-rolled ferritic stainless steel sheet having excellent formability, the method comprising the steps of: producing a slab by continuous casting a steel containing 0.001-0.1% of C, 10.0-14.0% of Cr, 0.001-0.5% of Ti, 0.001-0.5% of Nb, 0.001-1.5% of Ni, 0.001-1.5% of Mn, 0.001-1.0% of Cu, 0.001-2.0% of Si, 0.001-0.1% of N, and 0.1% or less of Al, with the remainder comprising Fe and inevitable impurities; reheating the produced slab; hot-rolling the reheated slab; pre-rolling the hot-rolled slab at a reduction ratio of 30% or more; and hot-annealing the pre-rolled slab.
Description
본 발명은 성형성이 우수한 페라이트계 스테인리스 열연강판 및 제조 방법에 관한 것이다.The present invention relates to a ferritic stainless steel hot-rolled steel sheet with excellent formability and a manufacturing method.
페라이트계 스테인리스 냉연 제품은 열팽창율, 열피로 등의 고온 특성이 우수하고 응력부식균열에 강하며 고온 강도 또한 우수하다. 이와 같은 특성을 바탕으로 페라이트계 스테인리스강은 자동차 배기계, 가정용 기구, 구조물, 가전 제품, 엘리베이터 등에 적용되고 있다. 페라이트계 스테인리스강의 적용 분야를 넓히기 위해서는 성형성 확보가 중요하다. 페라이트계 스테인리스강의 변형 기구는 소성 유기 변태에 의한 것으로 높은 가공성을 갖는 오스테나이트계 스테인리스강과 달리 전위의 생성 및 이동에 의해서 변형이 일어나기 때문에 전위의 생성 및 이동을 활동화 시키기 위해 압연량을 높이거나 전위의 이동을 방해하는 불순물을 제어하는 것에 의해 페라이트계 스테인리스강의 성형성이 변화되는 특징이 있다. 기존에 많은 연구자들이 페라이트계 스테인리스강의 성형성을 높이기 위해서 노력해 왔으나 장출 성형 등에는 취약한 문제점이 있다. 또한, 열연재는 변형률이 낮아 전위의 생성이 원활하지 않아 그 자체만으로는 동일한 두께라고 하여도 냉간 압연한 냉연 소둔재만큼의 성형성을 확보하기 어려워 열연재는 높은 성형성을 요하는 제품으로의 적용에 한계가 있다.Ferritic stainless steel cold-rolled products have excellent high-temperature properties such as thermal expansion coefficient and thermal fatigue, are resistant to stress corrosion cracking, and have excellent high-temperature strength. Based on these characteristics, ferritic stainless steel is applied to automobile exhaust systems, household appliances, structures, home appliances, and elevators. It is important to secure formability in order to expand the application field of ferritic stainless steel. The deformation mechanism of ferritic stainless steel is by plastic induced transformation, and unlike austenitic stainless steel with high workability, deformation occurs by generation and movement of dislocations. It is characterized in that the formability of ferritic stainless steel is changed by controlling the impurities that hinder the movement of the ferritic stainless steel. In the past, many researchers have tried to improve the formability of ferritic stainless steel, but there is a problem that is vulnerable to elongation molding. In addition, since hot-rolled steel has a low strain rate and does not generate dislocations smoothly, it is difficult to secure formability as much as cold-rolled cold-rolled annealed steel even if it has the same thickness by itself, so hot-rolled steel is applied to products requiring high formability. there is a limit to
본 발명은 이와 같은 문제점을 해결하기 위해, 열연강판을 소둔하기 전 소정의 압하율로 압연하여 열연재에 형성된 밴드조직을 제어하고 추가로 전위의 생성을 활성화시켜 열연소둔 후 결정립을 미세화하는 동시에 성형성을 높여 열연재임에도 불구하고 냉연재와 유사한 성형성을 나타내는 스테인리스 열연강판을 제조하는 것을 목적으로 한다.In order to solve this problem, the present invention controls the band structure formed in the hot-rolled material by rolling it at a predetermined reduction ratio before annealing the hot-rolled steel sheet and further activates the generation of dislocations to refine the crystal grains after the hot-rolled annealing and at the same time form An object of the present invention is to manufacture a stainless steel hot-rolled steel sheet that exhibits formability similar to that of cold-rolled steel even though it is a hot-rolled steel by increasing its properties.
본 발명의 일 실시예에 따른 성형성이 우수한 페라이트계 스테인리스 열연강판은, 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 열간압연한 뒤, 30% 이상의 압하율로 pre-rolling 한 후의 R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족한다.Ferritic stainless steel hot-rolled steel sheet with excellent formability according to an embodiment of the present invention, in weight%, C: 0.001 ~ 0.1%, Cr: 10.0 ~ 14.0%, Ti: 0.001 ~ 0.5%, Nb: 0.001 ~ 0.5% , Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities After hot rolling, the R-bar value after pre-rolling with a reduction ratio of 30% or more is 1.08 or more, and satisfies TS / YS ≤ 1.5, which represents the ratio of yield strength (YS) and tensile strength (TS).
본 발명의 다른 일 실시예에 따른 성형성이 우수한 페라이트계 스테인리스 열연강판의 제조방법은, 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 연속주조하여 슬래브를 제조하는 단계; 상기 제조된 슬래브를 재가열하는 단계; 상기 재가열된 슬래브를 열간압연하는 단계; R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족하도록 30% 이상의 압하율로 pre-rolling하는 단계; 및 열연 소둔하는 단계를 포함한다.Method for manufacturing a ferritic stainless steel hot-rolled steel sheet excellent in formability according to another embodiment of the present invention, in weight%, C: 0.001 ~ 0.1%, Cr: 10.0 ~ 14.0%, Ti: 0.001 ~ 0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities Manufacturing a slab by continuously casting a steel comprising a; reheating the manufactured slab; hot rolling the reheated slab; R-bar value is 1.08 or more, pre-rolling at a reduction ratio of 30% or more to satisfy TS / YS ≤ 1.5 representing the ratio of yield strength (YS) and tensile strength (TS); and hot rolling annealing.
본 발명에 따라 열연강판을 소둔하기 전 30% 이상의 압하율로 압연하는 경우, 열연재에 형성된 밴드조직을 제어하고 추가로 전위의 생성을 활성화시켜 열연소둔 후 결정립을 미세화하는 동시에 성형성을 높여 열연재임에도 불구하고 냉연재와 유사한 성형성을 나타내는 스테인리스 열연강판을 제조할 수 있다.According to the present invention, when the hot-rolled steel sheet is rolled at a reduction ratio of 30% or more before annealing, the band structure formed in the hot-rolled material is controlled and the generation of dislocations is additionally activated to refine the crystal grains after hot-rolling annealing and at the same time increase formability to heat Despite being a soft steel, it is possible to manufacture a stainless steel hot-rolled steel sheet exhibiting formability similar to that of a cold-rolled steel.
도 1은 실시예 1(페라이트계 스테인리스강 35% pre-rolling 소둔재)의 미세조직을 나타낸 것이다.1 shows the microstructure of Example 1 (ferritic stainless steel 35% pre-rolling annealed material).
도 2는 실시예 2(페라이트계 스테인리스강 50% pre-rolling 소둔재)의 미세조직을 나타낸 것이다.Figure 2 shows the microstructure of Example 2 (ferritic stainless steel 50% pre-rolling annealed material).
도 3은 비교예 1(페라이트계 스테인리스강 열연 소둔재(2.0t))의 미세조직을 나타낸 것이다.Figure 3 shows the microstructure of Comparative Example 1 (ferritic stainless steel hot-rolled annealed material (2.0t)).
도 4는 비교예 2(페라이트계 스테인리스강의 통상의 냉연 소둔재)의 미세조직을 나타낸 것이다.Figure 4 shows the microstructure of Comparative Example 2 (a conventional cold-rolled annealed material of ferritic stainless steel).
본 발명의 일 실시예에 따른 성형성이 우수한 페라이트계 스테인리스 열연강판은, 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 열간압연한 뒤, 30% 이상의 압하율로 pre-rolling 한 후의 R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족한다.Ferritic stainless steel hot-rolled steel sheet with excellent formability according to an embodiment of the present invention, in weight%, C: 0.001 ~ 0.1%, Cr: 10.0 ~ 14.0%, Ti: 0.001 ~ 0.5%, Nb: 0.001 ~ 0.5% , Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities After hot rolling, the R-bar value after pre-rolling with a reduction ratio of 30% or more is 1.08 or more, and satisfies TS / YS ≤ 1.5, which represents the ratio of yield strength (YS) and tensile strength (TS).
페라이트계 스테인리스강의 성형성을 개선하는 방법에 대해서 지금까지 다양한 방법이 검토되어 왔다. 일반적으로, 열연 재가열 온도를 낮게 관리하거나 조압연 후단에서 높은 압하율로 압연하여 전위의 도입을 활성화 시켜 재결정을 원활하게 해주는 방법이 있으나, 이는 실제 생산으로의 적용시 낮은 재가열 온도로 표면 산화스케일의 형성이 어려워 스티킹 결함을 비롯한 다양한 표면 결함을 유발시키거나 심하면 균열에 의한 파단 문제점도 있어 실제 적용에는 한계점이 분명히 있다.Various methods have been studied so far regarding methods for improving the formability of ferritic stainless steels. In general, there is a method of managing the hot-rolled reheating temperature at a low level or rolling at a high reduction ratio at the end of rough rolling to activate the introduction of dislocations to facilitate recrystallization. Since it is difficult to form, it causes various surface defects including sticking defects, and in severe cases, there is also a problem of fracture due to cracks, so there are clear limitations in practical application.
이러한 단점을 극복하기 위해 본 발명에서는, 열연강판을 소둔하기 전 소정의 압하율로 압연하여 열연재에 형성된 밴드조직을 제어하고 추가로 전위의 생성을 활성화시켜 열연소둔 후 결정립을 미세화하는 동시에 성형성을 높여 냉연재와 유사한 성형성을 나타내는 페라이트계 스테인리스강의 제조방법을 제공하고자 한다.In order to overcome these disadvantages, in the present invention, the hot-rolled steel sheet is rolled at a predetermined reduction ratio before annealing to control the band structure formed in the hot-rolled material and additionally activates the generation of dislocations to refine the crystal grains after hot-rolling annealing and at the same time formability It is intended to provide a method for producing ferritic stainless steel exhibiting formability similar to that of cold-rolled steel by increasing the
[페라이트계 스테인리스 열연강판][Ferritic stainless hot-rolled steel sheet]
본 발명의 일 실시예에 따른 성형성이 우수한 페라이트계 스테인리스 열연강판은, 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 열간압연한 뒤, 30% 이상의 압하율로 pre-rolling 한 후의 R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족하며, 바람직하게는 pre-rolling 압하율은 35% 이상일 수 있다.Ferritic stainless steel hot-rolled steel sheet with excellent formability according to an embodiment of the present invention, in weight%, C: 0.001 ~ 0.1%, Cr: 10.0 ~ 14.0%, Ti: 0.001 ~ 0.5%, Nb: 0.001 ~ 0.5% , Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities After hot rolling, the R-bar value after pre-rolling with a reduction of 30% or more is 1.08 or more, and satisfies TS / YS ≤ 1.5, which represents the ratio of yield strength (YS) and tensile strength (TS), Preferably, the pre-rolling reduction ratio may be 35% or more.
또한, 본 발명의 다른 일 실시예에 따르면, 성형성이 우수한 페라이트계 스테인리스 열연강판은 결정립간 방위차가 15°~180° 범위에서 EBSD(ELECTRON BACKSCATTERING DIFFRACTION) 분석법으로 결정립 크기를 측정하였을 때 페라이트 결정립 크기가 60㎛ 이하일 수 있다.In addition, according to another embodiment of the present invention, the ferritic stainless steel hot-rolled steel sheet having excellent formability is ferrite grain size when the crystal grain size is measured by EBSD (ELECTRON BACKSCATTERING DIFFRACTION) analysis method in the range of 15 ° to 180 ° between grain orientation differences may be 60 μm or less.
이하에서 특별한 언급이 없는 한 단위는 중량%이다. 또한, 어떤 부분이 어떤 구성요소를 "포함"한다고 할 때, 이는 특별히 반대되는 기재가 없는 한 다른 구성요소를 제외하는 것이 아니라 다른 구성요소를 더 포함할 수 있는 것을 의미한다.In the following, unless otherwise specified, units are % by weight. In addition, when a part "includes" a certain component, it means that it may further include other components without excluding other components unless otherwise stated.
(성분범위)(Ingredient range)
C: 0.001~0.1%C: 0.001 to 0.1%
탄소(C)의 양이 많으면 강도가 향상되지만 가공성이 낮아진다. 충분한 강도를 얻기 위해서는 0.001% 이상의 탄소(C)를 함유해야 하지만 0.1% 를 초과하면 가공성이 감소하는 문제가 있다.If the amount of carbon (C) is large, the strength is improved, but the workability is lowered. In order to obtain sufficient strength, 0.001% or more of carbon (C) must be contained, but if it exceeds 0.1%, there is a problem in that workability is reduced.
Cr: 10.0~14.0%Cr: 10.0 to 14.0%
크롬(Cr)의 양은 10.0% 이상 14.0% 이하인 것이 바람직하다. 크롬(Cr)은 스테인리스 강의 내식성을 확보하기 위하여 가장 중요하게 첨가되는 원소로, 본 발명에서는 내식성을 높이기 위해 10.0% 이상의 크롬(Cr)을 첨가하였다. 크롬(Cr)이 14.0%를 초과하게 되면 열연 스티킹(sticking) 결함 발생의 원인이 되므로 14.0% 이하인 것이 바람직하다.The amount of chromium (Cr) is preferably 10.0% or more and 14.0% or less. Chromium (Cr) is the most important element added to secure corrosion resistance of stainless steel, and in the present invention, 10.0% or more of chromium (Cr) is added to increase corrosion resistance. When the amount of chromium (Cr) exceeds 14.0%, it causes hot rolling sticking defects, so it is preferably 14.0% or less.
Ti: 0.001~0.5%Ti: 0.001 to 0.5%
티타늄(Ti)의 양은 0.001% 이상 0.5% 이하인 것이 바람직하다. 티타늄(Ti)의 양이 0.001% 미만이면 TiN 정출양이 줄어 슬라브의 등축정율이 낮아지고, 고용된 C, N 원소들이 많아져 연신율이 떨어지는 문제가 있고, 0.5%를 초과하면 Ti계 산화물의 증가로 가공성이 저하되는 문제가 있다.The amount of titanium (Ti) is preferably 0.001% or more and 0.5% or less. If the amount of titanium (Ti) is less than 0.001%, the amount of crystallization of TiN is reduced, and the equiaxed crystallization rate of the slab is lowered, and the amount of dissolved C and N elements increases, resulting in a decrease in elongation. There is a problem of deterioration of workability.
Nb: 0.001~0.5%Nb: 0.001 to 0.5%
니오븀(Nb)의 양은 0.001% 이상 0.5% 이하인 것이 바람직하다. 니오븀(Nb)은 탄소(C), 질소(N)와 우선적으로 결합해 내식성의 저하를 억제하는 석출물을 형성하지만, 과잉 첨가시에는 개재물에 의한 외관 불량 및 인성 저하를 초래하고 원료비가 상승되기 때문에 그 함량을 0.001% 이상 0.5% 이하로 제한한다.The amount of niobium (Nb) is preferably 0.001% or more and 0.5% or less. Niobium (Nb) preferentially combines with carbon (C) and nitrogen (N) to form a precipitate that suppresses the deterioration of corrosion resistance. The content is limited to 0.001% or more and 0.5% or less.
Ni: 0.001~1.5%Ni: 0.001 to 1.5%
니켈(Ni)의 양은 0.001% 이상 1.5% 이하인 것이 바람직하다. 니켈(Ni)은 내식성을 향상시키는 원소이지만, 다량 첨가하게 되면 경질화된 뿐만 아니라 응력부식균열이 발생될 우려가 있으므로 1.5%이하로 하는 것이 바람직하다.The amount of nickel (Ni) is preferably 0.001% or more and 1.5% or less. Nickel (Ni) is an element that improves corrosion resistance, but when a large amount is added, it is preferably 1.5% or less because there is a risk of not only hardening but also stress corrosion cracking.
Mn: 0.001~1.5%Mn: 0.001 to 1.5%
망간(Mn)의 양은 0.001% 이상 1.5% 이하인 것이 바람직하다. 망간(Mn)은 강의 강도를 높이는 효과가 있지만, 과잉 함유시 Mn계 퓸 발생이 급증하여 용접성이 저하되며, 과도한 MnS 석출물 형성으로 인해 강의 연성이 저하되는 바 1.5% 이하로 함유한다.The amount of manganese (Mn) is preferably 0.001% or more and 1.5% or less. Manganese (Mn) has the effect of increasing the strength of the steel, but when it is excessively contained, the generation of Mn-based fume rapidly decreases weldability, and the ductility of the steel decreases due to the formation of excessive MnS precipitates.
Cu: 0.001~1.0%Cu: 0.001~1.0%
구리(Cu)의 양은 1.0% 이하인 것이 바람직하다. 구리(Cu)는 내식성을 개선하는 효과가 있지만, 1.0%를 넘게 되면 가공성이 저하되는 문제가 있다.The amount of copper (Cu) is preferably 1.0% or less. Copper (Cu) has an effect of improving corrosion resistance, but when it exceeds 1.0%, there is a problem in that workability is lowered.
Si: 0.001~2.0%Si: 0.001 to 2.0%
규소(Si)는 제강 시 용강의 탈산과 페라이트 안정화를 위해 첨가되는 원소로 0.001% 이상인 것이 바람직하지만, 그 함량이 과다할 경우 재질의 경화를 일으켜 강의 연성이 저하되는 바 2.0% 이하로 제한한다.Silicon (Si) is an element added for deoxidation and ferrite stabilization of molten steel during steelmaking, and it is preferably 0.001% or more, but if its content is excessive, it causes hardening of the material and lowers the ductility of the steel. Limit it to 2.0% or less.
N: 0.001~0.1%N: 0.001 to 0.1%
질소(N)의 양은 0.001% 이상 0.1% 이하인 것이 바람직하다. 질소(N)는 탄소(C)와 같이 재료의 강도를 상승시키는 효과가 있다. 질소(N)의 양이 0.001% 미만이면 TiN 정출이 낮아져 슬라브의 등축정율이 낮아지고, 0.1%를 초과하면 소재의 불순물이 증가하여 연신율이 떨어지는 문제가 있다.The amount of nitrogen (N) is preferably 0.001% or more and 0.1% or less. Nitrogen (N), like carbon (C), has the effect of increasing the strength of the material. If the amount of nitrogen (N) is less than 0.001%, TiN crystallization is lowered and the equiaxed crystallization rate of the slab is lowered, and if it exceeds 0.1%, impurities in the material increase and the elongation rate decreases.
Al: 0.1% 이하Al: 0.1% or less
알루미늄(Al)의 양은 0.1% 이하인 것이 바람직하다. 알루미늄(Al)의 양이 0.1%를 초과하면 소재의 불순물이 증가하여 연신율이 떨어지는 문제가 있다.The amount of aluminum (Al) is preferably 0.1% or less. When the amount of aluminum (Al) exceeds 0.1%, there is a problem in that the elongation rate decreases due to an increase in impurities in the material.
[페라이트계 스테인리스 열연강판의 제조방법][Method of manufacturing ferritic stainless hot-rolled steel sheet]
본 발명의 일 실시예에 따른 성형성이 우수한 페라이트계 스테인리스 열연강판의 제조방법은, 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 연속주조하여 슬래브를 제조하는 단계; 상기 제조된 슬래브를 재가열하는 단계; 상기 재가열된 슬래브를 열간압연하는 단계; R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족하도록 30% 이상의 압하율로 pre-rolling하는 단계; 및In the manufacturing method of a ferritic stainless steel hot-rolled steel sheet excellent in formability according to an embodiment of the present invention, in weight%, C: 0.001 to 0.1%, Cr: 10.0 to 14.0%, Ti: 0.001 to 0.5%, Nb: 0.001 ~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% or less, remaining Fe and unavoidable impurities Manufacturing a slab by continuously casting a steel comprising; reheating the manufactured slab; hot rolling the reheated slab; R-bar value is 1.08 or more, pre-rolling at a reduction ratio of 30% or more to satisfy TS / YS ≤ 1.5 representing the ratio of yield strength (YS) and tensile strength (TS); and
열연 소둔하는 단계를 포함한다.It includes the step of hot rolling annealing.
열연 재가열 온도는 1100℃~1280℃ 범위로 한다. 1280℃ 이상의 온도로 슬래브를 재가열할 경우 조대한 band 조직이 잔류할 가능성이 높아 성형성을 저하시킬 우려가 있으며, 1100℃ 이하로 슬래브를 재가열할 경우 열간압연시 압연부하가 높아져 생산성을 저하할 우려가 있다. The hot rolling reheating temperature is in the range of 1100 ° C to 1280 ° C. If the slab is reheated to a temperature of 1280℃ or higher, there is a high possibility of a coarse band structure remaining, which may reduce formability. there is
이하, 본 발명을 실시예를 통하여 보다 구체적으로 설명한다. Hereinafter, the present invention will be described in more detail through examples.
하기 실시예는 본 발명이 속하는 기술분야에서 통상의 지식을 가진 자에게 본 발명의 사상을 충분히 전달하기 위해 제시하는 것이며, 본 발명은 여기서 제시한 실시예만으로 한정되지 않고, 다른 형태로 구체화될 수도 있다. The following examples are presented to sufficiently convey the spirit of the present invention to those skilled in the art to which the present invention belongs, and the present invention is not limited to only the examples presented here, and may be embodied in other forms. there is.
(실시예)(Example)
하기 표 1의 조성을 가지는 강을 연속주조하여 슬라브를 제조하고, 슬라브를 재가열한 후, 열간압연하고, 2.0~5.0t의 열연두께, 2.0t의 pre-rolling후 두께, 0~50%의 압하율로 pre-rolling을 실시한 후, 열연 소둔한 페라이트계 스테인리스 열연강판에 대하여, Grain size, R 값(R0, R45, R90, R-bar), 항복강도, 인장강도, TS/YS, 및 연신율을 측정하였다.A slab was prepared by continuously casting steel having the composition shown in Table 1 below, and after reheating the slab, hot rolling was performed, with a hot-rolled thickness of 2.0 to 5.0 t, a thickness after pre-rolling of 2.0 t, and a reduction ratio of 0 to 50%. For ferritic stainless steel hot-rolled steel sheets that were pre-rolled and then hot-rolled and annealed, grain size, R value (R 0 , R 45 , R 90 , R-bar), yield strength, tensile strength, TS/YS, and Elongation was measured.
구분 (중량%)division (weight%) |
CC | SiSi | MnMn | CrCr | NiNi | CuCu | TiTi | NbNb | NN | AlAl |
실시예 1Example 1 | 0.0070.007 | 0.4460.446 | 0.260.26 | 11.1211.12 | 0.0750.075 | 0.0130.013 | 0.190.19 | 0.0020.002 | 0.00770.0077 | 0.0320.032 |
실시예 2Example 2 | 0.0060.006 | 0.4470.447 | 0.260.26 | 11.3011.30 | 0.0730.073 | 0.0100.010 | 0.210.21 | 0.0030.003 | 0.00520.0052 | 0.0220.022 |
비교예 1Comparative Example 1 | 0.0060.006 | 0.4720.472 | 0.370.37 | 11.1511.15 | 0.0670.067 | 0.0090.009 | 0.180.18 | 0.0020.002 | 0.00570.0057 | 0.0230.023 |
비교예 2Comparative Example 2 | 0.0080.008 | 0.4660.466 | 0.360.36 | 11.1711.17 | 0.0720.072 | 0.0080.008 | 0.220.22 | 0.0020.002 | 0.00790.0079 | 0.0520.052 |
하율에 따른 열연소둔재(2.0t)를 비롯해 통상의 냉연 소둔재(2.0t)의 미세조직을 나타낸 것이다. 비교예 1은 통상의 2.0t 열연재로 평균 결정립 크기는 약 120㎛로 나타나 매우 조대하다. 실시예 1은 3.1t 두께의 열연강판을 약 35% 의 압하율로 pre-rolling한 후 열연 소둔한 소재의 미세조직을 나타낸 것으로, 표 2에 나타낸 바와 같이 결정립 크기는 약 60㎛ 수준으로 나타나, 기존의 열연 2.0t 강판을 소둔한 비교예 1의 미세조직과 비교해 50% 수준까지 결정립이 미세해짐을 알 수 있었다. 이는 30% 이상의 압하율로 열연재를 압연할 시 도입되는 전위의 추가 생성으로 인해 결정립이 미세화됨을 추정할 수 있다. 실시예 2는 4.0t 두께의 열연 강판을 약 35% 의 압하율로 pre-rolling한 후 열연 소둔한 소재의 미세조직을 나타낸 것으로 결정립 크기는 약 50㎛ 수준까지 미세해져 pre-rolling 압하율이 증가할수록 결정립이 미세해짐을 알 수 있다. 비교예 2는 5.0t 열연재를 열연소둔/산세한 후 약 60%의 압하율로 냉간압연하여 냉연소둔한 통상의 냉연 소둔재로 결정립은 약 55㎛ 수준으로 나타나, 약 50% 수준으로 pre-rolling한 실시예 2와 유사 수준의 결정립 크기를 보여주고 있다. It shows the microstructure of the conventional cold-rolled annealed material (2.0t) including the hot-rolled annealed material (2.0t) according to the load rate. Comparative Example 1 is a conventional 2.0t hot-rolled steel and has an average grain size of about 120 μm, which is very coarse. Example 1 shows the microstructure of a material hot-rolled after pre-rolling a 3.1t thick hot-rolled steel sheet at a reduction rate of about 35%, and as shown in Table 2, the grain size is about 60㎛, Compared to the microstructure of Comparative Example 1 in which the conventional hot-rolled 2.0t steel sheet was annealed, it was found that the crystal grains were finer to a level of 50%. It can be assumed that the crystal grains are refined due to the additional generation of dislocations introduced when rolling the hot-rolled material at a reduction ratio of 30% or more. Example 2 shows the microstructure of a material obtained by pre-rolling a 4.0t thick hot-rolled steel sheet at a reduction rate of about 35% and then hot-rolling and annealing, and the grain size is fine to about 50 μm, increasing the pre-rolling reduction rate It can be seen that the crystal grains become finer as time goes on. Comparative Example 2 is a conventional cold-rolled annealed material obtained by cold-rolling and cold-rolling a 5.0t hot-rolled material after hot-rolling/pickling and then cold-rolling at a reduction ratio of about 60%. It shows a grain size similar to the rolling Example 2.
구분division | 열연두께hot rolled thickness | Pre-rolling 후 두께Thickness after pre-rolling | Pre-rolling 압하율Pre-rolling reduction rate | Grain sizeGrain size |
실시예 1Example 1 | 3.1t3.1t | 2.0t2.0t | 35%35% | 59.5㎛59.5㎛ |
실시예 2Example 2 | 4.0t4.0t | 2.0t2.0t | 50%50% | 50.7㎛50.7㎛ |
비교예 1Comparative Example 1 | 2.0t2.0t | 2.0t2.0t | 0%0% | 121.5㎛121.5㎛ |
비교예 2Comparative Example 2 | 5.0t5.0t | 2.0t2.0t | 냉연 압하율 60%Cold rolled rolling reduction 60% | 54.9㎛54.9㎛ |
표 3은 pre-rolling 압하율에 따른 열연소둔재의 성형성 (R값) 및 통상의 냉연 소둔재의 성형성을 나타낸 것이다. 소재의 수직 이방성을 나타내는 R-bar값은 판재의 면 방향으로는 성질이 같고 두께 방향의 성질이 면 방향의 성질과는 다른 것으로, 대부분의 압연판은 면의 방향에 따라서도 소성이 변하는 평면 이방성을 가지고 있기 때문에, 압연 방향과 0도, 45도, 90도 방향으로 인장하여 측정한 R값의 평균값을 사용한다 (R-bar=(R0 + 2R45 + R90)/4).Table 3 shows the formability (R value) of hot-rolled annealed materials according to the pre-rolling reduction ratio and the formability of conventional cold-rolled annealed materials. The R-bar value, which represents the perpendicular anisotropy of the material, has the same properties in the plane direction of the plate, but the properties in the thickness direction are different from those in the plane direction. Since it has , the average value of R values measured by stretching in the rolling direction and 0 degree, 45 degree, and 90 degree directions is used (R-bar=(R 0 + 2R 45 + R 90 )/4).
비교예 1(통상의 2.0t 열연소둔재)의 R-bar 값은 약 1.01 수준으로 매우 열위하나, pre-rolling 압하율이 점차 높아짐에 따라 R-bar 값이 점차 증가함을 알 수 있다. 또한, 실시예 2(50% pre-rolling된 열연소둔재)의 R-bar 값은 약 1.21 수준으로 비교예 2(통상의 냉연소둔재)의 R-bar값과 유사 수준을 나타냄을 알 수 있다. It can be seen that the R-bar value of Comparative Example 1 (normal 2.0t hot rolled annealed material) is very poor at about 1.01 level, but the R-bar value gradually increases as the pre-rolling reduction gradually increases. In addition, it can be seen that the R-bar value of Example 2 (50% pre-rolled hot-rolled annealed material) is about 1.21, which is similar to the R-bar value of Comparative Example 2 (normal cold-rolled annealed material). .
구분division | 열연두께hot rolled thickness | Pre-rolling 후 두께Thickness after pre-rolling | Pre-rolling 압하율Pre-rolling reduction rate | R0 R 0 | R45 R45 | R90 R90 | R-barR-bar |
실시예 1Example 1 | 3.1t3.1t | 2.0t2.0t | 35%35% | 0.770.77 | 1.021.02 | 1.511.51 | 1.081.08 |
실시예 2Example 2 | 4.0t4.0t | 2.0t2.0t | 50%50% | 1.161.16 | 0.990.99 | 1.71.7 | 1.211.21 |
비교예 1Comparative Example 1 | 2.0t2.0t | 2.0t2.0t | 0%0% | 0.540.54 | 0.770.77 | 1.011.01 | 0.770.77 |
비교예 2Comparative Example 2 | 5.0t5.0t | 2.0t2.0t | 냉간압하율60%Cold rolling reduction 60% | 1.221.22 | 0.850.85 | 2.142.14 | 1.271.27 |
표 4는 각 소재의 인장 특성을 나타낸 것으로 실시예 2(약 50% pre-rolling한 후 열연소둔한 2.0t 소재)의 인장강도 값이 비교예 2(통상의 냉연소둔한 소재)의 인장강도 값 대비 큰 유의차가 없으나, 항복강도 값은 실시예 2에서 약 10% 이상 수준으로 높게 나타난다. 이는 열연소둔 및 냉연소둔의 총 2회 이상의 소둔공정을 거치는 통상의 냉연재 대비, pre-rolling재는 추가적으로 전위를 도입하고 단 1회의 열연 소둔공정을 거치기 때문에 통상의 냉연소둔재 대비 더 높은 항복강도를 나타내는 것으로 판단된다. 이러한 특성은 소재의 고강도화를 요하는 제품군으로의 적용도 가능하지만 기존에 적용되는 제품의 수명 연장에도 도움이 될 것으로 판단된다.Table 4 shows the tensile properties of each material, and the tensile strength value of Example 2 (2.0t material hot-rolled after about 50% pre-rolling) is the tensile strength value of Comparative Example 2 (normal cold-rolled material) There is no significant difference in contrast, but the yield strength value appears as high as about 10% or more in Example 2. Compared to normal cold-rolled products that undergo a total of two or more annealing processes of hot-rolling and cold-rolling annealing, pre-rolling materials have higher yield strength than conventional cold-rolled annealing materials because they additionally introduce dislocation and undergo only one hot-rolling annealing process. It is considered to represent These characteristics can be applied to products that require high-strength materials, but it is considered to be helpful in extending the lifespan of existing products.
구분division | 열연두께hot rolled thickness | Pre-rolling 후 두께Thickness after pre-rolling | Pre-rolling 압하율Pre-rolling reduction rate |
YS (MPa)YS (MPa) |
TS (MPa)TS (MPa) |
TS/YSTS/YS | EL(%)EL(%) | |
실시예 1Example 1 | 3.1t3.1t | 2.0t2.0t | 35%35% | 306306 | 415415 | 1.361.36 | 3333 | |
실시예 2Example 2 | 4.0t4.0t | 2.0t2.0t | 50%50% | 293293 | 405405 | 1.381.38 | 3636 | |
비교예 1Comparative Example 1 | 2.0t2.0t | 2.0t2.0t | 0%0% | 270270 | 419419 | 1.551.55 | 3434 | |
비교예 2Comparative Example 2 | 5.0t5.0t | 2.0t2.0t | 냉간압하율60%Cold rolling reduction 60% | 261261 | 397397 | 1.521.52 | 3535 |
본 발명의 일 실시예에 따른 페라이트계 스테인리스 열연강판은 열연재임에도 불구하고 냉연재와 유사한 성형성을 나타내는 바, 산업상 이용가능성이 인정된다.Although the ferritic stainless steel hot-rolled steel sheet according to an embodiment of the present invention is a hot-rolled material, it exhibits formability similar to that of a cold-rolled material, and thus industrial applicability is recognized.
Claims (3)
- 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 열간압연한 뒤, 30% 이상의 압하율로 pre-rolling 한 후의 R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족하는 성형성이 우수한 페라이트계 스테인리스 열연강판.In % by weight, C: 0.001 to 0.1%, Cr: 10.0 to 14.0%, Ti: 0.001 to 0.5%, Nb: 0.001 to 0.5%, Ni: 0.001 to 1.5%, Mn: 0.001 to 1.5%, Cu: 0.001 to 0.001% 1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% or less, after hot rolling the steel containing the remaining Fe and unavoidable impurities, R- after pre-rolling at a reduction ratio of 30% or more A ferritic stainless steel hot-rolled steel sheet with excellent formability that has a bar value of 1.08 or more and satisfies TS/YS≤1.5 representing the ratio of yield strength (YS) and tensile strength (TS).
- 청구항 1에 있어서,The method of claim 1,결정립간 방위차가 15°~180° 범위에서 EBSD(ELECTRON BACKSCATTERING DIFFRACTION) 분석법으로 결정립 크기를 측정하였을 때 페라이트 결정립 크기가 60㎛ 이하인, 성형성이 우수한 페라이트계 스테인리스 열연강판. A ferritic stainless steel hot-rolled steel sheet with excellent formability, with a ferrite grain size of 60㎛ or less when the grain size is measured by the EBSD (ELECTRON BACKSCATTERING DIFFRACTION) analysis method in the range of 15° to 180° for the orientation difference between grains.
- 중량%로, C: 0.001~0.1%, Cr: 10.0~14.0%, Ti: 0.001~0.5%, Nb: 0.001~0.5%, Ni: 0.001~1.5%, Mn: 0.001~1.5%, Cu: 0.001~1.0%, Si 0.001~2.0%, N: 0.001~0.1%, Al: 0.1% 이하, 나머지 Fe 및 불가피한 불순물을 포함하는 강을 연속주조하여 슬래브를 제조하는 단계; In % by weight, C: 0.001 to 0.1%, Cr: 10.0 to 14.0%, Ti: 0.001 to 0.5%, Nb: 0.001 to 0.5%, Ni: 0.001 to 1.5%, Mn: 0.001 to 1.5%, Cu: 0.001 to 0.001% 1.0%, Si 0.001 ~ 2.0%, N: 0.001 ~ 0.1%, Al: 0.1% or less, the remaining Fe, and manufacturing a slab by continuously casting a steel containing unavoidable impurities;상기 제조된 슬래브를 재가열하는 단계;reheating the manufactured slab;상기 재가열된 슬래브를 열간압연하는 단계;hot rolling the reheated slab;R-bar 값이 1.08 이상이며, 항복 강도(YS) 및 인장 강도(TS)의 비를 나타내는 TS/YS≤1.5를 만족하도록 30% 이상의 압하율로 pre-rolling하는 단계; 및R-bar value is 1.08 or more, pre-rolling at a reduction ratio of 30% or more to satisfy TS / YS ≤ 1.5 representing the ratio of yield strength (YS) and tensile strength (TS); and열연 소둔하는 단계를 포함하는 성형성이 우수한 페라이트계 스테인리스 열연강판의 제조방법.Method for producing a ferritic stainless steel hot-rolled steel sheet with excellent formability comprising the step of hot-rolling annealing.
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JP2001098327A (en) * | 1999-09-24 | 2001-04-10 | Kawasaki Steel Corp | Method of producing ferritic stainless steel excellent in ductility, workability and ridging resistance |
JP2001207244A (en) * | 1999-09-09 | 2001-07-31 | Kawasaki Steel Corp | Cold rolled ferritic stainless steel sheet excellent in ductility, workability and ridging resistance, and its manufacturing method |
JP2015196842A (en) * | 2014-03-31 | 2015-11-09 | 新日鐵住金ステンレス株式会社 | Austenitic stainless steel excellent in hot workability and hydrogen embrittlement resistance and production method therefor |
KR20200032899A (en) * | 2018-09-19 | 2020-03-27 | 주식회사 포스코 | Manufacturing method of ferritic stainless steel having excellent ridging property and formability |
US20210269890A1 (en) * | 2018-07-18 | 2021-09-02 | Jfe Steel Corporation | Ferritic stainless steel sheet and method of producing same |
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JP2001207244A (en) * | 1999-09-09 | 2001-07-31 | Kawasaki Steel Corp | Cold rolled ferritic stainless steel sheet excellent in ductility, workability and ridging resistance, and its manufacturing method |
JP2001098327A (en) * | 1999-09-24 | 2001-04-10 | Kawasaki Steel Corp | Method of producing ferritic stainless steel excellent in ductility, workability and ridging resistance |
JP2015196842A (en) * | 2014-03-31 | 2015-11-09 | 新日鐵住金ステンレス株式会社 | Austenitic stainless steel excellent in hot workability and hydrogen embrittlement resistance and production method therefor |
US20210269890A1 (en) * | 2018-07-18 | 2021-09-02 | Jfe Steel Corporation | Ferritic stainless steel sheet and method of producing same |
KR20200032899A (en) * | 2018-09-19 | 2020-03-27 | 주식회사 포스코 | Manufacturing method of ferritic stainless steel having excellent ridging property and formability |
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