WO2022131503A1 - Acier inoxydable ferritique présentant une excellente résistance à la chaleur et son procédé de fabrication - Google Patents

Acier inoxydable ferritique présentant une excellente résistance à la chaleur et son procédé de fabrication Download PDF

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Publication number
WO2022131503A1
WO2022131503A1 PCT/KR2021/014156 KR2021014156W WO2022131503A1 WO 2022131503 A1 WO2022131503 A1 WO 2022131503A1 KR 2021014156 W KR2021014156 W KR 2021014156W WO 2022131503 A1 WO2022131503 A1 WO 2022131503A1
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heat resistance
stainless steel
ferritic stainless
excellent heat
tensile strength
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PCT/KR2021/014156
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English (en)
Korean (ko)
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박지언
백종수
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주식회사 포스코
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Publication of WO2022131503A1 publication Critical patent/WO2022131503A1/fr

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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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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 having excellent heat resistance and a method for manufacturing the same, and more particularly, to a ferritic stainless steel capable of improving the heat resistance of a material by controlling a solid solution alloy component in a final matrix through component system control, and manufacturing the same it's about how
  • Ferritic stainless steel is a steel material with high price competitiveness compared to austenitic stainless steel because it has excellent corrosion resistance while adding a small amount of expensive alloying elements.
  • Such ferritic stainless steel is used for exhaust manifold, which is an exhaust system component. Since the exhaust system exhaust manifold is directly exposed to high temperature exhaust gas of 700°C or higher, very high safety is required in a long-term operation environment.
  • Embodiments of the present invention by optimizing the steel composition and manufacturing process to control the solid solution alloy composition in the final matrix to improve the heat resistance of the material.
  • Ferritic stainless steel having excellent heat resistance according to an embodiment of the present invention, by weight, C: 0.0005 to 0.02%, N: 0.005 to 0.02%, Si: 0.01 to 1.0%, Mn: 0.01 to 1.2%, P : 0.001 to 0.05%, Cr: 10.0 to 25.0%, Mo: 1.5 to 3.0%, Nb: 0.3 to 0.7%, W: 0.5 to 2.0%, the remainder including Fe and unavoidable impurities, the weight ratio of dissolved Mo in the matrix 85% or more, the weight ratio of solid solution W is included as 85% or more, and the following formulas (1) and (2) are satisfied.
  • the ferritic stainless steel having excellent heat resistance may have a tensile strength of 47 MPa or more at 900°C.
  • the tensile strength reduction rate may be 10% or less.
  • the method for producing a ferritic stainless steel having excellent heat resistance is, by weight, C: 0.0005 to 0.02%, N: 0.005 to 0.02%, Si: 0.01 to 1.0%, Mn: 0.01 to 1.2%, P: 0.001 to 0.05%, Cr: 10.0 to 25.0%, Mo: 1.5 to 3.0%, Nb: 0.3 to 0.7%, W: 0.5 to 2.0%, including the remainder of Fe and unavoidable impurities, the following formula (1) and (2) by reheating the slab satisfying the condition, rough rolling, and finishing rolling to prepare a hot-rolled steel sheet; hot-rolling annealing at 1,020 to 1,100°C; and cold rolling, followed by cold rolling annealing at 1,050 to 1,100° C., wherein the holding time (seconds) before the start of the finish rolling satisfies the following Equation (3).
  • the ferritic stainless steel according to an embodiment of the present invention may provide a ferritic stainless steel having excellent heat resistance by increasing the amount of a solid solution alloy in a matrix.
  • the weight ratio of Mo and W dissolved in the matrix is 85% or more, and the tensile strength reduction rate is 10% or less, so high stability is secured even when used for a long time can do.
  • 1 is a graph showing the tensile strength of 900 °C according to the solid solution Mo and the solid solution W.
  • FIG. 2 is a graph showing the change in tensile strength at 900°C before/after heat treatment at 900°C for 100 hours.
  • Ferritic stainless steel having excellent heat resistance according to an embodiment of the present invention, by weight, C: 0.0005 to 0.02%, N: 0.005 to 0.02%, Si: 0.01 to 1.0%, Mn: 0.01 to 1.2%, P : 0.001 to 0.05%, Cr: 10.0 to 25.0%, Mo: 1.5 to 3.0%, Nb: 0.3 to 0.7%, W: 0.5 to 2.0%, the remainder including Fe and unavoidable impurities, the weight ratio of dissolved Mo in the matrix 85% or more, the weight ratio of solid solution W is included as 85% or more, and the following formulas (1) and (2) are satisfied.
  • Ferritic stainless steel having excellent heat resistance according to an embodiment of the present invention, by weight, C: 0.0005 to 0.02%, N: 0.005 to 0.02%, Si: 0.01 to 1.0%, Mn: 0.01 to 1.2%, P : 0.001 to 0.05%, Cr: 10.0 to 25.0%, Mo: 1.5 to 3.0%, Nb: 0.3 to 0.7%, W: 0.5 to 2.0%, remaining Fe and unavoidable impurities.
  • the unit is % by weight.
  • the content of C (carbon) is 0.0005 to 0.02%.
  • C is an element that greatly affects strength. If its content is less than 0.0005%, the refining price to reduce strength and make high-purity products is high. If it exceeds 0.02%, impurities in the material increase, resulting in elongation and work hardening index (n value) is decreased, and DBTT is increased to deteriorate the impact properties.
  • the content of N (nitrogen) is 0.005 to 0.02%.
  • N is an element that promotes recrystallization by precipitating austenite during hot rolling. If the content is less than 0.005%, TiN crystallization decreases and the equiaxed crystal rate of the slab decreases. On the other hand, when it exceeds 0.02%, impurities in the material increase, resulting in lower elongation, and higher DBTT, thereby lowering impact properties.
  • the content of Si is 0.01 to 1.0%.
  • Si is an element added for deoxidation of molten steel and stabilization of ferrite during steelmaking. If the content is less than 0.01%, the refining price increases, and if it exceeds 1.0%, impurities in the material increase, resulting in elongation and work hardening index ( n value) decreases, and Si-based inclusions increase, resulting in poor workability.
  • the content of Mn (manganese) is 0.01 to 1.2%.
  • Mn is an effective element for improving corrosion resistance, and when its content is less than 0.01%, there is a problem in that the refining price increases, and when it exceeds 1.2%, impurities in the material increase and elongation is lowered.
  • the content of P (phosphorus) is 0.001 to 0.05%.
  • P is an impurity contained inevitably in steel.
  • the content is controlled to less than 0.001%, the refining price increases, and when it exceeds 0.05%, the elongation and work hardening index are lowered due to the increase of impurities.
  • the content of Cr (chromium) is 10.0 to 25.0%.
  • Cr is an element effective for improving corrosion resistance and oxidation resistance of steel, and is added in an amount of 10.0% or more in the present invention. However, if the content is excessive, elongation is lowered and hot-rolled sticking defects occur, so it is limited to 25.0% or less.
  • the content of Mo (molybdenum) is 1.5 to 3.0%.
  • Mo serves to increase the corrosion resistance of ferritic stainless steel and at the same time improve the high-temperature strength. If the Mo content is less than 1.5%, the amount of solid solution in the material is small, so high-temperature strength and thermal fatigue properties deteriorate, and the probability of abnormal oxidation increases. In addition, if it exceeds 3.0%, the impact properties are deteriorated, the risk of fracture during processing increases, and there is a problem of increased cost.
  • Nb niobium
  • the Nb content is less than 0.3%, there is a problem that the high-temperature strength is lowered because the amount of solid solution in the material is small, and if it exceeds 0.7%, the Nb-based precipitates and the high-solute capacity are excessively increased, and the elongation and impact properties are lowered.
  • the content of W (tungsten) is 0.5 to 2.0%.
  • W increases the corrosion resistance of the ferritic stainless steel and at the same time improves the high temperature strength. Therefore, it is preferable to add 0.5% or more, and if it is less than 0.5%, there is a problem in that the amount of solid solution in the material is small and the high temperature strength is lowered. On the other hand, if it exceeds 2.0%, there is a problem in that excessive precipitates are generated and cracks occur frequently during processing.
  • the remainder of the stainless steel except for the above-mentioned alloying elements consists of Fe and other unavoidable impurities.
  • Equation (1) a range of components for improving heat resistance was derived using Equation (1).
  • Equation (1) has a value less than 3, the 900° C. tensile strength value is less than 47 Mpa, and the reduction rate of the tensile strength after heat treatment exceeds 10%, making it difficult to secure the target heat resistance.
  • the weight ratio of dissolved Mo means a ratio to the weight% of Mo dissolved in the matrix among weight% of the total Mo, and the same applies to W.
  • Equation (2) was derived in order to secure the target heat resistance.
  • the value of formula (2) is more than 8, the dissolved Mo is less than 85%, the dissolved W is less than 85%, so that the tensile strength at 900°C is less than 47Mpa, and the decrease in tensile strength after heat treatment exceeds 10% . Therefore, in order to ensure the target heat resistance, the value of Formula (2) is controlled to 8 or less.
  • the ferritic stainless steel having excellent heat resistance of the present invention requires not only component control but also control of the hot rolling process so that Mo, W and Nb do not precipitate in the laves phase in order to secure target heat resistance.
  • the method for producing a ferritic stainless steel having excellent heat resistance is, by weight, C: 0.0005 to 0.02%, N: 0.005 to 0.02%, Si: 0.01 to 1.0%, Mn: 0.01 to 1.2%, P: 0.001 to 0.05%, Cr: 10.0 to 25.0%, Mo: 1.5 to 3.0%, Nb: 0.3 to 0.7%, W: 0.5 to 2.0%, reheating the slab containing the remaining Fe and unavoidable impurities and rough rolling , the rough-rolled bar may be finish-rolled, the finish-rolled hot-rolled steel sheet may be wound, and the wound hot-rolled coil may be subjected to annealing heat treatment.
  • the hot-rolled reheating temperature of the slab must be controlled to 1,100° C. or higher. At this time, if the reheating temperature is too high, crystal grains may become coarse, so it is limited to 1,300° C. or less.
  • the total reduction ratio of the last two passes of rough rolling may be set to 50% or more in order to impart strain energy.
  • Rough rolling is typically composed of three to four rolling mills, the last two passes in the present invention may mean the last rolling mill and the second to last rolling mill.
  • the time (seconds) for which the rough-rolled rough-rolled bar is maintained before the start of finish rolling may satisfy Equation (3) below.
  • RHT means reheating temperature (°C).
  • the time maintained until finish rolling is 8,000/(reheating temperature (°C) - 1,000) seconds or more to give sufficient recrystallization time, and limiting it to 120 seconds or less to prevent coarsening of grains. This is to further impart a deformed structure during finish rolling to prevent coarsening of the precipitates and to be employed in the subsequent annealing process.
  • the winding temperature of the finish-rolled hot-rolled steel sheet may be 450 to 700 °C.
  • the coiling temperature should be controlled to 700° C. or less to prevent coarsening of the precipitates precipitated during hot rolling and to prevent precipitation in the form of labes, and it is preferable to control it to 450° C. or higher for shape and surface quality.
  • the hot-rolled material manufactured in this way must be subjected to hot-rolling annealing at 1020°C or higher, and cold-rolled annealing at 1050°C or higher after cold rolling.
  • the final product undergoes an annealing process, and the weight ratio of Mo and W dissolved in the matrix is 85% or more, and the tensile strength reduction rate is 10% or less, thereby securing the target heat resistance.
  • the coiling temperature and the annealing temperature are different from the manufacturing method according to an embodiment of the present invention, that is, the coiling temperature exceeds 700 °C, and the hot rolling/cold rolling annealing temperature is less than 1000 °C, even if the target component is secured, dissolved Mo and W are less than 85%, so the desired heat resistance cannot be secured.
  • High-temperature tensile strength of the final product was evaluated by performing a test at 900°C according to the JIS G 0567 method, and after maintaining at 900°C for 100 hours, high-temperature tensile strength was again measured at 900°C. Then, the amount of each alloying element was measured by extracting the precipitate residue from the material, and the difference was obtained from the amount of the added alloying element to measure the ratio of dissolved alloying elements. Each result is shown in Table 2.
  • the tensile strength at 900°C high temperature should be 47MPa or more, and the tensile strength reduction rate should be less than 10% even after long-time heat treatment.
  • the steel grades of Examples 1 to 3 satisfy that the value of Formula (1) is 3 or more and the value of Formula (2) is 8 or less, and the weight ratio of dissolved Mo and W is 85% or more , and it was confirmed that the tensile strength at 900°C was 49Mpa or more.
  • the 900°C tensile strength was 47Mpa or higher, confirming that the 900°C tensile strength reduction rate was 10% or less.
  • Comparative Example 4 the content of Mo, W, and Nb is included in the component range of the present invention, and the value of Formula (1) is 3 or more, but the value of Formula (2) is more than 8, resulting in a tensile strength of 900°C It was less than 47Mpa, and the rate of decrease in tensile strength at 900°C exceeded 10%.
  • the content of Mo, W, and Nb was included in the component range of the present invention, the value of Formula (1) was 3 or more, and the value of Formula (2) was 8 or less, It was confirmed that the coiling temperature was higher than 700 °C, the annealing temperature was lower than 1,000 °C, and the dissolved Mo and W were less than 85%, so that the desired heat resistance could not be obtained.
  • 1 is a graph showing the tensile strength of 900 °C according to the solid solution Mo and the solid solution W.
  • the dissolved Mo or W was less than 85%, it was confirmed that the 900°C tensile strength was less than 47Mpa, and when the dissolved Mo and W were 85% or more, the 900°C tensile strength was 47Mpa or more.
  • FIG. 2 is a graph showing the change in tensile strength at 900°C before/after heat treatment at 900°C for 100 hours.
  • Comparative Examples 1 to 6 in which dissolved Mo or W was less than 85%, it was confirmed that the tensile strength reduction rate after heat treatment at 900 ° C was more than 10%, and in Examples 1 to 3 in which dissolved Mo or W was 85% or more, tensile strength after heat treatment at 900 ° C. It was confirmed that the strength reduction rate was 10% or less.
  • the ferritic stainless steel having excellent heat resistance according to an example of the present invention improves heat resistance by increasing the amount of solid solution alloy in the matrix, and the weight ratio of Mo and W dissolved in the matrix after heat treatment at 900° C. for 100 hours is 85% or more, Because the tensile strength reduction rate is less than 10%, high stability can be secured even when used for a long time.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

La présente invention concerne un acier inoxydable ferritique présentant une excellente résistance à la chaleur par l'intermédiaire de la commande d'un système de composants. L'acier inoxydable ferritique présentant une excellente résistance à la chaleur selon un mode de réalisation de la présente invention comprend, en pourcentage en poids, de 0,0005 à 0,02 % de C, de 0,005 à 0,02 % de N, de 0,01 à 1,0 % de Si, de 0,01 à 1,2 % de Mn, de 0,001 à 0,05 % de P, de 10,0 à 25,0 % de Cr, de 1,5 à 3,0 % de Mo, de 0,3 à 0,7 % de Nb, de 0,5 à 2,0 % de W, et le reste étant du Fe et des impuretés inévitables. Dans une matrice, une proportion en poids de solution solide de Mo supérieure ou égale à 85 % et une proportion en poids de solution solide de W supérieure ou égale à 85 % sont incluses et les expressions (1) et (2) ci-dessous sont satisfaites. (1) Mo ＋ W ＋ Nb ≥ 3 (2) (Mo ＋ W)/Nb ≤ 8
PCT/KR2021/014156 2020-12-18 2021-10-14 Acier inoxydable ferritique présentant une excellente résistance à la chaleur et son procédé de fabrication WO2022131503A1 (fr)

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KR1020200178908A KR20220088157A (ko) 2020-12-18 2020-12-18 내열성이 우수한 페라이트계 스테인리스강 및 그 제조방법
KR10-2020-0178908 2020-12-18

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20120108786A (ko) * 2011-03-25 2012-10-05 주식회사 포스코 고온강도가 우수한 페라이트계 스테인리스강의 제조방법
JP2013209726A (ja) * 2012-03-30 2013-10-10 Nippon Steel & Sumikin Stainless Steel Corp 加工性に優れた耐熱フェライト系ステンレス冷延鋼板、冷延素材用フェライト系ステンレス熱延鋼板及びそれらの製造方法
CN105200330A (zh) * 2015-09-24 2015-12-30 宝钢不锈钢有限公司 一种耐高温铁素体不锈钢及其制造方法
KR20180109865A (ko) * 2016-02-02 2018-10-08 닛신 세이코 가부시키가이샤 Nb함유 페라이트계 스테인리스 열연 강판 및 그 제조 방법과, Nb함유 페라이트계 스테인리스 냉연 강판 및 그 제조 방법
KR20200033055A (ko) * 2018-09-19 2020-03-27 주식회사 포스코 가공성과 고온강도가 우수한 페라이트계 스테인리스강 및 그 제조방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20120108786A (ko) * 2011-03-25 2012-10-05 주식회사 포스코 고온강도가 우수한 페라이트계 스테인리스강의 제조방법
JP2013209726A (ja) * 2012-03-30 2013-10-10 Nippon Steel & Sumikin Stainless Steel Corp 加工性に優れた耐熱フェライト系ステンレス冷延鋼板、冷延素材用フェライト系ステンレス熱延鋼板及びそれらの製造方法
CN105200330A (zh) * 2015-09-24 2015-12-30 宝钢不锈钢有限公司 一种耐高温铁素体不锈钢及其制造方法
KR20180109865A (ko) * 2016-02-02 2018-10-08 닛신 세이코 가부시키가이샤 Nb함유 페라이트계 스테인리스 열연 강판 및 그 제조 방법과, Nb함유 페라이트계 스테인리스 냉연 강판 및 그 제조 방법
KR20200033055A (ko) * 2018-09-19 2020-03-27 주식회사 포스코 가공성과 고온강도가 우수한 페라이트계 스테인리스강 및 그 제조방법

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