US20170327923A1 - Super duplex stainless steel having excellent yield strength and impact toughness and menufacturing method therefor - Google Patents

Super duplex stainless steel having excellent yield strength and impact toughness and menufacturing method therefor Download PDF

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US20170327923A1
US20170327923A1 US15/536,356 US201515536356A US2017327923A1 US 20170327923 A1 US20170327923 A1 US 20170327923A1 US 201515536356 A US201515536356 A US 201515536356A US 2017327923 A1 US2017327923 A1 US 2017327923A1
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stainless steel
yield strength
duplex stainless
super duplex
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Jong Jin Jeon
Dong Ik Shin
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Posco Holdings Inc
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Posco Co Ltd
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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
    • 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
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • 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
    • 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
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling

Definitions

  • the present disclosure relates to super duplex stainless steel and a method for manufacturing the same, and in particular, to super duplex stainless steel having excellent yield strength and impact toughness, wherein a reduction ratio and a heat treatment temperature are controlled so as to improve mechanical properties.
  • super duplex stainless steel containing 24% to 26% of chromium (Cr), 6.0% to 8.0% of nickel (Ni), 3.0% to 5.0% of molybdenum (Mo) and 0.24% to 0.32% of nitrogen (N) is dual-phase stainless steel formed with a dual-phase structure of austenite and ferrite, and has been used as materials of desulfurization facilities and seawater pipes with very excellent acid resistance and mechanical properties.
  • a matrix structure of such super duplex stainless steel has a structure property of a ferrite phase and an austenite phase being formed in an equal ratio.
  • super duplex stainless steel has great advantages of exhibiting higher strength compared to austenitic stainless steel and exhibiting excellent resistance for pitting corrosion for chloride ions and stress corrosion cracks.
  • super duplex stainless steel contains large quantities of chromium (Cr) and molybdenum (Mo) for securing acid resistance, and therefore, when maintained in a 750° C. to 850° C. region, causes a problem of degrading product qualities such as strengthening brittleness by readily producing a sigma phase, and significantly reducing acid resistance.
  • Cr chromium
  • Mo molybdenum
  • Such a sigma phase is very quickly produced in a specific temperature range (750° C. to 850° C.), and therefore, when annealing super duplex stainless steel, being delayed in a specific temperature range that readily produces a sigma phase needs to be avoided by controlling a temperature raising rate.
  • “Method for continuous annealing of super duplex stainless steel with excellent impact toughness and coil shape Korean Patent Application Laid-Open Publication No. 10-2013-0034350” and the like specifically disclose a method of avoiding a temperature zone readily producing a sigma phase by raising a temperature from 600° C. to an annealing temperature at a temperature raising rate of 10° C./s or higher, and maintaining the temperature at 1,060° C. to 1,080° C.
  • the annealing method may be normally used in a hot rolled coil having a thickness of 8 mm or less, however, the same heat treatment method may also be used in a thick plate having a thickness of 10 mm or greater.
  • a phenomenon not satisfying 0.2% off-set yield strength of 550 MPa or greater over a plate with various thicknesses from 5 mm to 50 mm frequently occurs.
  • the present disclosure has been made in view of the above, and is directed to providing super duplex stainless steel having excellent yield strength and impact toughness, wherein a reduction ratio and an annealing condition are controlled so as to improve mechanical properties when manufacturing thick super duplex stainless steel, and a method for manufacturing the same.
  • Super duplex stainless steel having excellent yield strength and impact toughness relates to thick super duplex stainless steel having a thickness of 30 mm or greater, and includes, in weight %, Cr: 24% to 26%, Ni: 6.0% to 8.0%, Mo: 3.5% to 5.0%, N: 0.24% to 0.32%, and the remainder being Fe and inevitable impurities, wherein a microstructure includes a ferrite phase, an austenite phase and a secondary austenite phase, and a grain size is 25 ⁇ m or less.
  • the super duplex stainless steel has the yield strength of 550 MPa or greater.
  • a sum of the yield strength and the impact toughness of the super duplex stainless steel is 750 or greater.
  • a method for manufacturing super duplex stainless steel having excellent yield strength and impact toughness includes casting of preparing a slab including, in weight %, Cr: 24% to 26%, Ni: 6.0% to 8.0%, Mo: 3.5% to 5.0%, N: 0.24% to 0.32%, and the remainder being Fe and inevitable impurities; hot rolling of hot rolling the slab to prepare a thick plate having a thickness of 30 mm or greater; temperature raising of raising a temperature of the thick plate to an annealing temperature to precipitate a CrN phase inside a ferrite phase, and precipitating a sigma phase and a secondary austenite phase around the CrN phase; and annealing of keeping the secondary austenite phase inside the ferrite phase while solid dissolving the sigma phase and the CrN phase in the ferrite phase.
  • the temperature raising is raising the temperature from 700° C. to the annealing temperature at a rate of at a rate of 0.11° C./s to 0.17° C./s.
  • the annealing anneals for 20 minutes to 60 minutes at a temperature of 1020° C. to 1060° C.
  • the hot rolling is rolling with a reduction ratio of 80% or greater so that a grain size of a microstructure becomes 25 ⁇ m or less.
  • effects of enhancing mechanical properties such as yield strength and impact toughness of thick super duplex stainless steel are obtained by inducing CrN phase precipitation and facilitating secondary austenite phase formation inside a ferrite phase.
  • FIG. 1 is a graph showing formation behaviors of a sigma phase and a CrN phase depending on a temperature raising rate when annealing.
  • FIG. 2 shows pictures of a microstructure at temperatures of 800° C., 1000° C. and 1040° C. depending on a temperature raising rate.
  • FIG. 3 is a diagram showing a behavior of precipitate depending on an annealing temperature and an annealing time, and its microstructure.
  • FIG. 4 is a graph showing yield strength and impact toughness depending on an annealing condition.
  • FIG. 5 is a graph showing a relation between a thick plate thickness (reduction ratio) and a grain size.
  • FIG. 6 shows pictures comparing microstructures of super duplex stainless steel having excellent yield strength and impact toughness manufactured according to one embodiment of the present disclosure and a comparative sheet.
  • Super duplex stainless steel having excellent yield strength and impact toughness includes, in weight %, Cr: 24% to 26%, Ni: 6.0% to 8.0%, Mo: 3.5% to 5.0%, N: 0.24% to 0.32%, and the remainder being Fe and inevitable impurities.
  • Chromium (Cr) is a ferrite-stabilizing element, and is an essential element for securing acid resistance as well as performing a main role in securing a ferrite phase. Acid resistance increases when the chromium (Cr) content increase, however, when added in excess of greater than 26%, the content of austenite-forming elements such as high-priced nickel (Ni) increases for maintaining a phase fraction, and as a result, manufacturing costs increase.
  • the chromium (Cr) content is preferably limited to a range of 24 wt % to 26 wt %.
  • Nickel (Ni) is an austenite-stabilizing element together with manganese (Mn), copper (Cu) and nitrogen (N), and performs a main role in increasing austenite phase stability. Accordingly, the content is limited to 6.0 wt % to 8.0 wt % for maintaining a phase fraction of the ferrite phase and the austenite phase.
  • Molybdenum (Mo) is an element very effective in improving acid resistance while stabilizing ferrite together with chromium (Cr), but has a disadvantage of being very high-priced. Accordingly, the molybdenum (Mo) content is preferably limited to 3.5 wt % to 5.0 wt %.
  • Nitrogen (N) is an element greatly contributing to austenite phase stabilization together with carbon (C) and nickel (Ni), and, as one of the elements causing thickening to the austenite phase during annealing, an increase in the acid resistance and high strengthening may be obtained concomitantly when increasing the nitrogen (N) content, however, when the nitrogen (N) content is excessive, surface defects caused by the generation of nitrogen pores may be induced during casting due to an excessive nitrogen (N) solid solubility, and therefore, the nitrogen (N) content is preferably limited to 0.24 wt % to 0.32 wt %.
  • a grain size of a microstructure including a ferrite phase, an austenite phase and a secondary austenite phase is preferably formed as 25 ⁇ m or less.
  • yield strength is 550 MPa or greater, and a sum of yield strength and impact toughness is 750 or greater.
  • a method for manufacturing super duplex stainless steel having excellent yield strength and impact toughness includes a casting step of preparing a slab by continuously casting molten steel having the above-mentioned composition, a rolling step of hot rolling the slab to produce a thick plate, a temperature raising step of heating the thick plate, and an annealing step.
  • a temperature raising rate, annealing temperature and time, and a reduction ratio are controlled to control a microstructure, and more specifically, by controlling a temperature raising rate in the temperature raising step, precipitation of a CrN phase is induced during a temperature rise, and then precipitation of a sigma phase and a secondary austenite phase is induced around the CrN phase, and as the sigma phase precipitated in the temperature raising step is solid dissolved inside the ferrite by controlling annealing temperature and time in the annealing step, the secondary austenite phase remains inside the ferrite phase.
  • FIG. 1 is a graph showing formation behaviors of the sigma phase and the CrN phase depending on the temperature raising rate when annealing
  • FIG. 2 shows pictures of a microstructure at temperatures of 800° C., 1000° C. and 1040° C. depending on the temperature raising rate.
  • the temperature raising step is preferably raising the temperature from 700° C. to the annealing temperature having a temperature range of 1030° C. to 1050° C. at a rate of 0.11° C./s to 0.17° C./s.
  • FIG. 3 is a diagram showing a behavior of precipitate depending on the annealing temperature and the annealing time, and its microstructure
  • FIG. 4 is a graph showing yield strength and impact toughness depending on the annealing condition.
  • the annealing step according to one embodiment of the present disclosure is carried out for 20 minutes to 40 minutes at a temperature of 1020° C. to 1060° C., and more preferably, the annealing step of the present disclosure varies the annealing time depending on the annealing temperature.
  • the annealing time is from 20 minutes to 40 minutes
  • the annealing temperature is from 1020° C. to 1030° C.
  • the annealing time is from 40 minutes to 60 minutes
  • the annealing temperature is from 1050° C. to 1060° C.
  • the annealing time is from 5 minutes to 20 minutes.
  • FIG. 5 is a graph showing, when producing a thick plate by rolling a 150 mm slab, a relation between the thick plate thickness (reduction ratio) and a grain size
  • FIG. 6 shows pictures comparing microstructures of the super duplex stainless steel having excellent yield strength and impact toughness manufactured according to one embodiment of the present disclosure and a comparative sheet.
  • a reduction ratio of the slab is preferably 80% or greater.
  • a thick steel plate having a thickness of 30 mm or greater has yield strength reduced to 550 MPa, and does not satisfy the ASTM standards. This may be improved through a method of controlling a microstructure, however, by using a reduction ratio of 82.5%, yield strength may be enhanced while forming a grain size of a microstructure as 25 ⁇ m or less.
  • the super duplex stainless steel having excellent yield strength and impact toughness according to one embodiment of the present disclosure may have a thickness of 30 mm or greater.
  • the present disclosure may be useful for a thick steel plate.
  • the upper limit of the thickness is not particularly limited, and for example, may be 100 mm, 70 mm or 50 mm.
  • the inventors of the present disclosure formed a CrN phase during heat treatment, and then finely precipitated a sigma phase and a secondary austenite phase inside a ferrite phase, by controlling a temperature raising rate to 0.11° C./s to 0.17° C./s or lower during annealing.
  • annealing was carried out for 20 minutes to 60 minutes in a temperature range of 1020° C. to 1060° C. to solid dissolving all the sigma phase while keeping the secondary austenite phase inside the ferrite phase, and as a result, yield strength and impact properties of a thick plate having a thickness of 30 mm or greater were both improved.
  • Table 1 shows a slab thickness (reduction ratio), a temperature raising rate, an annealing temperature and an annealing time for various examples and comparative examples.
  • a steel to Y steel that are examples and comparative examples were heated at a rate of 5° C./s to 700° C., and heated at temperature raising rates of 1.3° C./s, 0.66° C./s, 0.33° C./s and 0.17° C./s from 700° C. to an annealing temperature, and the annealing temperature was 1000° C., 1020° C., 1040° C., 1060° C. and 1080° C., and the annealing time was for 20 minutes, 40 minutes and 60 minutes each, and water cooling was carried out after the heat treatment.
  • Table 2 shows changes in the microstructure occurring during a temperature raising process when carrying out hot rolling and heat treatment under the conditions described in Table 1.
  • a CrN phase was finely formed inside a ferrite phase in the temperature range of 700° C. to 800° C. during the temperature raising process as the temperature raising rate becomes low of 0.33° C./s, and a secondary austenite phase remained inside the ferrite phase in the temperature range of 1020° C. to 1060° C.
  • P steel to U steel had a temperature raising rate of 0.17° C./s, which tends to be similar to K steel to O steel, however, as the amount of CrN phase precipitation increased, the remaining secondary austenite phase increased as well.
  • a steel to U steel had a reduction ratio of 77% resulting in the coarsening of the final microstructure grain, and the size became greater than 25 ⁇ m, which is outside the scope of the present disclosure.
  • V steel to X steel satisfying the embodiments of the present disclosure with a reduction ratio of 82.5%, a temperature raising rate of 0.17° C./s, and an annealing temperature of 1020° C. to 1060° C. a secondary austenite phase remained inside a ferrite phase in the temperature region of 1020° C. to 1060° C. while properly precipitating a CrN phase in the temperature raising process in some of V steel and X steel and all of W steel depending on the annealing time, and most fine structures were secured.
  • Y steel was outside the scope of the present disclosure with a secondary austenite phase being solid dissolved with an annealing temperature of 1080° C.
  • Table 3 shows properties for representative steel types (T, R, W) of Table 2.
  • a JIS 5 tensile specimen was collected in a 90° direction of the rolling direction and a tensile test was carried out at a crosshead speed of 20 mm/min at room temperature.
  • the grain became coarse with a reduction ratio of 77%, and the size was greater than 25 ⁇ m, a standard value, and particularly in R steel, the yield strength was 536 MPa, which was less than 550 MPa, a standard value, and a sum of the yield strength and the impact toughness was 708 MPa, which was also less than 750 MPa, a standard value, and it was seen that yield strength and impact toughness properties were not enhanced.
  • the yield strength and a sum of the yield strength and the impact toughness satisfied the standard values, however, the grain size was greater than 25 ⁇ m, a standard value, with a reduction ratio of 77%.
  • the reduction ratio was 82.5%
  • the annealing temperature, the annealing time and the temperature raising rate satisfied the scope of the present disclosure, and as a result, the grain size was fine with 25 ⁇ m or less, and the yield strength and the impact toughness were enhanced with the yield strength being 585 MPa and a sum of the yield strength and the impact toughness being 778 MPa, and it was identified that mechanical properties were enhanced compared to the comparative sheets.

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US15/536,356 2014-12-26 2015-12-22 Super duplex stainless steel having excellent yield strength and impact toughness and menufacturing method therefor Abandoned US20170327923A1 (en)

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KR1020140191169A KR101668532B1 (ko) 2014-12-26 2014-12-26 항복강도 및 충격인성이 우수한 슈퍼 듀플렉스 스테인리스강 및 그 제조방법
KR10-2014-0191169 2014-12-26
PCT/KR2015/014114 WO2016105094A1 (fr) 2014-12-26 2015-12-22 Acier inoxydable super duplex présentant une excellente limite d'élasticité et résistance aux chocs et son procédé de fabrication

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CN114346142A (zh) * 2022-01-18 2022-04-15 山西太钢不锈钢股份有限公司 一种提高s32750超级双相不锈钢圆钢低温冲击韧性的锻造方法
CN114657335A (zh) * 2022-04-01 2022-06-24 山西太钢不锈钢股份有限公司 超级双相不锈钢及其退火方法

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CN109385507B (zh) * 2018-12-20 2020-06-09 四川民盛特钢锻造有限公司 一种超低碳双相不锈钢钵体的热处理方法
CN114164373B (zh) * 2021-11-10 2022-11-11 中国兵器科学研究院宁波分院 一种Nb微合金化双相不锈钢及其制备方法
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CN113523166A (zh) * 2021-07-21 2021-10-22 苏州雷格姆海洋石油设备科技有限公司 深海连接器用25%Cr大壁厚超级双目不锈钢锻件的生产工艺
CN114346142A (zh) * 2022-01-18 2022-04-15 山西太钢不锈钢股份有限公司 一种提高s32750超级双相不锈钢圆钢低温冲击韧性的锻造方法
CN114657335A (zh) * 2022-04-01 2022-06-24 山西太钢不锈钢股份有限公司 超级双相不锈钢及其退火方法

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KR101668532B1 (ko) 2016-10-24
EP3239340A1 (fr) 2017-11-01
JP2018501403A (ja) 2018-01-18
CN107109603B (zh) 2019-05-07
CN107109603A (zh) 2017-08-29

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