CN110129682A - A kind of 950MPa grades of TWIP steel and preparation method thereof - Google Patents

A kind of 950MPa grades of TWIP steel and preparation method thereof Download PDF

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Publication number
CN110129682A
CN110129682A CN201910340060.0A CN201910340060A CN110129682A CN 110129682 A CN110129682 A CN 110129682A CN 201910340060 A CN201910340060 A CN 201910340060A CN 110129682 A CN110129682 A CN 110129682A
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China
Prior art keywords
950mpa
twip steel
grades
steel
twip
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CN201910340060.0A
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Chinese (zh)
Inventor
李秋寒
郭子峰
郭佳
张衍
冯军
陈斌
李玉鹏
吕宝锋
赵青
尼兴
范然然
杨业
周娜
徐伟
张嘉琪
宋春华
陈波
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Shougang Group Co Ltd
Beijing Shougang Co Ltd
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Shougang Group Co Ltd
Beijing Shougang Co Ltd
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Priority to CN201910340060.0A priority Critical patent/CN110129682A/en
Publication of CN110129682A publication Critical patent/CN110129682A/en
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The present invention relates to the chemical component of a kind of 950MPa grades of TWIP steel and preparation method thereof, percentage, TWIP steel of the present invention is as follows: C:0.10-0.70%, Si≤0.10%, Mn:15-20%, Al≤0.05%, P≤0.01%, S≤0.008%, Ti≤0.10%, Nb≤0.05%, B:0.0015-0.0035%, RE≤0.10%, remaining is Fe and inevitable impurity, wherein, Ti+RE:0.15-0.2%.

Description

A kind of 950MPa grades of TWIP steel and preparation method thereof
Technical field
The invention belongs to hot-rolled steel production technical fields, and in particular to a kind of 950MPa grades of TWIP steel and preparation method thereof.
Background technique
TWIP steel refers to that the steel grade with twinning induced plasticity effect, TWIP steel not only have high intensity and extension Rate, while also there is high flanging forming performance, it is easier to produce the part of complicated shape.Since comprehensive performance is very excellent Show, therefore attracted the extensive concern of automobile industry.
TWIP steel solves the problems, such as that intensity is difficult to take into account with plasticity, and TWIP steel is mainly at present with cold-rolled products It is main, higher cost, and the addition of a large amount of Mn elements improves and smelts difficulty, high Mn causes coarse columanar structure and high C carbon The defects of compound precipitation causes slab crackle, deteriorates welding performance, so that the market for limiting TWIP steel uses.
Summary of the invention
In view of the above problems, it proposes on the present invention overcomes the above problem or at least be partially solved in order to provide one kind State the 950MPa grade TWIP steel and preparation method thereof of problem.
The embodiment of the present invention provides a kind of 950MPa grades of TWIP steel, percentage, the chemistry of the TWIP steel at Divide as follows: C:0.10-0.70%, Si≤0.10%, Mn:15-20%, Al≤0.05%, P≤0.01%, S≤0.008%, Ti ≤ 0.10%, Nb≤0.05%, B:0.0015-0.0035%, RE≤0.10%, remaining is Fe and inevitable impurity, wherein Ti+RE:0.15-0.2%.
Further, the chemical component of the TWIP steel is as follows: C:0.20-0.40%, Si:0.02-0.06%, Mn:15- 18%, Al≤0.05%, P≤0.01%, S≤0.008%, Nb≤0.04%, Ti:0.1-0.15%, B:0.002- 0.003%, RE:0.05-0.08%, remaining is Fe and inevitable impurity.
Further, the TWIP steel microscopic metallographic structure is austenite and nanoscale precipitated phase.
Further, yield strength >=470MPa of the TWIP steel, tensile strength >=950MPa.
Further, the elongation after fracture A of the TWIP steel80>=45%.
Based on the same inventive concept, the embodiment of the present invention also provides a kind of preparation method of 950MPa grades of hot rolling TWIP steel, Include:
Molten steel is deployed by the chemical component, the molten steel is poured fastly by low temperature, obtains slab；
The slab is heated, obtains and heats steel billet, in the heating process, rate controlling is warming up to 1230-1260 DEG C, and soaking Keep the temperature 1h；
Hot rolling is carried out to the heating steel billet, obtains hot rolled plate, the start rolling temperature of the hot rolling is 1120-1170 DEG C, eventually Rolling temperature is 880-930 DEG C；
The hot rolled plate is cooled to the furnace room temperature simultaneously to 580-640 DEG C, and after furnace inside holding 1h by section cooling It batches, obtains TWIP steel.
Further, the rate controlling heating rate is 3-4.5 DEG C/s.
Further, the hot rolling uses two sections of rolling mill practices.
Further, in the course of hot rolling, the hot rolled plate with a thickness of 6-8mm is obtained by 7 passes.
Further, the cooling rate is 10-20 DEG C/s.
One or more technical solutions in the embodiment of the present invention, have at least the following technical effects or advantages:
TWIP steel provided by the present application, using C-Mn-Nb-Ti-B-RE component system and hot rolling technology, microalloy element Nb Addition with Ti is combined with controlled rolling and control recrystallization technique gives full play to refined crystalline strengthening and precipitation strength effect, so that The microscopic metallographic structure of finished product be tiny austenite structure, and in matrix containing disperse educt tiny (Nb, Ti) (C, N) second phase particles；Precipitation strength mode improves material yield strength and the effect of tensile strength is suitable, is improving yield strength When can minimum elevated material yield tensile ratio, the intensity and plasticity of TWIP steel are enhanced, the defects of so as to avoid slab crackle Generation.
Detailed description of the invention
By reading the following detailed description of the preferred embodiment, various other advantages and benefits are common for this field Technical staff will become clear.The drawings are only for the purpose of illustrating a preferred embodiment, and is not considered as to the present invention Limitation.And throughout the drawings, identical component is indicated with identical reference pattern.In the accompanying drawings:
Fig. 1 shows the tissue micrograph of TWIP steel in the embodiment of the present invention 1；
Fig. 2 shows the precipitated phase micrographs of TWIP steel in the embodiment of the present invention 1.
Specific embodiment
Below in conjunction with specific embodiment and embodiment, it is specifically described the present invention, advantages of the present invention and various effects It thus will clearly present.It will be understood by those skilled in the art that these specific embodiments and embodiment are for illustrating The present invention is not intended to limit the present invention.
Throughout the specification, unless otherwise specified, terms used herein are interpreted as usual in this field Used meaning.Therefore, unless otherwise defined, all technical and scientific terms used herein has leads with belonging to the present invention The identical meaning of the general understanding of field technique personnel.Contradiction if it exists, this specification are preferential.
Unless otherwise specified, various raw material, reagent, the instrument and equipment etc. used in the present invention, can pass through Market is commercially available or can be prepared by existing method.
The application provides a kind of 950MPa grades of TWIP steel, and the chemical component of percentage, the TWIP steel is as follows: C:0.10-0.70%, Si≤0.10%, Mn:15-20%, Al≤0.05%, P≤0.01%, S≤0.008%, Ti≤ 0.10%, Nb≤0.05%, B:0.0015-0.0035%, RE≤0.10%, remaining is Fe and inevitable impurity, wherein Ti + RE:0.15-0.2%.
Preferably, the chemical component of the TWIP steel is as follows: C:0.20-0.40%, Si:0.02-0.06%, Mn:15- 18%, Al≤0.05%, P≤0.01%, S≤0.008%, Nb≤0.04%, Ti:0.1-0.15%, B:0.002- 0.003%, RE:0.05-0.08%, remaining is Fe and inevitable impurity.
In the application, the TWIP steel microscopic metallographic structure is austenite and nanoscale precipitated phase.
In the application, yield strength >=470MPa of the TWIP steel, tensile strength >=950MPa.
In the application, the elongation after fracture A of the TWIP steel80>=45%.
Based on the same inventive concept, the application also provides a kind of preparation method of 950MPa grades of hot rolling TWIP steel, comprising:
Molten steel is deployed by the chemical component, the molten steel is poured fastly by low temperature, obtains slab；
The slab is heated, obtains and heats steel billet, in the heating process, rate controlling is warming up to 1230-1260 DEG C, and soaking Keep the temperature 1h；
Hot rolling is carried out to the heating steel billet, obtains hot rolled plate, the start rolling temperature of the hot rolling is 1120-1170 DEG C, eventually Rolling temperature is 880-930 DEG C；
The hot rolled plate is cooled to the furnace room temperature simultaneously to 580-640 DEG C, and after furnace inside holding 1h by section cooling It batches, obtains TWIP steel.
In the application, the rate controlling heating rate is 3-4.5 DEG C/s.
In the application, the hot rolling uses two sections of rolling mill practices.
In the application, in the course of hot rolling, the hot rolled plate with a thickness of 6-8mm is obtained by 7 passes.
In the application, the cooling rate is 10-20 DEG C/s.
Below in conjunction with six specific embodiments to the 950MPa grade hot rolling TWIP steel of the application and corresponding preparation method It is described in detail.
The chemical component (wt%) of embodiment 1-6 is as shown in table 1.
Table 1
Embodiment C Si Mn Al P S Nb Ti B RE
1 0.33 0.050 16.04 0.01 0.005 0.003 0.036 0.082 0.0023 0.067
2 0.35 0.055 16.25 0.03 0.005 0.004 0.042 0.073 0.0022 0.059
3 0.21 0.042 16.49 0.02 0.006 0.003 0.036 0.080 0.0026 0.063
4 0.32 0.023 17.33 0.03 0.005 0.003 0.030 0.068 0.0025 0.061
5 0.28 0.023 17.68 0.03 0.005 0.004 0.038 0.095 0.0019 0.079
6 0.41 0.039 16.84 0.02 0.005 0.003 0.032 0.103 0.0020 0.046
The main technologic parameters of embodiment 1-6 are as shown in table 2, and technological parameter in addition to this is equal are as follows: in heating process, Heat heat preservation 1 hour；In course of hot rolling, using 7 passes.
Table 2
Embodiment Heating rate Tapping temperature Open bundle temperature Finishing temperature Cooling rate The cold temperature of layer Thickness
1 3.5 1228℃ 1170℃ 907℃ 20℃/s 640℃ 7
2 3.5 1230℃ 1165℃ 930℃ 15℃/s 598℃ 6.5
3 4 1236℃ 1120℃ 900℃ 17℃/s 600℃ 7
4 4 1250℃ 1130℃ 905℃ 13℃/s 610℃ 6.5
5 4.5 1260℃ 1137℃ 880℃ 10℃/s 605℃ 6.5
6 3 1233℃ 1158℃ 900℃ 19℃/s 580℃ 6.5
Mechanics Performance Testing is carried out to the TWIP steel that 1-6 of the embodiment of the present invention is prepared, using GB/T 228-2002 It processes tensile sample (sample marking distance 80mm), acquired results are as shown in table 3.
Table 3
Embodiment Yield strength MPa Tensile strength MPa Elongation after fracture A80(%)
1 577 1011 59.0
2 674 1090 54.0
3 509 1002 47.5
4 471 988 61.5
5 580 1023 52.5
6 644 1130 53.0
The present invention has a characteristic that in alloying component
C content of the invention is C:0.20-0.40%, and carbon enrichment improves its stability in retained austenite, with alloy Element nb and Ti etc. form microalloy carbide and play the role of precipitation strength, but high-carbon content excessively can be formed largely along crystal boundary Carbide adversely affects formability, thus carbon content control is in 0.20-0.40%.
Si content of the invention takes lower silicone content less than 0.06%, the influence of silicon properties of weld when reducing welding.
Mn content of the invention is 15-18%, and displacement solid solution element Mn is austenite former, is remarkably improved Ovshinsky Body tissue stability inhibits Austenite Grain Growth while solution strengthening improves matrix strength, but Mn too high levels can make Steel billet as-cast structure is coarse, and is segregated in crystal boundary influence material weldability and increases temper brittleness tendency, to obtain TWIP effect, Mn content is controlled in 15-18%.
P and S of the invention has an adverse effect to material property, answers P and S content in strict control steel.
Al is as deoxidant element in the present invention, and Al content Shi Huiyu N element below 0.04% forms tiny AlN in steel It is precipitated, plays the role of refining grain structure and precipitation strength, control Al content less than 0.05%.
Nb element can make C be enriched with raising stability of retained austenite in austenite and play refined crystalline strengthening effect in the present invention Fruit.The refined crystalline strengthening effect of Nb basically reaches saturation after content is more than 0.04%, Nb content of the present invention control 0.04% with Under.
0.10% or so Ti is added in the present invention, and it is to inhibit under heating furnace high temperature state that Ti element interaction one, which is added, Austenite grain is grown up.Second, Ti element replaces strip MnS with spherical TiS2, change is mingled with form, prevents austenite grain boundary Place generates rich iron sulfide and causes slab.Third, improving welded steel, the coarsening of seam organization is prevented.
The B element of 0.002-0.003% is added in the present invention, the also available tiny equiax crystal when pouring temperature is higher Tissue strengthens austenite grain boundary, improves the harden ability of austenite structure and the consistency of potassium steel.When carbon content is higher in steel When, B element easily with the compound precipitation of C, interferes B element to play above-mentioned effect.Therefore it while strong carbonitride element is added, examines Consider the rare earth elements RE raising C element solubility that certain content is added.
In steel when compound addition rare earth element not only cleaning molten steel, control inclusion morphology, improve and as-cast structure but also have The effect of solution strengthening and precipitation strength guarantees good plasticity, plays the comprehensive purpose for improving steel performance.
The present invention selects preparation method corresponding with mentioned component system, and is adjusted to the parameter in method, this hair The preparation method of bright embodiment TWIP steel, includes the following steps:
Smelting molten steel casting obtains slab；After the slab is carried out heating and thermal insulation, 5-8mm hot rolling is obtained by rolling Plate, the finishing temperature control is 880-920 DEG C, by the hot rolled plate section cooling to 590-640 DEG C of fed to boiler (furnace temperature 600 DEG C) keep the temperature furnace cooling after 1h.
To dissolve microalloy precipitated phase in slab sufficiently, it is ensured that homogenization of composition, and uniform austenite structure is obtained, The heating temperature of slab is set in 1230~1240 DEG C.Take finishing temperature at 880~920 DEG C sufficiently to refine austenite group It knits.Control laminar flow cooling temperature cools to room temperature with the furnace after 590-620 DEG C of fed to boiler keeps the temperature 1h and obtains austenite structure.
Compared with existing TWIP steel, the TWIP steel of the application is had the following characteristics that
Yield strength reaches 674MPa, and tensile strength reaches 1130MPa, and elongation after fracture A80Up to 61.5%.
Finally, it is to be noted that, the terms "include", "comprise" or its any other variant be intended to it is non-exclusive Property include so that include a series of elements process, method, article or equipment not only include those elements, but also Further include other elements that are not explicitly listed, or further include for this process, method, article or equipment it is intrinsic Element.
Although preferred embodiments of the present invention have been described, it is created once a person skilled in the art knows basic Property concept, then additional changes and modifications may be made to these embodiments.So it includes excellent that the following claims are intended to be interpreted as It selects embodiment and falls into all change and modification of the scope of the invention.
Obviously, various changes and modifications can be made to the invention without departing from essence of the invention by those skilled in the art Mind and range.In this way, if these modifications and changes of the present invention belongs to the range of the claims in the present invention and its equivalent technologies Within, then the present invention is also intended to include these modifications and variations.

Claims (10)

1. a kind of 950MPa grades of TWIP steel, which is characterized in that the chemical component of percentage, the TWIP steel is as follows: C:0.10-0.70%, Si≤0.10%, Mn:15-20%, Al≤0.05%, P≤0.01%, S≤0.008%, Ti≤ 0.10%, Nb≤0.05%, B:0.0015-0.0035%, RE≤0.10%, remaining is Fe and inevitable impurity, wherein Ti + RE:0.15-0.2%.
2. a kind of 950MPa grades of TWIP steel according to claim 1, which is characterized in that TWIP described in percentage The chemical component of steel is as follows: C:0.20-0.40%, Si:0.02-0.06%, Mn:15-18%, Al≤0.05%, P≤ 0.01%, S≤0.008%, Nb≤0.04%, Ti:0.1-0.15%, B:0.002-0.003%, RE:0.05-0.08%, Remaining is Fe and inevitable impurity.
3. a kind of 950MPa grades of TWIP steel according to claim 1 or 2, which is characterized in that the microcosmic metallographic of TWIP steel Tissue is austenite and nanoscale precipitated phase.
4. a kind of 950MPa grades of TWIP steel according to claim 1 or 2, which is characterized in that the surrender of the TWIP steel is strong Degree >=470MPa, tensile strength >=950MPa.
5. a kind of 950MPa grades of TWIP steel according to claim 1 or 2, which is characterized in that the having no progeny for TWIP steel is prolonged Stretch rate A80>=45%.
6. a kind of preparation method of 950MPa grades of hot rollings TWIP steel as described in any one in claim 1-5, which is characterized in that packet It includes:
Molten steel is deployed by the chemical component, the molten steel is poured fastly by low temperature, obtains slab；
The slab is heated, obtains and heats steel billet, in the heating process, rate controlling is warming up to 1230-1260 DEG C, and soaking is kept the temperature 1h；
Hot rolling is carried out to the heating steel billet, obtains hot rolled plate, the start rolling temperature of the hot rolling is 1120-1170 DEG C, finish to gauge temperature Degree is 880-930 DEG C；
The hot rolled plate is cooled to the furnace room temperature and rolled up by section cooling to 580-640 DEG C, and after furnace inside holding 1h It takes, obtains TWIP steel.
7. a kind of preparation method of 950MPa grades of hot rollings TWIP steel according to claim 6, which is characterized in that the rate controlling Heating rate is 3-4.5 DEG C/s.
8. a kind of preparation method of 950MPa grades of hot rollings TWIP steel according to claim 6, which is characterized in that the hot rolling Using two sections of rolling mill practices.
9. a kind of preparation method of 950MPa grades of hot rollings TWIP steel according to claim 6, which is characterized in that the hot rolling In the process, the hot rolled plate with a thickness of 6-8mm is obtained by 7 passes.
10. a kind of preparation method of 950MPa grades of hot rollings TWIP steel according to claim 6, which is characterized in that described cold But rate is 10-20 DEG C/s.
CN201910340060.0A 2019-04-25 2019-04-25 A kind of 950MPa grades of TWIP steel and preparation method thereof Pending CN110129682A (en)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19528671C1 (en) * 1995-08-04 1996-10-10 Thyssen Stahl Ag Steel for linear construction profiles for underground pit mining
KR20100076729A (en) * 2008-12-26 2010-07-06 주식회사 포스코 High tensile steel with excellent low-temperature toughness, manufacturing method thereof and manufacturing method of deep drawing article
CN106521318A (en) * 2016-11-22 2017-03-22 河北工业大学 High-strength Fe-Mn-Al-C-series low density cast steel and preparation method thereof
JP6477983B1 (en) * 2018-03-29 2019-03-06 新日鐵住金株式会社 Austenitic wear-resistant steel sheet
CN109554615A (en) * 2018-12-29 2019-04-02 首钢集团有限公司 A kind of tensile strength 900MPa grades of analysis of producing hot rolled TRIP and preparation method thereof

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19528671C1 (en) * 1995-08-04 1996-10-10 Thyssen Stahl Ag Steel for linear construction profiles for underground pit mining
KR20100076729A (en) * 2008-12-26 2010-07-06 주식회사 포스코 High tensile steel with excellent low-temperature toughness, manufacturing method thereof and manufacturing method of deep drawing article
CN106521318A (en) * 2016-11-22 2017-03-22 河北工业大学 High-strength Fe-Mn-Al-C-series low density cast steel and preparation method thereof
JP6477983B1 (en) * 2018-03-29 2019-03-06 新日鐵住金株式会社 Austenitic wear-resistant steel sheet
CN109554615A (en) * 2018-12-29 2019-04-02 首钢集团有限公司 A kind of tensile strength 900MPa grades of analysis of producing hot rolled TRIP and preparation method thereof

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Application publication date: 20190816