CN110331326A - High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof - Google Patents

High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof Download PDF

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Publication number
CN110331326A
CN110331326A CN201910697090.7A CN201910697090A CN110331326A CN 110331326 A CN110331326 A CN 110331326A CN 201910697090 A CN201910697090 A CN 201910697090A CN 110331326 A CN110331326 A CN 110331326A
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cooled
preparation
hot rolling
1000mpa
dual phase
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CN201910697090.7A
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Inventor
彭欢
胡学文
王海波
闻成才
王泉
王承剑
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Maanshan Iron and Steel Co Ltd
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Maanshan Iron and Steel Co Ltd
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Priority to CN201910697090.7A priority Critical patent/CN110331326A/en
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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

Abstract

The invention discloses high-strength dual phase sheet steels of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof, including following chemical component and weight percent: C:0.10~0.20%；Si:0.80~1.20%；Mn:1.20~2.0%；P :≤0.020%；S :≤0.010%；Ti:0.010~0.040%；Cr:0.20~0.60%；Als:0.020~0.060%；Remaining is Fe and is inevitably mingled with, and is prepared by smelting, continuous casting, heating, hot rolling, cooling and coiling technique.Use thickness specification produced by the invention for the hot rolled steel plate of 3-6mm, its microscopic structure is ferrite+martensite, wherein ferritic volume fraction is 30~40%, Martensite Volume Fraction is 60~70%, yield strength >=550MPa of product, tensile strength >=1000MPa, yield tensile ratio≤0.60, elongation percentage A50>=16%, 180 ° of cold-bending property, D=2a is qualified, intensity with higher, lower yield tensile ratio, preferable forming property.

Description

High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof
Technical field
The invention belongs to hot-rolling high-strength steel technical field of producing, and in particular to a kind of 1000MPa grades of thin gauge hot rolling High-strength dual phase sheet steel and preparation method thereof.
Background technique
Critical component one of of the automotive wheel as automobile, will not only bear gravity, brake force, driving force, the vapour of automobile The lateral force that vehicle generates when turning to, and still suffer from the impact force of Uneven road generation.Therefore, automotive wheel should have gently Matter, high-strength, high rigidity, high fatigue performance etc..With the rapid development of auto industry, lightweight, energy conservation and environmental protection, high security Have become the inexorable trend of its development, this requirement also to wheel comprehensive performance is higher and higher.
Hot-rolled dual-phase steel due to good strong plasticity, low yield strength ratio, high initial work hardening rate, good baking and hardening performance and Anti-fatigue performance etc. is used for the manufacture of automotive wheel by automobile manufacturing enterprises such as general, Ford, Beijing Jeeps.Currently, by The factors such as product surface quality, structure property uniformity are formed on, produces both at home and abroad and the hot-rolled dual-phase steel of application is mainly with DP540 Based on~DP600, the dual phase steel of DP780 and the above rank is still based on cold rolling.Therefore, DP980 and the above rank hot rolling are developed For promoting automotive sheet " with hot Dai Leng ", automotive light weight technology and energy-saving and emission-reduction etc. have great importance dual phase steel.
It does not relate to set by other chemical components about the production technology of 1000MPa grades of hot-rolled dual-phase steels is less at present Meter, and the optimization by rolling cooling coiling technique, it is high to be able to produce out the good 1000MPa grades of thin gauge hot rolling of forming property Strong dual phase steel.
Summary of the invention
The purpose of the present invention is to provide high-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof, Reasonable ingredient design, smelting, continuous casting, heating, hot rolling, cooling and the optimization of coiling technique are crossed, hot-rolled dual-phase steel can be made to obtain While obtaining higher-strength, there is good forming property.This hot-rolled dual-phase steel is mainly used for the vehicle structures such as wheel and is thinned The manufacture of part.
Technical solution provided by the invention are as follows:
A kind of high-strength dual phase sheet steel of 1000MPa grades of thin gauge hot rolling, including following chemical component and weight percent: C: 0.10~0.20%；Si:0.80~1.20%；Mn:1.20~2.0%；P :≤0.020%；S :≤0.010%；Ti:0.010 ~0.040%；Cr:0.20~0.60%；Als:0.020~0.060%；Remaining is Fe and is inevitably mingled with.
Further, it is preferable to which being includes following chemical component and weight percent: C:0.13~0.16%；Si:1.05~ 1.20%；Mn:1.75~1.86%；P :≤0.012%；S :≤0.008%；Ti:0.020~0.028%；Als:0.032~ 0.046%；Remaining is Fe and is inevitably mingled with.
Its microscopic structure of the high-strength dual phase sheet steel of the 1000MPa grades of thin gauge hot rolling is ferrite+martensite, wherein iron The volume fraction of ferritic is 30~40%, and Martensite Volume Fraction is 60~70%；Its yield strength >=550MPa, tensile strength >=1000MPa, yield tensile ratio≤0.60, elongation percentage A50>=16%, 180 ° of cold-bending property D=2a.
The present invention also provides the preparation method of the high-strength dual phase sheet steel of the 1000MPa grades of thin gauge hot rolling, the preparations Method the following steps are included:
(1) it smelts, the refining of LF furnace, continuous casting；
(2) slab enters in heating furnace and is heated；
(3) it rolls, using two-stage control rolling mill practice；
(4) cooling: to use three stage control cooling technique；
(5) it batches, is air-cooled to room temperature after batching.
In step (2), the heating temperature is 1150~1200 DEG C, soaking time 1.5-2h.
In step (3), it is >=70% that reduction ratio is accumulated in roughing, and it is >=80% that reduction ratio is accumulated in finish rolling.
In step (3), roughing start rolling temperature is 1100~1150 DEG C, and finish rolling finishing temperature is 810~860 DEG C.
In step (4), rolling rear steel plate, with the cooling velocity of 30~50 DEG C/s to be cooled to 680~720 DEG C of progress air-cooled, air-cooled After 6~10s, then steel plate is cooled to≤350 DEG C with the cooling velocity of >=50 DEG C/s and is batched.
Further, in step (2), the heating temperature is 1160~1200 DEG C, soaking time 1.7-2.0h；Step (3) in, roughing accumulate reduction ratio be 75~80%, finish rolling accumulate reduction ratio be 81~85%, roughing start rolling temperature be 1118~ 1147 DEG C, finish rolling finishing temperature is 815~850 DEG C.
In step (4), rolling rear steel plate, with the cooling velocity of 35~50 DEG C/s to be cooled to 683~713 DEG C of progress air-cooled, air-cooled Steel plate is cooled to≤346 DEG C again with the cooling velocity of 65~78 DEG C/s and batched by 7.4~9.4s.
Chemical component of the present invention uses C-Si-Mn-Cr mentality of designing, and adds a small amount of Ti element, and strict control P, S etc. The content of impurity element, each component content control are as follows:
C:0.10~0.20%, C play very important effect as the basic element in steel, to the intensity for improving steel, In order to obtain higher intensity, it is necessary to assure the content of C is 0.10% or more, but C content can not be higher than 0.20%, otherwise exist The ferrite of quantity required for obtaining is difficult to after hot rolling in cooling procedure, causes the moulding of steel poor.
Si:0.80~1.20% adds suitable Si, can not only play the effect of solution strengthening, increases the intensity of steel, And can promote ferrite and formed, expand the process window that ferrite is formed, purifies ferrite.Correlative study shows this of Si Kind, which acts on when its content reaches 0.8% or more, just to be showed, but the content of Si can not be too high, and Si too high levels are easy Steel surface generates red scale, influences the surface quality of product.
The intensified element of Mn:1.20~2.0%, Mn as steel can be improved the intensity of steel and improve its harden ability, in order to Guarantee the intensity of steel, Mn content should be controlled 1.20% or more, but Mn content cannot be excessively high, and Mn content is more than that 2.0% slab is inclined A possibility that analysis, dramatically increases, and is not easy to form required amount of ferrite after rolling, and generates unfavorable shadow to the forming property of steel It rings.
P, S is as impurity element, can the forming properties such as punching press, clod wash to steel have an adverse effect, it should strict control, The lower its content the better, considers cost factor, controls P in actual production :≤0.020%, S :≤0.010%.
Carbide in Cr:0.20~0.60%, Cr conduct, is remarkably improved the harden ability of steel, increases difficult to understand The supercooling ability of family name's body postpones pearlite and ferrite transformation, and postpones bainitic transformation, meanwhile, Cr can also play solid solution Invigoration effect, but Cr too high levels can deteriorate the formability and welding performance of steel.
The effect of Ti:0.010~0.040%, Ti in steel mainly plays two, first is that fining austenite grains, and Refining effect is played to the ferrite and martensite that finally change；Second is that forming TiN in conjunction with N element, nitrogen fixation is played.
Als:0.020~0.060%, Als are used mainly as deoxidier, and can be reacted with N and be generated AlN anchoring crystalline substance Grain refinement is played on boundary, if Als too high levels, the coarse AlN particle of generation instead subtracts the grain refinement effect of material It is weak.
The present invention is in hot rolling technology design, and for heating and temperature control at 1150~1200 DEG C, main purpose is to prevent from adding Hot temperature is excessively high, and Si reacts with FeO generate fayalite Fe under the high temperature conditions2SiO4, fayalite can anchoring iron oxide Skin increases its adhesiveness with matrix, and iron scale is caused to be difficult to remove, and the red rust that belt steel surface generates increases, and influences strip Surface quality.
Finishing temperature control at 810~860 DEG C, lower finishing temperature be conducive to refine original austenite grains size and Enter ferrite phase region after rolling steel billet promptly part ferrite is precipitated.Using three-stage Controlled cooling process after rolling: the One-step cooling speed control is in 30-50 DEG C/s, and final cooling temperature is controlled to 680-720 DEG C, and the purpose is to so that material is quickly entered iron Ferritic phase change region；Second segment air cooling time is controlled in 6-10s, and final cooling temperature is controlled to 640-680 DEG C, and its purpose is to obtain Obtain a certain proportion of ferritic structure；The control of third section cooling velocity in 50 DEG C/s or more, oiler temperature control 350 DEG C with Under, the purpose is to make the austenite structure fast transition martensitic structure not changed, thus make steel finally obtain ferrite+ The duplex structure of martensite.
Use thickness specification produced by the invention for the hot rolled steel plate of 3-6mm, microscopic structure is ferrite+martensite, Ferrite average grain size be 6-10 μm, ferritic volume fraction be 30~40%, Martensite Volume Fraction be 60~ 70%, yield strength >=550MPa of product, tensile strength >=1000MPa, yield tensile ratio≤0.60, elongation percentage A50>=16%, it is cold 180 ° of curved performance, D=2a are qualified, intensity with higher, lower yield tensile ratio, preferable forming property.
Detailed description of the invention
Fig. 1 is the metallographic structure figure of the high-strength dual phase sheet steel of 1000MPa grade thin gauge hot rolling in the embodiment of the present invention 1.
Specific embodiment
Technical solution of the present invention is explained below by specific embodiment.
It is C:0.10~0.20% according to chemical component provided by the invention and weight percent content；Si:0.80~ 1.20%；Mn:1.20~2.0%；P :≤0.020%；S :≤0.010%；Ti:0.010~0.040%；Cr:0.20~ 0.60%；Als:0.020~0.060%；Remaining is Fe and is inevitably mingled with, and carries out converter smelting, the refining of LF furnace, connects Casting, rolling, cooling, is batched at heating.
Each embodiment and the chemical component of comparative example are as shown in table 1, and rolling technological parameter is as shown in table 2, and mechanical property is such as Shown in table 3.
The metallographic structure of 1000MPa obtained in the embodiment 1 grades of high-strength dual phase sheet steel of thin gauge hot rolling as shown in Figure 1, its Middle ferrite volume fraction is 30~40%, and Martensite Volume Fraction is 60~70%.
Each implementation of table 1 and comparative example chemical component and weight percent/%
The main rolling technological parameter of 2 embodiment of table
The mechanical property of 3 embodiment of table
What above-mentioned reference embodiment carried out high-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof Detailed description, is illustrative without being restrictive, can enumerate several embodiments according to limited range, therefore not The change and modification being detached under present general inventive concept, should belong within protection scope of the present invention.

Claims (10)

1. a kind of high-strength dual phase sheet steel of 1000MPa grades of thin gauge hot rolling, which is characterized in that including following chemical component and weight hundred Divide ratio: C:0.10~0.20%；Si:0.80~1.20%；Mn:1.20~2.0%；P :≤0.020%；S :≤0.010%； Ti:0.010~0.040%；Cr:0.20~0.60%；Als:0.020~0.060%；Remaining folder for Fe and inevitably It is miscellaneous.
2. the high-strength dual phase sheet steel of 1000MPa grades of thin gauge hot rolling according to claim 1, which is characterized in that including as follows Chemical component and weight percent: C:0.13~0.16%；Si:1.05~1.20%；Mn:1.75~1.86%；P :≤ 0.012%；S :≤0.008%；Ti:0.020~0.028%；Als:0.032~0.046%；Remaining is for Fe and inevitably It is mingled with.
3. the high-strength dual phase sheet steel of 1000MPa grades of thin gauge hot rolling according to claim 1, which is characterized in that described Its microscopic structure of the 1000MPa grades of high-strength dual phase sheet steels of thin gauge hot rolling is ferrite+martensite, wherein ferritic volume point Number is 30~40%, and Martensite Volume Fraction is 60~70%；Its yield strength >=550MPa, tensile strength >=1000MPa are bent Strong ratio≤0.60, elongation percentage A50>=16%, 180 ° of cold-bending property D=2a.
4. the preparation method of the high-strength dual phase sheet steel of 1000MPa grade thin gauge hot rolling according to claim 1 to 3, It is characterized in that, the preparation method comprises the following steps:
(1) it smelts, the refining of LF furnace, continuous casting；
(2) slab enters in heating furnace and is heated；
(3) it rolls, using two-stage control rolling mill practice；
(4) cooling: to use three stage control cooling technique；
(5) it batches, is air-cooled to room temperature after batching.
5. the preparation method according to claim 4, which is characterized in that in step (2), the heating temperature be 1150~ 1200 DEG C, soaking time 1.5-2h.
6. the preparation method according to claim 4, which is characterized in that in step (3), roughing accumulate reduction ratio be >= 70%, it is >=80% that reduction ratio is accumulated in finish rolling.
7. the preparation method according to claim 4, which is characterized in that in step (3), roughing start rolling temperature be 1100~ 1150 DEG C, finish rolling finishing temperature is 810~860 DEG C.
8. the preparation method according to claim 4, which is characterized in that in step (4), roll rear steel plate with 30~50 DEG C/s's Cooling velocity is cooled to that 680~720 DEG C of progress are air-cooled, and air-cooled 6~10s is cooled to 640-680 DEG C, then by steel plate with >=50 DEG C/s Cooling velocity be cooled to≤350 DEG C and batched.
9. the preparation method according to claim 4, which is characterized in that in step (2), the heating temperature be 1160~ 1200 DEG C, soaking time 1.7-2.0h；In step (3), it is 75~80% that reduction ratio is accumulated in roughing, and finish rolling accumulation reduction ratio is 81~85%, roughing start rolling temperature is 1118~1147 DEG C, and finish rolling finishing temperature is 815~850 DEG C.
10. the preparation method according to claim 4, which is characterized in that in step (4), roll rear steel plate with 35~50 DEG C/s Cooling velocity to be cooled to 683~713 DEG C of progress air-cooled, air-cooled 7.4~9.4s to 645-671 DEG C, then by steel plate with 65~78 DEG C/cooling velocity of s is cooled to≤346 DEG C and batched.
CN201910697090.7A 2019-07-30 2019-07-30 High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof Pending CN110331326A (en)

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Cited By (8)

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CN110629003A (en) * 2019-10-22 2019-12-31 马鞍山钢铁股份有限公司 Heat treatment-free hot continuous rolling ultrahigh-strength steel plate and manufacturing method thereof
CN110643800A (en) * 2019-10-22 2020-01-03 马鞍山钢铁股份有限公司 1200 MPa-level hot-rolled high-strength dual-phase steel plate and manufacturing method thereof
CN110724876A (en) * 2019-10-22 2020-01-24 马鞍山钢铁股份有限公司 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof
CN111266406A (en) * 2020-03-02 2020-06-12 攀钢集团攀枝花钢铁研究院有限公司 Rolling method of ultrathin hot continuous rolling steel strip
CN111793777A (en) * 2020-08-20 2020-10-20 山东华星新材料科技有限公司 1000 MPa-level hot-rolled high-strength corrosion-resistant dual-phase steel plate and preparation method thereof
CN112708824A (en) * 2020-12-07 2021-04-27 邯郸钢铁集团有限责任公司 Production method of hot-rolled thin-specification Gepa-grade high-strength steel
CN113215490A (en) * 2021-05-07 2021-08-06 马鞍山钢铁股份有限公司 Thin HB 300-grade wear-resistant steel plate and manufacturing method thereof
CN113528944A (en) * 2021-06-17 2021-10-22 首钢集团有限公司 1000MPa easily-formed wear-resistant steel plate and preparation method thereof

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CN103031493A (en) * 2011-09-29 2013-04-10 鞍钢股份有限公司 650 MPa-grade low-Si Cr-containing hot-rolled dual-phase steel plate and manufacturing method thereof
CN108396225A (en) * 2018-04-17 2018-08-14 马钢(集团)控股有限公司 A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method

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CN103031493A (en) * 2011-09-29 2013-04-10 鞍钢股份有限公司 650 MPa-grade low-Si Cr-containing hot-rolled dual-phase steel plate and manufacturing method thereof
CN108396225A (en) * 2018-04-17 2018-08-14 马钢(集团)控股有限公司 A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110629003A (en) * 2019-10-22 2019-12-31 马鞍山钢铁股份有限公司 Heat treatment-free hot continuous rolling ultrahigh-strength steel plate and manufacturing method thereof
CN110643800A (en) * 2019-10-22 2020-01-03 马鞍山钢铁股份有限公司 1200 MPa-level hot-rolled high-strength dual-phase steel plate and manufacturing method thereof
CN110724876A (en) * 2019-10-22 2020-01-24 马鞍山钢铁股份有限公司 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof
CN111266406A (en) * 2020-03-02 2020-06-12 攀钢集团攀枝花钢铁研究院有限公司 Rolling method of ultrathin hot continuous rolling steel strip
CN111266406B (en) * 2020-03-02 2022-01-28 攀钢集团攀枝花钢铁研究院有限公司 Rolling method of ultrathin hot continuous rolling steel strip
CN111793777A (en) * 2020-08-20 2020-10-20 山东华星新材料科技有限公司 1000 MPa-level hot-rolled high-strength corrosion-resistant dual-phase steel plate and preparation method thereof
CN112708824A (en) * 2020-12-07 2021-04-27 邯郸钢铁集团有限责任公司 Production method of hot-rolled thin-specification Gepa-grade high-strength steel
CN113215490A (en) * 2021-05-07 2021-08-06 马鞍山钢铁股份有限公司 Thin HB 300-grade wear-resistant steel plate and manufacturing method thereof
CN113528944A (en) * 2021-06-17 2021-10-22 首钢集团有限公司 1000MPa easily-formed wear-resistant steel plate and preparation method thereof

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