CN110257725A - A kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling and preparation method thereof - Google Patents

A kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling and preparation method thereof Download PDF

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Publication number
CN110257725A
CN110257725A CN201910695913.2A CN201910695913A CN110257725A CN 110257725 A CN110257725 A CN 110257725A CN 201910695913 A CN201910695913 A CN 201910695913A CN 110257725 A CN110257725 A CN 110257725A
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cooled
preparation
strength
hot rolling
980mpa
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Inventor
彭欢
胡学文
王海波
司小明
刘启龙
王泉
王承剑
吴志文
饶添荣
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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 CN201910695913.2A priority Critical patent/CN110257725A/en
Publication of CN110257725A publication Critical patent/CN110257725A/en
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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
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for cooling
    • 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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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 present invention discloses can a kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling and preparation method thereof.The high-strength dual phase sheet steel of 980MPa grades of 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%；Als:0.10~0.50%；Remaining is Fe and is inevitably mingled with.Pass through the design of reasonable ingredient, smelting, continuous casting, heating, hot rolling, cooling and the optimization of coiling technique, while hot-rolled dual-phase steel can be made to obtain higher-strength, with good forming property, its microscopic structure is ferrite+martensite, wherein ferritic volume fraction is 30~40%, Martensite Volume Fraction is 60~70%, yield strength >=600MPa of product, tensile strength >=980MPa, yield tensile ratio≤0.65, elongation percentage A50>=15%, 180 ° of cold-bending property, D=2a is qualified.

Description

A kind of high-strength dual phase sheet steel of 980MPa grades of 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 high-strength two-phase of 980MPa grades of hot rolling Steel plate 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, safety are As the main trend of its development, this requirement also to wheel 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, state The hot-rolled dual-phase steel of inside and outside production and application mainly based on DP540~DP600, the dual phase steel of DP780 and the above rank still with Based on cold rolling.
Summary of the invention
The purpose of the present invention is to provide a kind of high-strength dual phase sheet steels of 980MPa grades of hot rolling and preparation method thereof.By reasonable Ingredient design, smelting, continuous casting, heating, hot rolling, cooling and the optimization of coiling technique, can make hot-rolled dual-phase steel obtain it is higher While intensity, there is good forming property.This hot-rolled dual-phase steel is mainly used for the system that part is thinned in the structures such as automotive wheel It makes.
Technical solution provided by the invention are as follows:
A kind of high-strength dual phase sheet steel of 980MPa grades of 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%；Als:0.10~0.50%；Remaining is Fe and is inevitably mingled with.
Further, it is preferable to which being includes 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%；Als:0.10~ 0.50%；Remaining is Fe and is inevitably mingled with.
Its microscopic structure of the high-strength dual phase sheet steel of 980MPa grades of hot rolling is ferrite+martensite, wherein ferritic Volume fraction is 30~40%, and Martensite Volume Fraction is 60~70%；Its yield strength >=600MPa, tensile strength >= 980MPa, yield tensile ratio≤0.65, elongation percentage A50>=15%, 180 ° of cold-bending property D=2a.
The present invention also provides the preparation method of the high-strength dual phase sheet steel of 980MPa grades of hot rolling, the preparation method includes 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.
Further, 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 800~840 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 8~12s is cooled to 640-680 DEG C, then steel plate is cooled to≤300 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 1.7-2h；Step (3) in, roughing accumulate reduction ratio be 71~79%, finish rolling accumulate reduction ratio be 82~85%, roughing start rolling temperature be 1120~ 1146 DEG C, finish rolling finishing temperature is 809~834 DEG C.
In step (4), rolling rear steel plate, with the cooling velocity of 38~49 DEG C/s to be cooled to 687~706 DEG C of progress air-cooled, air-cooled 8.5~11s is cooled to 646-672 DEG C, then steel plate is cooled to≤260 DEG C with the cooling velocity of 65~78 DEG C/s and is batched.
Chemical component of the present invention uses C-Si-Mn-Al 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 is 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 performances such as forming, welding to steel have an adverse effect, it should strict control contains The lower measure the better, considers production cost factor, controls P in actual production :≤0.020%, S :≤0.010%.
Als:0.10~0.60%, Als are mainly used for improving ferrite transformation start temperature, promote certain proportion ferrite The formation of tissue, but Als cannot be excessively high, and Als is excessively high to have an adverse effect to the castability of molten steel in continuous casting process；Ti: 0.010~0.040%.
Ti:0.010~0.040%, the effect in steel mainly plays two, first is that fining austenite grains, and it is right The ferrite and martensite finally changed plays refining effect；Second is that forming TiN in conjunction with N element, nitrogen fixation is played.
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 800~840 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 8-12s, 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 300 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 is 6-10 μm, wherein ferritic volume fraction is 30~40%, Martensite Volume Fraction 60 ~70%, yield strength >=600MPa of product, tensile strength >=980MPa, yield tensile ratio≤0.65, elongation percentage A50>=15%, 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 980MPa grade 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%；Als:0.10~ 0.60%；Remaining is Fe and is inevitably mingled with, and carries out converter smelting, the refining of LF furnace, continuous casting, heating, rolling, cooling, volume It takes.
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 980MPa obtained in the embodiment 1 grades of high-strength dual phase sheet steel of hot rolling is as shown in Figure 1, white is geneva Body tissue, grey are ferritic structure, wherein ferrite volume fraction be 30~40%, Martensite Volume Fraction be 60~ 70%.
Each implementation of table 1 and comparative example chemical component and weight percent/%
Number C Si Mn P S Ti Als
Embodiment 1 0.16 1.17 1.75 0.014 0.008 0.028 0.35
Embodiment 2 0.13 1.10 1.70 0.012 0.006 0.026 0.40
Embodiment 3 0.14 1.05 1.86 0.010 0.007 0.024 0.50
Comparative example 1 0.16 1.17 1.75 0.014 0.008 0.028 0.35
Comparative example 2 0.08 0.95 2.13 0.016 0.012 0.005 0.22
Comparative example 3 0.22 1.42 1.05 0.012 0.009 0.042 0.38
Table 2 respectively implements and comparative example preparation technology parameter
The mechanical property of table 3 embodiment and comparative example
It is above-mentioned to be retouched in detail referring to embodiment to what a kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling and preparation method thereof carried out It states, is illustrative without being restrictive, several embodiments can be enumerated according to limited range, therefore do not departing from this Change and modification under invention general plotting should belong within protection scope of the present invention.

Claims (10)

1. a kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling, which is characterized in that 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%；Als:0.10~0.50%；Remaining is Fe and is inevitably mingled with.
2. the high-strength dual phase sheet steel of 980MPa grades of hot rolling according to claim 1, which is characterized in that 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%；Als:0.10~0.50%；Remaining is Fe and is inevitably mingled with.
3. the high-strength dual phase sheet steel of 980MPa grades of hot rolling according to claim 1 or 2, which is characterized in that 980MPa grades described Its microscopic structure of the high-strength dual phase sheet steel of hot rolling is ferrite+martensite, wherein ferritic volume fraction is 30~40%, horse Family name's body volume fraction is 60~70%；Its yield strength >=600MPa, tensile strength >=980MPa, yield tensile ratio≤0.65 extend Rate A50>=15%, 180 ° of cold-bending property D=2a.
4. the preparation method of the high-strength dual phase sheet steel of 980MPa grade hot rolling according to claim 1 to 3, feature It is, 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 800~840 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 8~12s is cooled to 640-680 DEG C, then by steel plate with >=50 DEG C/s Cooling velocity be cooled to≤300 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 1.7-2h；In step (3), it is 71~79% that reduction ratio is accumulated in roughing, and it is 82 that reduction ratio is accumulated in finish rolling ~85%, roughing start rolling temperature is 1120~1146 DEG C, and finish rolling finishing temperature is 809~834 DEG C.
10. the preparation method according to claim 4, which is characterized in that in step (4), roll rear steel plate with 38~49 DEG C/s Cooling velocity to be cooled to 687~706 DEG C of progress air-cooled, air-cooled 8.5~11s is cooled to 646-672 DEG C, then by steel plate with 65~ The cooling velocity of 78 DEG C/s is cooled to≤260 DEG C and is batched.
CN201910695913.2A 2019-07-30 2019-07-30 A kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling and preparation method thereof Pending CN110257725A (en)

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Cited By (2)

* 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
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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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101880825A (en) * 2010-07-08 2010-11-10 东北大学 Ultrafine grained hot rolled dual-phase steel with tensile strength of above 750MPa and manufacturing method of plate thereof
CN107723604A (en) * 2017-11-29 2018-02-23 攀钢集团攀枝花钢铁研究院有限公司 A kind of economical 690MPa levels dual phase steel and preparation method thereof
CN108018493A (en) * 2016-10-31 2018-05-11 宝山钢铁股份有限公司 A kind of 1180MPa grades of hot-rolled dual-phase steel and its manufacture method
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

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101880825A (en) * 2010-07-08 2010-11-10 东北大学 Ultrafine grained hot rolled dual-phase steel with tensile strength of above 750MPa and manufacturing method of plate thereof
CN108018493A (en) * 2016-10-31 2018-05-11 宝山钢铁股份有限公司 A kind of 1180MPa grades of hot-rolled dual-phase steel and its manufacture method
CN107723604A (en) * 2017-11-29 2018-02-23 攀钢集团攀枝花钢铁研究院有限公司 A kind of economical 690MPa levels dual phase steel and preparation 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 (2)

* 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
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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