CN102719732A - Hot-rolled high-strength dual phase steel plate and manufacturing method thereof - Google Patents
Hot-rolled high-strength dual phase steel plate and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides a hot-rolled high-strength dual phase steel plate and a manufacturing method thereof. The steel plate comprises the following chemical components in percentage by weight: 0.10 to 0.13 percent of C, 0.85 to 1.15 percent of Si, 1.40 to 1.70 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.005 percent of S, 0.015 to 0.035 percent of Al, less than or equal to 0.006 percent of N and the balance of Fe and inevitable impurities. The steel plate has a ferrite and martensite dual phase structure. The manufacturing method for the steel plate comprises the following steps of: performing converter blowing; performing vacuum degassing; performing continuous casting or die casting, and rolling into a steel billet; heating; rolling, and performing sectional cooling; and reeling, and cooling. The steel plate which has the thickness of 2 to 6mm and is manufactured by the method has low yield ratio and high work hardening rate, is suitable for manufacturing members such as a structure, a reinforcer and a wheel disc, and meets the high requirements of automobile industry, engineering machinery industry and the like on advanced high-strength steel plates.
Description
Technical field
The present invention relates to a kind of high tensile steel plate and method of manufacture thereof, particularly a kind of hot rolling biphase plate and method of manufacture thereof.
Background technology
Orthodox car mainly comprises the part low strength rank kind of gapless atomic steel (IF), HS gapless atomic steel (IF-HS), general carbon soft steel (MILD), isotropy steel (IS), baking hardened steel (BH), carbon manganese steel (C-Mn) and HSLA (HSLA), dual phase steel (DP), phase change induction plasticity steel three kinds such as (TRIP) with low strength steel (LSS) and plow-steel (HSS).Traditional high-strength steel mostly through solid solution, separate out with means such as crystal grain thinning as its mode of mainly strengthening.Along with the development of automobile industry and increasingly sharpening of energy dilemma and environmental problem; Increasingly high to automobile energy-saving and safe requirement; In order to satisfy the light weight requirement more and more gentlier to improve the demand of fuel economy, AHSS (AHSS) or ultrahigh-strength steel (Ultra-HSS) arise at the historic moment.Usually tensile strength is decided to be AHSS (AHSS) or ultrahigh-strength steel greater than the steel grade of 600MPa, mainly contains following five big types: HSLA, dual phase steel, phase change induction plasticity steel, complex phase steel (CP), martensitic steel (MP).Advanced high-strength steel is mainly strengthened through phase transformation, contains martensite, bainite and/or residual austenite in the tissue.Advanced high-strength steel has HS concurrently and plasticity, particularly work hardening exponent are high preferably, helps improving the energy absorption in the impact process, assurance security when reaching loss of weight.
Wherein, hot-rolled dual-phase steel (Dual Phase steel is called for short DP) because of having the cooperation of HS and good stampability, is one of important composition in the advanced high-strength steel.The martensite that is organized as distribution small and dispersed on the ferrite matrix of hot-rolled dual-phase steel or bainite (generally 15%) have unit elongation and higher work hardening rate preferably.Because ferritic structure has lower ys; And martensitic stucture has advantages of higher tensile strength; So the duplex structure that this steel grade is had makes it possess lower yield tensile ratio and higher unit elongation; Have better fatigue resistance and endergonic characteristics, be fit to members such as manufacturing structure spare, stiffener, wheel wheel disc.
Granted publication number is the Chinese invention patent of CN100441724C, discloses a kind of technology of hot-rolled dual-phase steel, and wherein the weight percent composition (%) of chemical element is designed in the molten steel: C:0～0.075%; Si:0.6～1.0%; Mn: 1.5～2.0%; Cr:0.4～0.6%; Als:0.010～0.080%; V:0.02～0.14%; All the other are Fe and impurity element.Take to prick back sectional process for cooling, finishing temperature is 800～900 ℃, and coiling temperature is 400～500 ℃.
Application publication number is the Chinese invention patent of CN101880825A, discloses a kind of production technique of hot-rolled dual-phase steel equally and according to plate product that this mode of production obtains, this dual phase steel chemical constitution is controlled to be by mass percent (%): C:0.06～0.16%; Si:0.10～0.50%, Mn:1.00～2.00%, Al:0.02～0.06%; Nb:0.01～0.08%, Ti:0～0.03%, and restriction P≤0.1; S≤0.005, surplus are Fe and other element impurity.Take continuous process for cooling, finishing temperature is 770-860 ℃, < 350 ℃ of coiling temperatures.
All add a certain amount of microalloy element Nb, V, Ti and valuable alloying elements cr, Ni, Mo in the technical process of above-mentioned two patents of invention and obtained the higher dual phase steel product of tensile strength; Increased production cost on the one hand; Also can impact on the other hand use propertieies such as the extensibility of steel plate and weldablenesies; And the tensile strength through above-mentioned two kinds of steel plates that method obtains all is not more than 800MPa, is difficult to satisfy the growing HS in automobile industry and mechanical industry field and the requirement of excellent plasticity.
Summary of the invention
The object of the present invention is to provide a kind of tensile strength in 800MPa level other hot-rolled high-strength dual phase sheet steel and method of manufacture thereof, just can satisfy the low yield strength ratio of members such as manufacturing structure spare, stiffener, wheel wheel disc in automobile industry and the mechanical industry field and the requirement of high work hardening rate with lower cost.
To achieve these goals; The present invention is satisfying the plate property parameter request and is not adding under the situation of expensive alloy element; The optimization of appropriate design through chemical ingredients and the control of the parameter of technical process changes steel grade types of organization and ratio, to obtain the dual phase sheet steel of HS and high-quality plasticity.
The chemical composition design of hot-rolled high-strength dual phase sheet steel provided by the invention (percentage composition meter by weight) is: C:0.10～0.13%; Si:0.85～1.15%, Mn:1.40～1.70%, P :≤0.015%; S :≤0.005%; Al:0.015～0.035%, N :≤0.006%, surplus is iron and inevitable impurity.
The reason of chemical element Composition Control in respective range is:
1) carbon: carbon is the key element of guaranteeing steel plate tissue and intensity.For the steel plate that needs obtain ferritic and martensite duplex structure, carbon content can not be too high, otherwise ferritic formation needs very long incubation period and incubation time, the quick cooling after being unfavorable for rolling.For the segmentation cooling, the middle air cooling time need very longly just can be separated out ferritic, and existing hot rolling line can not satisfy the requirement of overlength layer cold-peace segmentation cooling mode.Should suitably reduce carbon content, but can not be too low, otherwise can not satisfy high-tensile requirement, so carbon content narrow range of the present invention, best carbon content is 0.10～0.13%.
2) silicon: silicon is a very important cheap alloying element for dual phase steel, and it can promote ferritic formation.Therefore the present invention adopts higher silicone content both to impel the ferrite transformation initial to move to left, and can improve intensity again.But silicone content should not be too high, and the oxide debris viscosity when too high silicone content can make the steel plate heating is bigger, the back de-scaling difficulty of coming out of the stove, and the red oxide debris of surface of steel plate is serious after causing rolling, and surface quality is relatively poor, and the high welding property that influences steel plate of silicone content.Take all factors into consideration the influence of silicon each side, silicone content of the present invention is 0.85～1.15%.
3) manganese: manganese is cheap stable austenite tissue and reinforced alloys element, and its ability is only second to alloying element nickel.Simultaneously, manganese can also increase the hardening capacity of steel, reduces the critical cooling velocity that bainite and martensite form, and can effectively reduce the speed of cooling of rolling first section water-cooled in the segmentation cooling of back, is beneficial to and obtains bainite or martensitic stucture.But manganese has higher segregation tendency, and its content can not be too high, and manganese content is no more than 2.0% in the general low-carbon micro steel-alloy.The add-on of manganese depends primarily on the intensity rank of steel.The content of manganese of the present invention should be controlled at 1.4～1.7%.Manganese in steel also and aluminium play the effect of deoxidation together jointly.
4) sulphur and phosphorus: sulphur closes formation plastic occluded foreignsubstance manganese sulfide with manganese in steel, especially all unfavorable to the horizontal plastic property and the toughness of steel, so the content of sulphur should be controlled at lowest range as much as possible.Phosphorus also is the harmful element in the steel, the plasticity of heavy damage steel plate and toughness.For the present invention, sulphur and phosphorus all are unavoidable impurities elements, should be low more good more.Consider the steel-making level that steel mill is actual, the present invention requires P: S≤0.015% :≤0.005%.
5) aluminium: aluminium is strong deoxidant element.Low as best one can in order to guarantee the oxygen level in the steel, the content of aluminium should be controlled at 0.015～0.035% as far as possible.Unnecessary aluminium and the nitrogen element in the steel can form the AlN precipitate after the deoxidation, improve intensity and the element autstenitic grain size of ability refinement steel when thermal treatment heat.
Further, the present invention also provides the method for manufacture of above-mentioned steel plate, and the concrete technical process of optimizing is following:
1. bessemerize and vacuum-treat: purpose is to guarantee the basal component requirement of molten steel, obnoxious flavoures such as the oxygen in the removal steel, hydrogen, and add necessary alloying element such as manganese, titanium; Carry out the adjustment of alloying element, and carry out Composition Control (in weight percentage) for contained chemical element and be: C:0.10～0.13%, Si:0.85～1.15%; Mn:1.40～1.70%; P :≤0.015%, S :≤0.005%, Al:0.015～0.035%; N :≤0.006%, surplus is iron and inevitable impurity.
2. continuous casting or die casting: guarantee that all even surface quality of strand internal component is good, the steel ingot of die casting need be rolled into steel billet.
3. heating is with rolling: because the present invention do not add microalloy element, so than general micro-alloyed steel, can reduce the effect that Heating temperature not only can play the refinement original austenite grains and also can save the production energy.Continuously cast bloom or steel billet are heated under 1100～1150 ℃ temperature.In austenite recrystallization and non-recrystallization TR, be rolled into steel plate through multi-pass; Because do not add microalloy element; Event needs bigger compression ratio (rolling refined austenite crystal in recrystallization zone and non-recrystallization district are rolling with refinement follow-up ferritic and martensite crystal grain); Total draft >=80%; 820～860 ℃ of finishing temperatures, lower finishing temperature help continuously cast bloom or steel billet and after rolling, promptly get into the ferritic phase region to separate out part ferritic (certainly also need with roll back first section quick water-cooled and match).
4. carry out the segmentation cooling after rolling: 70～100 ℃/s of first section water-cooled speed; The water-cooled purpose is to make material get into the ferritic phase region rapidly fast, and middle air cooling temperature is controlled at 620～660 ℃, air cooling time 4～6s; The cooperation of air cooling temperature and time is in order to obtain an amount of ferritic structure (about volume(tric)fraction 80%) and lower ys; Second section water-cooled rate request be greater than 100 ℃/s, final cooling temperature≤200 ℃, preferred 150～200 ℃ of the final cooling temperature of second section water-cooled; Its purpose is to make the austenite structure of not phase transformation to be quenched to martensitic stucture, improves the tensile strength of steel.Owing to produce the key of hot-rolled dual-phase steel is the type of cooling after the control hot rolling, so present method can obtain the required performance of dual phase sheet steel through control phase-change organization's type and ratio.
5. the coiler plate after cold eventually is cooled to room temperature and gets final product.
Compared with prior art; On the chemical ingredients aspect; Owing to contain suitable carbon in the steel plate; And its content range is narrower, has guaranteed that so promptly certain carbon content has increased tensile strength to steel plate, has reduced the too high meeting of carbon content again and has caused ferritic formation to need the overlong time of incubation period; An amount of element silicon can not only can promote the ferrite transformation initial to move to left, and can also improve armor plate strength; Suitably add manganese element except that the intensity that can increase steel plate, can also promote the through hardening performance of steel, reduce the critical cooling velocity that bainite and martensite form.The present invention adopts cheap alloying element C, Si, Mn not only to reach and adopts the expensive required purpose that reaches steel plate refined crystalline strengthening, phase transformation reinforcement and strength enhancing of alloying elements cr, Ni, Mo before; Intensity, hardness and the forming property of steel plate have also been improved; Alleviated the weight of steel plate; Having obtained the tensile strength rank is the steel plate of 800Mpa, has satisfied the requirement of industry fields such as automobile, engineering machinery to this type of steel plate.
On the ME aspect; The present invention controls for heating, processing parameter rolling and that roll steps such as back segmentation (dividing two sections) cooling; Especially made full use of the stronger water-cooled ability and the advantage that possesses multiple water-cooled pattern of hot rolling unit; After rolling, take the segmentation process for cooling, make cooled steel plate tissue be rendered as ferritic+martensitic duplex structure.Such duplex structure has given the characteristics that the steel plate yield tensile ratio is low, plasticity good and work hardening rate is high.
Steel plate through this method manufacturing: ys >=450MPa; Tensile strength >=800MPa; Unit elongation A50 >=15%; Have higher intensity, plastotype property and plasticity, use propertieies such as extensibility, weldableness, clod wash property have satisfied members such as structural part, stiffener, wheel wheel disc and have made higher requirement preferably.Simultaneously, this method of manufacture can alleviate the steelwork deadweight, has reduced manufacturing cost, has effectively utilized resource, has reduced the discharging of contamination level.
Description of drawings
Fig. 1 rolls back segmentation cooling synoptic diagram.
Fig. 2 utilizes light microscope determining 2mm Plate Steel to have the photo of ferritic+martensitic metallographic structure.
Fig. 3 utilizes light microscope determining 4mm Plate Steel to have the photo of ferritic+martensitic metallographic structure.
Fig. 4 utilizes light microscope determining 6mm Plate Steel to have the photo of ferritic+martensitic metallographic structure.
Embodiment
Through following five embodiment the present invention is further described, embodiment operates according to technical process.The steel plate chemical composition design of five embodiment is seen table 3, and process parameter table is seen table 4, and the mechanical property and the organizational composition that are obtained steel plate by embodiment are seen table 5.
Present embodiment 1-5 carries out according to following technical process: 1) bessemerize and vacuum-treat; 2) continuous casting or die casting; 3) heating and rolling, Heating temperature is 1100～1150 ℃, multi-pass is rolling, total draft>=80%, 820～860 ℃ of finishing temperatures; 4) segmentation cooling: 70-100 ℃/s of first section water-cooled speed, middle air cooling temperature is controlled at 620～660 ℃, air cooling time 4～6s; Second section water-cooled rate request be greater than 100 ℃/s, final cooling temperature≤200 ℃, and it is as shown in Figure 1 specifically to roll the postcooling pattern; Slow cooling temperature in the middle of being cooled to rapidly after the finish rolling finish to gauge; This temperature range slow cooling for some time to generate the ferritic of enough content, be cooled fast to martensite transformation temperature then, making not the austenitic transformation that changes is martensite; 5) batch and be cooled to room temperature.
The metallographic structure of part steel plate such as Fig. 2 are shown in 3,4.Visible from figure, the tissue of steel plate of the present invention is ferritic+martensite.
Table 3 be embodiment of the invention 1-5 chemical composition design (percentage composition by weight, %)
| Embodiment | C | Si | Mn | P | S | Al | N | Ceq* |
| 1 | 0.10 | 1.05 | 1.55 | 0.008 | 0.002 | 0.033 | 0.0042 | 0.36 |
| 2 | 0.11 | 1.15 | 1.60 | 0.010 | 0.003 | 0.015 | 0.0045 | 0.38 |
| 3 | 0.125 | 0.95 | 1.40 | 0.007 | 0.003 | 0.025 | 0.0041 | 0.36 |
| 4 | 0.125 | 1.01 | 1.68 | 0.007 | 0.002 | 0.035 | 0.0039 | 0.41 |
| 5 | 0.13 | 0.85 | 1.70 | 0.008 | 0.002 | 0.020 | 0.0040 | 0.41 |
*Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/14
Can know that by table 3 carbon equivalent of five embodiment is all lower, show that steel plate of the present invention has good welding property.
Table 4 is the heating of embodiment of the invention 1-5, rolling, segmentation cooling related process parameter
Table 5 by through embodiment of the invention 1-5 the mechanical property and the organizational composition of acquisition steel plate
Remarks: table 5 is for obtaining the parameters such as ys, tensile strength, unit elongation and yield tensile ratio of steel plate by GB/T228-2002 metallic substance tensile test at room temperature method.
Can know the thick finished product steel plate of the 2～6mm that adopts above-mentioned chemical composition design and processing parameter to process acquisition, its ys>=450Pa from above embodiment; Tensile strength>=800MPa, yield tensile ratio≤0.65, unit elongation A50>=15%; Has low yield strength ratio, high work hardening rate, higher intensity, plastotype and forming property; Use properties such as extensibility, weldableness preferably; Good cold-bending property is particularly suitable for members such as manufacturing structure spare, stiffener, wheel wheel disc, under the situation that production cost reduces; Satisfied the high requirement of industries such as automobile, engineering machinery, had market application foreground and fine economic benefit value widely the AHSS plate.
Claims (5)
1. hot-rolled high-strength dual phase sheet steel, its chemical element composition weight percentage is C:0.10～0.13%; Si:0.85～1.15%, Mn:1.40～1.70%, P :≤0.015%; S :≤0.005%; Al:0.015～0.035%, N :≤0.006%, surplus is iron and inevitable impurity.
2. hot-rolled high-strength dual phase sheet steel as claimed in claim 1 is characterized in that said steel plate is organized as ferritic and martensite.
3. the method for manufacture of a hot-rolled high-strength dual phase sheet steel as claimed in claim 1, its step is following,
1) bessemerizes;
2) vacuum outgas;
3) continuous casting or die casting;
4) heating adds hot continuously cast material or steel billet under 1100～1150 ℃ temperature;
5) rolling, the rolling total draft of multi-pass >=80%, finishing temperature is 820～860 ℃;
6) segmentation cooling, 70～100 ℃/s of first section water-cooled speed, middle air cooling temperature is controlled at 620～660 ℃, air cooling time 4～6s, second section water-cooled rate request>100 ℃/s, final cooling temperature≤200 ℃;
7) batch and be cooled to room temperature.
4. the method for manufacture of hot-rolled high-strength dual phase sheet steel as claimed in claim 3 is characterized in that, and is rolling in austenite recrystallization and non-recrystallization TR in the said step 5).
5. the method for manufacture of hot-rolled high-strength dual phase sheet steel as claimed in claim 3 is characterized in that, second section water-cooled final cooling temperature of said segmentation cooling is 150～200 ℃.
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| CN105838997A (en) * | 2016-05-17 | 2016-08-10 | 武汉钢铁股份有限公司 | Si-Mn 780 MPa-grade hot-rolled dual-phase steel and production method thereof |
| CN105925892A (en) * | 2016-06-21 | 2016-09-07 | 宝山钢铁股份有限公司 | 780 MPa-grade hot-rolled high-reaming dual-phase steel and manufacturing method thereof |
| CN106119703A (en) * | 2016-06-21 | 2016-11-16 | 宝山钢铁股份有限公司 | A kind of 980MPa level hot-rolled dual-phase steel and manufacture method thereof |
| CN106216412A (en) * | 2016-07-29 | 2016-12-14 | 安阳钢铁股份有限公司 | A kind of method utilizing stove volume unit laminar flow sub-sectional cooling to control cut deal phase transformation |
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| CN109694985A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | The 800MPa grade hot rolling biphase plate and its manufacturing method of function admirable |
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| CN108698437A (en) * | 2016-02-10 | 2018-10-23 | 蒂森克虏伯钢铁欧洲股份公司 | Commercial vehicle wheel and application |
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| CN105925892A (en) * | 2016-06-21 | 2016-09-07 | 宝山钢铁股份有限公司 | 780 MPa-grade hot-rolled high-reaming dual-phase steel and manufacturing method thereof |
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| CN109694985A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | The 800MPa grade hot rolling biphase plate and its manufacturing method of function admirable |
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| CN112680660A (en) * | 2020-12-03 | 2021-04-20 | 山东钢铁集团日照有限公司 | 1.2 GPa-grade TRIP steel and regulation and control method of microstructure thereof |
| CN112680660B (en) * | 2020-12-03 | 2022-04-15 | 山东钢铁集团日照有限公司 | 1.2 GPa-grade TRIP steel and regulation and control method of microstructure thereof |
| CN116497274A (en) * | 2023-04-19 | 2023-07-28 | 邯郸钢铁集团有限责任公司 | Low-cost and easy-rolling 600 MPa-grade hot-rolled dual-phase steel and preparation method thereof |
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Application publication date: 20121010 |