CN108315662B - A kind of yield strength 900MPa level hot rolled steel plate and its production technology - Google Patents

A kind of yield strength 900MPa level hot rolled steel plate and its production technology Download PDF

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CN108315662B
CN108315662B CN201810294415.2A CN201810294415A CN108315662B CN 108315662 B CN108315662 B CN 108315662B CN 201810294415 A CN201810294415 A CN 201810294415A CN 108315662 B CN108315662 B CN 108315662B
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steel
steel plate
cooling
steel billet
billet
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CN108315662A (en
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梁亮
李光辉
刘旭辉
肖尊湖
罗钢
肖爱达
徐德强
谢世正
汪宏兵
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Lysteel Co Ltd
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/14Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226Hot rolling
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/12Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Abstract

The invention discloses a kind of yield strength 900MPa level hot rolled steel plate (volume) and its production technologies, control the mass percentage and CEV of C, Si, Mn, P, S, Cr, Mo, V, Ti, Nb and Al of steel.Pretreated blast furnace desulphurised hot metal enters converter smelting, it smelts qualified molten steel and is casting continuously to form steel billet after LF+RH+ Calcium treatment, steel billet rolls into steel plate after being heated to 1150~1300 DEG C in heating furnace, finishing temperature is 830~890 DEG C, steel plate of the steel billet after finish to gauge carries out ultra-rapid cooling with 100~300 DEG C/S of cooling velocity, and steel plate is cooled to 560~660 DEG C in the method for 10~25 DEG C/s section cooling.Cold steel plate is rolled into coil of strip with 560~660 DEG C eventually.Horizontal and vertical tensile strength >=the 900MPa of coil of strip (plate) obtained through production technology as above, transverse and longitudinal elongation >=15%, transverse and longitudinal Charpy-V impact power AKv (- 40 DEG C) >=27J.Steel plate is widely used in lightweight body of tipper carriage and structural member, has good welding performance and buckling performance.

Description

A kind of yield strength 900MPa level hot rolled steel plate and its production technology
Technical field
The present invention relates to a kind of hot-rolling high-strength steel plate and its production technologies, more particularly to one kind to be applied to commercial vehicle (such as Body of tipper carriage etc.) yield strength be 900MPa level hot rolled steel plate (volume) and its production technology.
Background technique
High-strength steel sheet is applied to the lightweight of engineering machinery and commercial vehicle, in particular with national standard GB1589-2016's Formal publication and implementation, propose higher loss of weight demand to material in terms of the lightweight of commercial vehicle.900MPa grades of yield strength Or more high-strength steel sheet be widely used to the structural member of commercial vehicle.Only to compartment plate gauge in national standard GB/T33963-2017 Surely the intensity of 700Mpa rank has been arrived, intensity is up the abrasion-resistant stee of quenched and tempered state.It is defined in national standard GB/T16270-2009 in the wrong Take the mechanical property and carbon equivalent standard of 890MPa grades of quenched and tempered state high-strength steel of intensity.Its yield strength >=890MPa, tensile strength 940 ~ 1100MPa and elongation percentage >=11%, meet -40 DEG C of impact of collision function > 34J, and the carbon equivalent ce V satisfaction of steel is less than or equal to 0.72% requirement.
The manufacturing technology of high-strength steel sheet is mainly controlled rolling and controlled cooling (TMCP) and quenched (Q+T).TMCP(Thermo- Mechanical Control Process) by two-phase control rolling temperature, drafts and the cooling technique of control steel plate, it is formed Specific microstructure, to obtain good mechanical performance.At present TMCP technique production high-strength steel be mainly 700Mpa and its with Under, the high-strength steel of 700Mpa or more is produced by hardening and tempering process, and hardening and tempering process is steel plate in heating austenite Enter rolling mill practice after homogenization, is rolled down to air-cooled after specified thickness.The air-cooled steel plate to after room temperature enters heating furnace, specified Quenching is cooled to room temperature after temperature austenitizing, and quenched steel plate enters back into tempering furnace and is reheated to assigned temperature, heat preservation It comes out of the stove after a certain period of time air-cooled.Hardening and tempering process production high-strength steel sheet is by the quenching process refinement after austenitizing, finally For martensitic structure, carbon is discharged from supersaturated ferrite using tempering process, is formed simultaneously tiny carbide, improves The internal stress and low-temperature impact toughness of steel plate.Although hardening and tempering process can obtain high intensity and excellent mechanical property, it is given birth to Long flow path is produced, energy consumption is big, complex process.
Due to the development of the industries such as heavy load truck, engineering machinery, the requirement of load-carrying and mechanical strength to vehicle is constantly mentioned Height, while also requiring to mitigate self weight, therefore it is required that, intensity rank lower using the cost better superelevation of high and low temperature impact flexibility Strength steel sheet.
Summary of the invention
The purpose of the present invention is to provide a kind of 900MPa grades of yield strength (Rel) and there are superior weldability energy, elongation percentage And hot rolled steel plate (volume) and its production technology compared with high-tensile (Rm).
To achieve the above object, the technical solution adopted by the present invention is that: a kind of yield strength 900MPa grades of hot rollings Steel plate (volume), its Design of Chemical Composition are C=0.08~0.15 (in terms of wt%), Si=0.10~0.40, Mn=1.30~2.0, P ≤ 0.015, S≤0.005, Mo=0.20~0.50, V=0.10~0.20, Ti=0.10~0.20, Nb=0.015~0.050, Al= 0.02~0.07, surplus is Fe and other inevitable impurity, carbon equivalent ce V≤0.55% of steel.
A kind of production technology of yield strength 900MPa level hot rolled steel plate (volume) includes following procedure: through desulfurization It is pretreated it is blast-melted pour into oxygen top bottom blowing converter and smelted, by qualified smelting molten steel through Argon, vacuum And steel billet is casting continuously to form by conticaster after Calcium treatment.The steel billet being casting continuously to form is sent into soaking pit or heating furnace and is heated, when steel billet plus Heat is to soaking time >=15min after 1150~1300 DEG C.
Steel billet after heating is rolled: roughing, 5~7 passage of roughing, the single track of roughing mill are carried out to the steel billet of heating Secondary reduction ratio >=15%, total reduction of the steel billet on roughing mill are 70~85%.Steel billet becomes intermediate base after roughing.After roughing Intermediate base enter finishing tandem rolling unit finish rolling, intermediate base entry temperature at finishing control is between 1000~1100 DEG C, finishing tandem rolling unit Single chassis reduction ratio >=10%, the total reduction of intermediate base is 75~97%.Finishing temperature control of the intermediate base in finishing tandem rolling unit For system at 820~900 DEG C, steel plate thickness of the intermediate base after finishing tandem rolling unit finish rolling is 1.2~10.0mm, the steel plate after finish rolling with 100~300 DEG C/S of cooling velocity carries out ultra-rapid cooling, and steel plate is cooled to 560 in the method for 10~25 DEG C/s section cooling ~660 DEG C.Steel plate coils into coil of strip under the conditions of 560~660 DEG C.
It is cold or be slowly cooled to room temperature that offline coil of strip is subjected to heap.
A kind of yield strength 900MPa level hot rolled steel plate (volume) and its production technology that are there is provided using technical solution as above and The prior art is compared, and has the technical effect that 1. a kind of yield strength 900MPa level hot rolled steel plate (volume) provided by the invention is not only Elongation percentage with higher and tensile strength also have excellent Bending Processing performance and welding performance;What 2. the present invention designed Integral Thought is to add the component system of V-Ti-Mo and the process system of controlled rolling and controlled cooling using low C, is matched by alloying element Between optimization, make full use of technique to act on the raising of steel plate obdurability, production has compared with low-carbon-equivalent (CEV≤0.55%) High strength steel plate;It obtains the disperse on ultra-fine grained ferrite matrix of the crystallite dimension less than 5 μm and issues the left side partial size about 5nm The microstructure of right microalloy precipitated phase so that steel plate yield strength can reach under the conditions of hot continuous rolling 900Mpa grades with On, transverse and longitudinal elongation >=15%, transverse and longitudinal Charpy-V impact power AKv (- 40 DEG C) >=27J rolls at rear quenched heat so as to cancel Reason.Advantage is to simplify Production Flow Chart, reduces energy consumption, reduces steel plate internal stress;3. in addition to good welding performance, Also there is the buckling performance more excellent than hardened and tempered steel plate, elongation percentage.
Specific embodiment
A specific embodiment of the invention is described in further detail below.
A kind of yield strength 900MPa level hot rolled steel plate (volume) of the present invention chemical component proportion (wt%) be C= 0.08~0.15, Si=0.10~0.40, Mn=1.30~2.0, P≤0.015, S≤0.005, Mo=0.20~0.50, V=0.10 ~0.20, Ti=0.10~0.20, Nb=0.015~0.050, Al=0.02~0.07, surplus be Fe and it is other inevitably it is miscellaneous Matter;Carbon equivalent (CEV)≤0.55%.Wherein the calculation formula of carbon equivalent ce V is CEV(%)=C+Mn/6+ (Mo+Cr+V)/5+ (Ni+ Cu)/15。
The addition principle of chemical element is as follows in the present invention.
C:C content difference has important influence: the higher steel grade of C content in the phase transformation of cooling procedure to steel plate, same Under the cooling condition of sample, the higher tissue of bainite or martensite equal strength easy to form in cooling procedure;But C content is too high, It then will form more crisp tissue, reduce the low-temperature impact toughness of steel plate, on the other hand, C content is too low, ferrite easy to form etc. The lower tissue of intensity.Suitable C and Ti, Nb, Mo form stable MC nanoscale precipitate, can produce strong precipitation strength The effect of effect and refined crystalline strengthening, increases substantially armor plate strength;To reach yield strength 900Mpa or more and other comprehensive power The considerations of learning performance and processing performance etc., the present invention control C content within the scope of 0.08~0.15wt%.
Si:Si element solid solution improves the intensity of steel plate in steel.Si too high levels can inhibit the formation of cementite, simultaneously Higher Si content can deteriorate the welding performance of steel plate.Therefore, the Si content control in the present invention is 0.10~0.40wt%.
Mn:Mn is weak carbide formation element, is usually solid-solubilized in steel, and the effect of solution strengthening is played.Using controlled rolling control The high-strength steel sheet that cold mode produces, Mn element pass through across diffusion interface dissipation free energy, inhibit the diffusion of sheet phase end face Control is grown up, and the sheet lath of bainite of refinement is formed, to improve the comprehensive performances such as intensity and the toughness of steel plate.Mn content It is excessively high to will lead to slab tearing tendency increasing, it is easy the defects of lobe is formed in slab production process, and Mn content is lower then It is smaller to the contribution of intensity, therefore C element or other expensive alloying elements such as Mo element etc. must be added to guarantee the strong of steel plate Degree.Addition C element can deteriorate the welding performance of steel plate, and steel plate cost can be improved by adding other noble elements.Therefore, in the present invention 1.30~2.0wt%Mn element is added, makes steel plate that there is good obdurability.
Mo:Mo element is solid-solubilized in steel in austenitizing, in the hot rolling there is certain delay austenite to tie again Crystalline substance effect, improves the defect density in deformed austeaite, in cooling procedure can be by inhibiting diffusion Interface Motion to realize refinement Final tissue.The free energy that Mo element dissipates to diffusion interface effect of dragging is approximately 3 times of Mn element, is helped in coiling process In being precipitated jointly with V, Ti, nanoscale (V, Ti, Mo) C complex precipitates are formed, significant precipitation enhancement is generated.When Mo contains When amount is lower than 0.20 wt%, above-mentioned effect is smaller, and when more than 0.45wt%, function and effect reach saturation, while Mo element is valuable The Mo of 0.20~0.45wt% is added to guarantee plate property and cost in alloying element in the present invention.
V:V is ferritisey, strongly diminution austenitic area.The V element that high temperature dissolves in austenite can increase steel Harden ability.The carbide V4C3 of V element is more stable in steel, can inhibit crystal boundary is mobile to grow up with crystal grain.V element and Cu member Element has all been precipitation enhancement in steel, but for opposite Cu element, minimal amount of V element only need to be added, that is, can reach Same precipitation strength effect.In addition, Cu element easily causes grain-boundary crack in steel;It thus must be added at least up to one The Ni element of half content, ability Crack prevention, and Ni element is equally sufficiently expensive alloying element, therefore, is replaced with V element The manufacturing cost of steel can be greatly lowered in Cu element.When V content is lower than 0.10wt%, the precipitation strength increment of generation is insufficient So that the yield strength of steel plate reaches 900Mpa, when V content is more than 0.20wt%, function and effect reach saturation, and cost compared with It is high.Therefore, the V element of 0.10~0.20wt% is added in the present invention to guarantee to have higher yield strength.
Ti:Ti and N form TiN at high temperature, and when heating of plate blank austenitizing, TiN can inhibit Austenite Grain Growth.Heat During rolling, Ti and C form nanoscale TiC in lower temperature section, tiny TiC particle have significant precipitation strength and Refined crystalline strengthening effect is conducive to the intensity and low temperature impact properties that improve steel plate, while Ti and V, Mo are common in coiling process It is precipitated, forms nanoscale (V, Ti, Mo) C complex precipitates.But works as Ti too high levels, on the one hand then will form coarse rectangular TiN is precipitated, and steel plate stress in stress is concentrated near TiN particle, and the forming core for becoming micro-crack is grown up source, reduces steel plate Fatigue behaviour.On the other hand cause Ti during (continuous casting) heating steel billet to be difficult to be dissolved since TiC solubility product is smaller, rise not To corresponding effect.In summary, the Ti content in the present invention controls within the scope of 0.10~0.20wt%.
Nb: steel plate will form the defects of a large amount of dislocation during the rolling process.Austenite occurs under the action of defect energy Recrystallization, recrystallization process include the forming core of the new crystal grain of austenite and grow up, and Nb element is by inhibiting Austenite Interfacial to move Improve the recrystallization temperature of steel plate.A certain amount of Nb, which is added, can realize two-phase control rolling, non-recrystallization zone lower temperature rolling with Dislocation density inside austenite is improved, forms the tissue of refinement in subsequent cooling procedure.Nb be realize non-recrystallization rolling, Obtain the most effective element of final fine grained texture.Nb content is higher to form coarseer NbC precipitation in drawing process, from And reduce the low-temperature impact work of steel plate.Therefore, the present invention in be added 0.015~0.050wt%Nb with control steel plate microstructure and Mechanical property.
Al:Al element forms tiny AlN at high temperature and is precipitated, and inhibits austenite grain in heating of plate blank austenitizing It grows up, achievees the purpose that austenite refinement crystal grain, improves the toughness of steel at low temperature.Al content is excessively high to will lead to biggish Al's Oxide is formed, and the low temperature impact properties and detection capability of steel plate are reduced.Therefore, it is added 0.02~0.07wt%'s in the present invention Al refines crystal grain, to improve the toughness of steel plate and guarantee its welding performance.
P, S, O, N: the objectionable impurities elements in steel can significantly reduce the plasticity and toughness and welding performance of steel, therefore Ying Jinke The above-mentioned impurity content of reduction of energy.
It is that optimization C, Mn and other constituent contents, the present invention set the relationship between C+Mn and other elements to guarantee to adopt Excellent performance is obtained with suitable composition proportion.Alloyingequivalent (AEQ) considers the condition in appropriate carbon equivalent (CEV) Under, different-alloy element and its influence to interact to obdurability.Constant term before alloying element is with the alloying element to strong The influence of toughness is related.Alloyingequivalent considers influence of the compound addition of Nb, V, Mo and Ti to mechanical property of steel plate simultaneously.Together When, alloyingequivalent is too low, can not produce the steel plate for meeting mechanical property requirements, and it is excessively high, it will lead to carbon equivalent raising, welding Penalty.
Know the present invention carbon content (0.08% to 0.15wt%) more moderate using relatively other patents, this carbon content was both Be not it is very low nor very high, can both meet the requirement of steel making working procedure, also can guarantee the subsequent requirement to welding performance of steel plate.Add The Ca and S content entered guarantees Ca/S=0.5~2.0, makes the complete nodularization of sulfide or approximate spindle, improves the lateral punching of steel plate Hit performance and cold-bending property.When V, Mo, Ti and other alloying elements in steel are added simultaneously, can not simultaneously close to the upper limit or under Limit, the purpose for the arrangement is that proof strength and carbon equivalent.To the suitable control of element described above, it is therefore intended that with lower conjunction Golden cost, accurate composition proportion, simple steel-making, rolling and cooling technique obtain steel plate (material) preferable mechanics, welding etc. Comprehensive performance.
Composition quality percentage composition as described above and its producer for bending the hot rolled steel plate (volume) that limit intensity is 900MPa grades Method includes following programs.
Smelt: to blast-melted carry out desulfurization pretreatment, it is compound that blast-melted through desulfurization pretreatment is blended into oxygen top bottom (such as 210t grades) of converter smelting, for smelting molten steel through Argon, vacuum and after adding calcium heat treatment, ladle chemistry is (i.e. qualified The mass percentage of each metallurgy element in molten steel) it is identical to the chemical component of finished product material, molten steel is after LF+RH+ Calcium treatment The steel billet that molten steel send conticaster to be casting continuously to form required cross dimensions, steel billet is with a thickness of 230mm.
Steel billet is sent into soaking pit (or heating furnace) heating, after heating steel billet is to 1150 DEG C~1300 DEG C soaking time >= 15min, such heating temperature and soaking time can be such that the austenite structure of steel billet homogenizes, and can also make Nb, V in steel billet It is sufficiently dissolved with the carbide of Ti etc., and TiN also has part and melts to prevent growing up for original austenite grains.
Steel billet after heating is rolled: roughing, 5~7 passage of roughing, the single track of roughing mill are carried out to the steel billet of heating Secondary reduction ratio >=15%, the total reduction of roughing steel billet are 70~85%.Steel billet becomes intermediate base, the centre after roughing after roughing Base enters finishing tandem rolling unit finish rolling, and intermediate base entry temperature at finishing control is between 1000~1100 DEG C, the single machine of finishing tandem rolling unit Frame reduction ratio >=10%, intermediate base are 75~97% in the total reduction of finishing tandem rolling unit.
In the second stage of rolling its finishing temperature control between 820~900 DEG C, in this operation of rolling, austenite It does not recrystallize, and forms the austenite elongated, there are a large amount of deformation band, niobium, vanadium and titaniums in the austenite crystal of elongation Being precipitated Deng solid solution atom due to deformation induced is carbide and carbonitride.After Unhydrated cement finish to gauge, the tissue of steel is The austenite structure of deformation.Steel plate thickness after finishing tandem rolling unit finish rolling is 1.2~10.0mm.
Steel plate of the steel billet after finish to gauge carries out ultra-rapid cooling with 100~300 DEG C/S of cooling velocity, with 10~25 DEG C/s layers Steel plate is cooled to 560~660 DEG C by the cooling method of stream.Cold steel plate is rolled into coil of strip with 560~660 DEG C eventually.If final cooling temperature When lower than 560 DEG C, microalloy element is precipitated slowly, and amount of precipitation is smaller, and precipitation enhancement is smaller, and intensity can be not achieved.Simultaneously Temperature is too low also to generate a large amount of bainite structure, be unfavorable for the plasticity of steel plate;If final cooling temperature is higher than 660 DEG C, it is precipitated The size of phase particle can be obvious thicker, and the tissue of ferrite matrix also can be coarse, and intensity can also be not achieved.
Coil of strip after rolling carries out slow cooling, the case where to ensure the disperse educt of carbide and improve plate shape and internal stress.
Steel plate (volume) transverse and longitudinal yield strength >=900MPa obtained through production technology as above, transverse and longitudinal elongation >=15%, Transverse and longitudinal Charpy-V impact power AKv (- 40 DEG C) >=27J.The steel plate of 1.2~10.0mm thickness is widely used in lightweight body of tipper carriage And structural member, there is good welding performance and buckling performance.

Claims (1)

1. a kind of production technology of yield strength 900MPa level hot rolled steel plate, the chemical component of steel C in terms of mass percentage: 0.08~0.15, Mo:0.20~0.5, V:0.10~0.20, Ti:0.10~0.20, Si:0.10~0.40, Mn:1.30~ 2.00, P≤0.015, S≤0.005, Nb:0.015~0.050, Al:0.02~0.07, surplus be Fe and it is other inevitably Impurity, carbon equivalent ce V≤0.55 of steel;It is characterized in that: by converter smelting through LF station Argon and RH vacuum and plus Calcium treatment Qualified molten steel steel billet is casting continuously to form by conticaster, steel billet is with a thickness of 230mm;
Steel billet is sent into heating furnace or soaking pit and is heated, soaking time is more than or equal at 1150~1300 DEG C of heating temperature 15min;
The roughing on roughing mill the steel billet after heating, total reduction of the steel billet on roughing mill are 70~85%, and steel billet is rolled into Intermediate base;
Intermediate base enters finishing tandem rolling unit finish rolling, and the entry temperature at finishing that intermediate base enters finishing tandem rolling unit is 1000~1100 DEG C, essence Rolling finishing temperature is 820~900 DEG C;Total reduction of the intermediate base on finishing tandem rolling unit is 75~97%, and intermediate base is through finishing tandem rolling Steel plate thickness after unit finish rolling is 1.2~10.0mm;
Steel plate after finish rolling carries out ultra-rapid cooling with 100~300 DEG C/s of cooling velocity, thereafter with 10~25 DEG C/s section cooling Mode steel plate is cooled to 560~600 DEG C, cold steel plate coils into coil of strip, slow cooling with 560~600 DEG C eventually.
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