CN106086632B - With the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling and production method - Google Patents

With the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling and production method Download PDF

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CN106086632B
CN106086632B CN201610713632.1A CN201610713632A CN106086632B CN 106086632 B CN106086632 B CN 106086632B CN 201610713632 A CN201610713632 A CN 201610713632A CN 106086632 B CN106086632 B CN 106086632B
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CN106086632A (en
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毛新平
胡宽辉
李立军
汪水泽
葛锐
潘利波
彭涛
杜晓峰
周少云
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Wuhan Iron and Steel Co Ltd
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    • 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
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

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

Abstract

With the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling, its component and wt%：C:0.12~0.16%, Si：0.15~0.20%, Mn：0.7~1.0%, P≤0.02%, S≤0.008%, Als：0.015~0.060%, Cr：0.15~0.20%, Ti：0.005~0.02% or Nb：0.005~0.02% or V：0.005~0.02% or two of which more than with the mixing of arbitrary proportion, B：0.0005~0.0020%, N≤0.005%.Production stage：Desulfurizing iron；Electric furnace or converter smelting and refining；Continuous casting；Enter the processing of the de-scaling before soaking pit；Soaking；Heating；High-pressure water descaling before feed mill；Rolling；Cooling；Batch；Austenitizing；Mould punching shapes；Quenching.Flow of the present invention is short, and product surface quality is good, and thickness and precision is high, can reach the quality requirement of cold-rolled products, can smoothly complete complex deformation, and high without resilience, the dimensional accuracy of part after deformation.

Description

With the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling and production Method
Technical field
The present invention relates to a kind of auto parts and components steel and its production method, specifically belongs to one kind and is directly rolled with sheet billet The thin hot forming steel of tensile strength >=1100MPa and production method of system, and suitable for production product thickness 0.8 to 2mm.
Background technology
As automobile industry development and automobile industry are gradually sent out Automobile Design and manufacture to energy-saving and environmental protection, safe direction Exhibition, automotive light weight technology turn into the main flow direction of significant period of time Automobile Design at present and in the future.
Research finds that the complete vehicle weight of automobile and energy resource consumption are linear.According to statistics, vehicle weight often reduces by 10% Then fuel efficiency can improve 6%~8%.One of most important approach of automotive light weight technology is to use high intensity and unimach, from And can make while crashworthiness and comfortableness is not reduced, automobile weight in working order is greatly reduced.It is but continuous with intensity Improve, the forming property of steel plate can worse and worse, and especially more than 1100MPa unimach can be deposited in forming process Cracking, resilience and parts size precision do not reach requirement the problems such as, and higher requirement is also proposed to pressing equipment simultaneously, The stamping machine and high abrasion mould of large-tonnage are needed, and also has large effect to the mold use cycle.It is domestic at present Also without the cold forming pressing equipment and mould that can shape more than 1100MPa.
Currently, existing hot forming steel uses cold rolled annealed state or cold rolled annealed rear precoated shet both at home and abroad.Its production technology Flow is：Desulphurised hot metal → converter smelting → external refining → continuous casting → heating of plate blank → hot continuous rolling → pickling+cold continuous rolling → company Continuous annealing →（Precoated shet）→ finishing packaging → blanking → heating → mould punching quenching.It is longer to there is the technological process of production, into This higher deficiency.Impact resistant and carrying are improved for some impact resistant or load bearing component using multiple part combination components Ability, and cause to greatly improve the cost of raw material and processing cost.
With the development of steel and iron industry, medium thin slab continuous casting and rolling technique has obtained tremendous development, is connected using medium thin slab 0.8~2 mm specification steel plates and steel band can be produced with Direct Rolling by casting continuous rolling process, and some can only use cold rolling high-strength steel originally Thin Specs part or for increase intensity using multiple parts composition component progressively use casting and rolling process Direct Rolling Ultrahigh-strength steel plates are replaced.Such as Application No. CN 102965573A Patent exploitation yield strength（ReL）>=700MPa, resist Tensile strength（Rm）>=750MPa engineering structure high strength steel, its component percentages are：C:0.15~0.25%, Si:≤ 0.10%, Mn:1.00~1.80%, P:≤ 0.020%, S≤0.010%, Ti:0.09~0.20%, Als:0.02~0.08%, N ≤ 0.008%, remaining is Fe and is inevitably mingled with；Its production stage carries out soaking, control is equal to smelt and being casting continuously to form base For hot temperature at 1200~1300 DEG C, soaking time is 20~60min；Rolled, and control start rolling temperature to be not less than 1200 DEG C, Finishing temperature is at 870~930 DEG C；Section cooling is carried out, coiling temperature is cooled under being not less than 20 DEG C/s in cooling velocity；Enter Row batches, and controls coiling temperature at 580~650 DEG C.A kind of short route of Patent No. CN 103658178A patented invention The method for producing high-strength thin strip steel, the strip yield strength invented（ReL）>=550MPa, tensile strength（Rm）>=600MPa, Its chemical composition mass percent is：C:0.02~0.15%, Si:0.20~0.6%, Mn:0.2~1.50%, P:0.02~ 0.3%, S≤0.006%, Cr:0.40~0.8%, Ni:0.08~0.40%, Cu:0.3~0.80%, Nb:0.010~0.025%, Ti:0.01~0.03%, Al:0.01~0.06%, Re:0.02~0.25%;Remaining is Fe and inevitable impurity, is poured after smelting The thick Cast Strips of 1.0~2.0mm are cast, 60~150m/min of casting rate, are rolled, control 850~1000 DEG C of finishing temperature； Cooled down, 50~100 DEG C/s of cooling velocity, batched using atomization, it is 520~660 DEG C to control coiling temperature.
The tensile strength of above-mentioned two document is very low, it is impossible to meets high-end body of a motor car to more than 1100MPa superhigh intensitys Demand.
The content of the invention
The invention reside in overcoming, intensity rank existing for prior art is low, it is impossible to meets user to superhigh intensity part demand Deficiency, there is provided a kind of flow is short, and product surface quality is good, and thickness and precision is high, can reach the quality requirement of cold-rolled products, energy Smoothly complete complex deformation, and without resilience after deforming, the high tensile strength >=1100MPa hot formings steel of the dimensional accuracy of part and Production method.
Realize the measure of above-mentioned purpose：
With the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling, its component and weight percent content For：C:0.12~0.16%, Si：0.15~0.20%, Mn：0.7~1.0%, P≤0.02%, S≤0.008%, Als：0.015~ 0.060%, Cr：0.15~0.20%, Ti：0.005~0.02% or Nb：0.005~0.02% or V：0.005~0.02% or wherein The two or more mixing with arbitrary proportion, B：0.0005~0.0020%, N≤0.005%, remaining is Fe and inevitable impurity.
The production method of the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling, it is：It is walked Suddenly：
1）Desulfurizing iron, and S≤0.002% is controlled, molten iron exposed surface is not less than 96% after skimming；
2）Conventional electric furnace or converter smelting, and conventional refinery；
3）Continuous casting is carried out, at 15~30 DEG C, slab thickness exists bag molten steel overheat in 55~60mm, casting speed in control 3.5~7.0 m/min；
4）Carry out strand and enter the de-scaling processing before soaking pit, and control the pressure of de-scaling water in 300~400 bar；
5）Conventional soaking is carried out to strand, is in weak oxide atmosphere in control soaking pit, though remaining oxygen is 0.5 in stove~ 5.0%；
6）Strand is heated, and controls strand charging temperature at 780~1000 DEG C, tapping temperature is 1170~1190 ℃；
7）The high-pressure water descaling before feed mill is carried out, and controls de-scaling water pressure in 280~420bar；
8）Rolling, and control the first percentage pass reduction to be：52~63%, the second percentage pass reduction is：50~60%, extreme trace Reduction ratio is：10~16%；Controlled rolling speed is in 8~12 m/s；And press water in being carried out between the first passage and second time De-scaling, de-scaling water pressure are 200~280bar；Finishing temperature is controlled at 830~870 DEG C；
9）Cooled down, the type of cooling is cooled to for the mode of section cooling or Water-Curta in Cooling or encryption cooling and batches temperature Degree；
10）Batched, and it is 685 ~ 715 DEG C to control coiling temperature；
11）The austenitizing after uncoiling blanking is carried out, control austenitizing temperature is incubated 3~5 at 850~920 DEG C min；
12）Mould punching shapes, and the s of pressurize 10~20 in mould；
13）Quenched, control quenching cooling velocity is in 20~40 DEG C/s；After naturally cool to room temperature.
It is：：The operation of rolling of the medium thin slab is 6F producing lines or 1R+6F producing lines or 2R+ in rolling mill layout 6F producing lines or 7F producing lines or 3R+4F producing lines or 2R+5F producing lines or 1R+5F short routes producing line are carried out.
The effect of each element and main technique and mechanism in the present invention
C：Carbon is strong solution strengthening element, to being played a decisive role for superhigh intensity, group of the carbon content to final products Knitting form and performance has considerable influence, but content is too high, easily formed in the cooling procedure after finish rolling substantial amounts of pearlite or Bainite, martensite, its content is higher, and intensity is higher, and so as to cause plasticity to reduce, the blanking before being formed is difficult.So On the premise of heat treatment reinforcement is ensured, carbon content is not easy too high.Therefore its content is limited to 0.12~0.16% scope.
Si：Silicon has stronger solid solution strengthening effect, can improve the intensity of steel, meanwhile, silicon can improve the quenching degree of steel, have and subtract Few effect of the austenite to Volume Changes during martensite transfor mation, so as to effectively control the generation of hardening flaw；In lonneal Carbon diffusion can be hindered, delays the speed of martensite decomposition and carbide agglomeration, declines steel hardness in tempering slower, Significantly improve steel belt roof bolt stability and intensity.So its content is limited to 0.15~0.20% scope.
Mn：Manganese plays solution strengthening effect, while can remove the FeO in steel, significantly improves the quality of steel.Can also be with sulfide Dystectic MnS is generated, in hot-working, MnS has enough plasticity, steel is not produced hot-short phenomenon, mitigates harmful work of sulphur With improving the hot-working character of steel.Manganese can reduce phase driving force, move to right " C " curve, improve the quenching degree of steel, expand γ Phase region, separately it can reduce the Ms points of steel, therefore can ensure to obtain martensite under suitable cooling velocity.So its content is limited It is scheduled on 0.7~1.0% scope.
C:0.12~0.16%, Si：0.15~0.20%, Mn：0.7~1.0%, P≤0.02%, S≤0.008%, Als： 0.015~0.060%, Cr：0.15~0.20%, Ti：0.005~0.02% or Nb：0.005~0.02% or V：0.005~0.02% Or more than two of which with the mixing of arbitrary proportion, B：0.0005~0.0020%, Mo：0.10~0.13%, N≤0.005%
Cr：Chromium can reduce phase driving force, and the forming core of carbide is grown up when also reducing phase transformation, so improving the through hardening of steel Property.In addition, chromium can improve steel belt roof bolt stability.So its content is limited to 0.15~0.20% scope.
B:Boron is strong raising quenching degree element, and the quenching degree of steel can be significantly improved by adding micro boron element in steel.But It is that its content is less than 0.0005%, or higher than 0.002%, the effect unobvious to improving quenching degree.So to consider to produce Reality and quenching degree effect, its content is limited to 0.0005~0.002% scope.
Als, it plays deoxidation in steel, and should ensure that in steel has a certain amount of dissolved aluminum, otherwise can not play its effect, But excessive aluminium also can be mingled with generation aluminium system in steel, and be unfavorable for the smelting and casting of steel.Simultaneously appropriate aluminium is added in steel Nitrogen in steel, oxygen atom can be eliminated to the adverse effect of performance.Therefore its content is limited to 0.015~0.060% scope.
P：Phosphorus is the harmful element in steel, easily causes center segregation of casting blank.In subsequent hot continuous rolling heating process easily partially Gather crystal boundary, significantly increase the fragility of steel.While based on cost consideration and the performance of steel is not influenceed, the control of its content is existed Less than 0.02%.
S：Sulphur is very harmful element.Sulphur in steel often exists with the oxide morphology of manganese, this sulphide inculsion meeting Deteriorate the toughness of steel, and cause the anisotropy of performance, therefore, sulfur content in steel need to be controlled more low better.Based on to system This consideration is caused, by sulfur content control in steel below 0.008%.
N：Nitrogen can combine to form titanium nitride in the steel for add titanium with titanium, and this second phase separated out at high temperature is advantageous to by force Change matrix, and improve the welding performance of steel plate.But nitrogen content, higher than 0.005%, the solubility product of nitrogen and titanium is higher, in high temperature The thick titanium nitride of particle will be formed in steel, the serious plasticity and toughness for damaging steel；In addition, higher nitrogen content can make stabilization Micro alloying element content increase needed for nitrogen, so as to increase cost.Therefore by the control of its content below 0.005%.
Ti：Titanium is strong C, N compound formation element, and the purpose that Ti is added in steel is the N element in fixed steel, but excessive Ti can be combined with C so as to reduce the hardness and intensity of martensite after experiment steel quenches.In addition, the addition of titanium has to the quenching degree of steel Certain contribution.So its content is limited to 0.005~0.02% scope.
Nb、V:Niobium and vanadium are also strong C, N compound formation element, can play a part of fining austenite grains, be added in steel A small amount of niobium or vanadium can forms the carbon of a certain amount of niobium, nitride, and so as to hinder Austenite Grain Growth, therefore, it is quenched Martensite lath size after fire is smaller, greatly improves the intensity of steel.Therefore its content is controlled between 0.005~0.02%.
Why the present invention takes de-scaling three times in whole production process, is due to by controlling de-scaling passage and suitable De-scaling water pressure, the iron scale of belt steel surface can be removed as far as possible, so as to ensure that strip has good surface matter Amount.Controlled additionally by one, two and last percentage pass reduction, the even tissue and stable performance of strip can be achieved.
Compared with prior art, flow is short, and product surface quality is good by the present invention, and thickness and precision is high, can reach cold rolling production The quality requirement of product, complex deformation can be smoothly completed, and it is high without resilience, the dimensional accuracy of part after deformation.
Brief description of the drawings
Fig. 1 is product metallographic structure figure of the present invention.
Embodiment
The present invention is described in detail below：
Table 1 is the chemical composition comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters comparative example of various embodiments of the present invention and comparative example；
Table 3 is the performance text list of various embodiments of the present invention and comparative example.
Various embodiments of the present invention press following technique productions：
1）Desulfurizing iron, and S≤0.002% is controlled, molten iron exposed surface is not less than 96% after skimming；
2）Conventional electric furnace or converter smelting, and conventional refinery；
3）Continuous casting is carried out, at 15~30 DEG C, slab thickness exists bag molten steel overheat in 55~60mm, casting speed in control 3.5~7.0 m/min；
4）Carry out strand and enter the de-scaling processing before soaking pit, and control the pressure of de-scaling water in 300~400 bar；
5）Conventional soaking is carried out to strand, is in weak oxide atmosphere in control soaking pit, though remaining oxygen is 0.5 in stove~ 5.0%；
6）Strand is entered to heat, and controls strand charging temperature at 780~1000 DEG C, tapping temperature is 1170~ 1190℃；
7）The high-pressure water descaling before feed mill is carried out, and controls de-scaling water pressure in 280~420bar；
8）Rolling, and control the first percentage pass reduction to be：52~63%, the second percentage pass reduction is：50~60%, extreme trace Reduction ratio is：10~16%；Controlled rolling speed is in 8~12 m/s；And press water in being carried out between the first passage and second time De-scaling, de-scaling water pressure are 200~280bar；Finishing temperature is controlled at 830~870 DEG C；
9）Cooled down, the type of cooling is cooled to for the mode of section cooling or Water-Curta in Cooling or encryption cooling and batches temperature Degree；
10）Batched, and it is 685 ~ 715 DEG C to control coiling temperature；
11）The austenitizing after uncoiling blanking is carried out, control austenitizing temperature is incubated 3~5 at 850~920 DEG C min；
12）Mould punching shapes, and the s of pressurize 10~20 in mould；
13）Quenched, control quenching cooling velocity is in 20~40 DEG C/s；After naturally cool to room temperature.
The chemical composition of the various embodiments of the present invention of table 1 and comparative example（wt.%）
The main technologic parameters comparative example of the various embodiments of the present invention of table 2 and comparative example
The mechanical property situation list of the various embodiments of the present invention of table 3 and comparative example
From table 3 it can be seen that by the abbreviated system of sheet billet Direct Rolling, the intensity for realizing invention steel reaches More than 1100MPa, it can reach with hot Dai Leng purpose, while its intensity is significantly larger than existing short route producing line product strength, For promoting automotive light weight technology development significant.
Present embodiment is only the best example, not to the restricted implementation of technical solution of the present invention.

Claims (2)

1. the production method of the thin hot forming steel of tensile strength >=1100MPa with sheet billet Direct Rolling, described straight with sheet billet The component and weight percent content for connecing the thin hot forming steel of tensile strength >=1100MPa of rolling be：C:0.12~0.13%, Si：0.15~0.19%, Mn：0.7~1.0%, P≤0.02%, S≤0.008%, Als：0.046~0.060%, Cr：0.15~ 0.20%, Ti：0.005~0.012% or Nb：0.005~0.02% or V：0.005~0.02% or two of which more than arbitrarily to compare The mixing of example, B：0.0005~0.0009%, N≤0.005%, remaining is Fe and inevitable impurity；Its step：
1）Desulfurizing iron, and S≤0.002% is controlled, molten iron exposed surface is not less than 96% after skimming；
2）Conventional electric furnace or converter smelting, and conventional refinery；
3）Continuous casting is carried out, bag molten steel overheat is at 15~30 DEG C in control, and slab thickness is in 55~60mm, and casting speed is 3.5 ~7.0 m/min；
4）Carry out strand and enter the de-scaling processing before soaking pit, and control the pressure of de-scaling water in 300~400 bar；
5）Conventional soaking is carried out to strand, is in weak oxide atmosphere in control soaking pit, even if remaining oxygen is 0.5~5.0% in stove；
6）Strand is entered to heat, and controls strand charging temperature at 780~1000 DEG C, tapping temperature is 1170~1190 ℃；
7）The high-pressure water descaling before feed mill is carried out, and controls de-scaling water pressure in 280~420bar；
8）Rolling, and control the first percentage pass reduction to be：52~63%, the second percentage pass reduction is：50~60%, extreme trace time pressure Rate is：10~16%；Controlled rolling speed is in 8~12 m/s；And pressure water removes in being carried out between the first passage and second time Squama, de-scaling water pressure are 200~280bar；Finishing temperature is controlled at 830~870 DEG C；
9）Cooled down, the type of cooling is cooled to coiling temperature for the mode of section cooling or Water-Curta in Cooling or encryption cooling；
10）Batched, and it is 685 ~ 715 DEG C to control coiling temperature；
11）The austenitizing after uncoiling blanking is carried out, control austenitizing temperature is incubated 3~4.5 at 905~920 DEG C min；
12）Mould punching shapes, and the s of pressurize 10~20 in mould；
13）Quenched, control quenching cooling velocity is in 20~40 DEG C/s；After naturally cool to room temperature.
2. the producer of the thin hot forming steel of tensile strength >=1100MPa of sheet billet Direct Rolling is used as claimed in claim 1 Method, it is characterised in that：The operation of rolling of the sheet billet is 6F producing lines or 1R+6F producing lines or 2R+6F productions in rolling mill layout Line or 7F producing lines or 3R+4F producing lines or 2R+5F producing lines or 1R+5F short route producing line are carried out.
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CN107190203B (en) * 2017-05-31 2019-07-23 武汉钢铁有限公司 With the yield strength >=800MPa hot rolled sheet and production method of sheet billet Direct Rolling
CN108396224A (en) * 2018-04-03 2018-08-14 河钢股份有限公司承德分公司 A kind of hot press-formed ultra-thin hot-rolled strip steel and its production method
CN112760554A (en) * 2019-10-21 2021-05-07 宝山钢铁股份有限公司 High-strength steel with excellent ductility and manufacturing method thereof
CN116200677A (en) * 2022-12-15 2023-06-02 本钢板材股份有限公司 A high-strength hot-rolled coil plate for a vehicle frame with a tensile strength of 1100MPa and its manufacturing method

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CN104419877A (en) * 2013-09-05 2015-03-18 鞍钢股份有限公司 Cold-rolled martensitic steel with weather resistance and manufacturing method thereof

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