CN106191678B - With the tensile strength >=1700MPa hot formings steel and production method of medium thin slab Direct Rolling - Google Patents

With the tensile strength >=1700MPa hot formings steel and production method of medium thin slab Direct Rolling Download PDF

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CN106191678B
CN106191678B CN201610713646.3A CN201610713646A CN106191678B CN 106191678 B CN106191678 B CN 106191678B CN 201610713646 A CN201610713646 A CN 201610713646A CN 106191678 B CN106191678 B CN 106191678B
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steel
rolling
1700mpa
tensile strength
control
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CN106191678A (en
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毛新平
葛锐
胡宽辉
汪水泽
潘利波
李立军
彭涛
杜晓峰
陈寅
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
    • C22C38/06—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

With tensile strength >=1700MPa hot forming steel, component and wt% of medium thin slab Direct Rolling：C:0.26~0.30%, Si：0.31~0.35%, Mn：1.3~1.5%, P≤0.008%, S≤0.005%, Als：0.015~0.060%, Cr：0.31~0.35%, Ti：0.031~0.035% or Nb：0.031~0.035% or V：0.031~0.035% or two of which more than with the mixing of arbitrary proportion, B：0.003~0.004%, Mo：0.20~0.25%, Ni：0.06~0.10%, 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；It batches；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 is of great significance after deforming without rebound, the dimensional accuracy height of part for automobile lightweight.

Description

With tensile strength >=1700MPa hot formings steel of medium thin slab Direct Rolling and production Method
Technical field
The present invention relates to a kind of auto parts and components steel and its production methods, specifically belong to a kind of direct with medium thin slab The tensile strength of rolling >=1700MPa hot formings steel and production method, and it is more than 2 to 10mm suitable for the product thickness of production.
Background technology
As automobile industry development and automobile industry gradually send out Automobile Design and manufacture to energy-saving and environmental protection, safe direction Exhibition, automotive light weight technology become the main flow direction of significant period of time Automobile Design at present and in the future.
The study found that the complete vehicle weight and energy consumption of automobile 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 comfort is not reduced, automobile weight in working order can be greatly reduced by adopting.But with intensity It is continuously improved, the forming property of steel plate can worse and worse, the especially unimach of more than 1700MPa, in forming process There can be the problems such as precision that cracking, rebound and accessory size do not reach requirement, and higher also is proposed to stamping equipment simultaneously Requirement, that is, need the press machine of large-tonnage and high abrasion mold, and also have large effect to the service life of mold.Mesh The preceding country also can not shape the cold forming stamping equipment and mold of more than 1700MPa.
Currently, both at home and abroad the tensile strength of existing hot forming steel cannot reach 1700MPa and more than, and all using cold Roll annealed state or cold rolled annealed rear precoated shet.Its technological process of production is：Desulphurised hot metal → converter smelting → external refining → company Casting → heating of plate blank → hot continuous rolling → pickling+cold continuous rolling → continuous annealing →（Precoated shet）→ finishing packaging → blanking → heating → Mould punching quenches.It is longer there are the technological process of production, the higher deficiency of cost.Some impact resistant or load bearing component are adopted Impact resistant and bearing capacity are improved with multiple part combination components, and causes to greatly improve the cost of raw material and be processed into This.
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 2.0~10 mm specification steel plates of ＞ and steel band can be produced with Direct Rolling by casting continuous rolling process, some can only use cold rolling high-strength originally The Thin Specs part of steel is gradually directly rolled using casting and rolling process to increase intensity using the structure of multiple parts composition Ultrahigh-strength steel plates processed are replaced.Such as the Patent exploitation yield strength that China Patent Publication No. is CN 102965573A（ReL） >=700MPa, tensile strength（Rm）The engineering structure high strength steel of >=750MPa, 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 is smelting and is casting continuously to form base, into Row soaking, for control soaking temperature at 1200~1300 DEG C, soaking time is 20~60min；It is rolled, and controls start rolling temperature Not less than 1200 DEG C, finishing temperature is at 870~930 DEG C；Section cooling is carried out, is cooled down under being not less than 20 DEG C/s in cooling velocity To coiling temperature；It is batched, and controls coiling temperature at 580~650 DEG C.China Patent Publication No. is CN 103658178A A kind of method of short route production high-strength thin strip steel of patented invention, the strip yield strength invented（ReL）≥ 550MPa, tensile strength（Rm）>=600MPa, chemical composition mass percent are：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 For Fe and inevitable impurity, the Cast Strip of 1.0~2.0mm thickness is cast into after smelting, 60~150m/min of casting rate is rolled System controls 850~1000 DEG C of finishing temperature；It is cooled down using atomization, 50~100 DEG C/s of cooling velocity is batched, control is batched Temperature is 520~660 DEG C.The tensile strength of above-mentioned two document is very low, it is impossible to meet high-end body of a motor car to more than 1700MPa The demand of superhigh intensity.
Invention content
The invention reside in overcoming, intensity rank of the existing technology is low, it is impossible to meet user to superhigh intensity part demand Deficiency, providing a kind of can not only meet requirement of the Automobile Design to superhigh intensity mechanical property, but also can smoothly complete complicated change Shape, and without rebound after deforming, the high tensile strength >=1700MPa hot formings steel of the dimensional accuracy of part and production method.
Realize the measure of above-mentioned purpose：
With tensile strength >=1700MPa hot forming steel, component and weight percent content of medium thin slab Direct Rolling For：C:0.26~0.30%, Si：0.31~0.35%, Mn：1.3~1.5%, P≤0.008%, S≤0.005%, Als：0.015 ~0.060%, Cr：0.31~0.35%, Ti：0.031~0.035% or Nb：0.031~0.035% or V：0.031~0.035% or More than two of which with the mixing of arbitrary proportion, B：0.003~0.004%, Mo：0.20~0.25%, Ni：0.06~0.10%, N ≤ 0.005%, remaining is Fe and inevitable impurity；Quenched metallographic structure is full lath martensite；Mechanical property：Surrender The MPa of intensity >=1150, tensile strength >=1700MPa, elongation A80mm≥5%。
The method of tensile strength >=1700MPa hot forming steel of production medium thin slab Direct Rolling, it is characterised in that：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, packet molten steel overheat is at 15~30 DEG C in control, and slab thickness is in 61~150mm, casting speed In 2.8~5.5 m/min；
4）It carries out strand and enters the de-scaling processing before soaking pit, and control the pressure of de-scaling water in 300~400 bar；
5）Carry out conventional soaking to strand, in weak oxide atmosphere in control soaking pit, even if 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 for 1150~ 1180℃；
7）The high-pressure water descaling before feed mill is carried out, and controls de-scaling water pressure in 280~420bar；
8）Rolling, and the first percentage pass reduction of control is：40~50%, the second percentage pass reduction is：40~50%, extreme trace Reduction ratio is：10~16%；Controlled rolling speed is in 3~8 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 840~880 DEG C；
9）It is 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）It is batched, and it is 615 ~ 645 DEG C to control coiling temperature；
11）The austenitizing after uncoiling blanking is carried out, control austenitizing temperature keeps the temperature 6~15 at 930~980 DEG C min；
12）Mould punching shapes, and 6~9 s of pressurize in mold；
13）It is quenched, control quenching cooling velocity is in 50~100 DEG C/s；Cooled to room temperature afterwards.
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 producing lines carry out.
The effect of each element and main technique and mechanism in the present invention
C：Carbon is strong solution strengthening element, and to being played a decisive role for superhigh intensity, carbon content is to the group of final products Knitting form and performance has larger impact, but content is too high, easily formed in the cooling procedure after finish rolling a large amount of pearlite or Bainite, martensite, content is higher, and intensity is higher, and so as to which plasticity be caused to reduce, the blanking before being formed is difficult.So Under the premise of heat treatment reinforcement is ensured, carbon content is not easy excessively high.Therefore its content is limited to 0.26~0.30% range.
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 change 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 0.31~0.35% range.
Mn：Manganese plays solution strengthening effect, while can remove the FeO in steel, significantly improves the quality of steel.It can also be with sulfide Dystectic MnS is generated, in hot-working, MnS has enough plasticity, and steel is made not generate 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 1.3~1.5% ranges.
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 0.31~0.35% range.
B:Boron is strong raising quenching degree element, and the quenching degree of steel can be significantly improved by adding in micro boron element in steel.But It is that its content is less than 0.003% or higher than 0.004%, to improving the effect unobvious of quenching degree.So to consider to produce Its content is limited to 0.003~0.004% range by reality and quenching degree effect.
Als plays deoxidation in steel, and should ensure that in steel has a certain amount of dissolved aluminum, otherwise cannot play its effect, But excessive aluminium can also be such that generation aluminium system in steel is mingled with, and be unfavorable for the smelting and casting of steel.Simultaneously suitable 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% range.
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 brittleness of steel.Based on cost consideration and the performance of steel is not influenced simultaneously, the control of its content is existed Less than 0.008%.
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 lower better.Based on to system This considerations of is caused, by sulfur content control in steel below 0.005%.
N：Nitrogen can be combined to form titanium nitride with titanium in the steel for adding titanium, and this second phase being precipitated at high temperature is conducive 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, at high temperature The coarse 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 needed for nitrogen increases, 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 the hardness and strength so as to reduce martensite after experiment steel quenches with C.In addition, the addition of titanium has the quenching degree of steel Certain contribution.So its content is limited to 0.031~0.035% range.
Nb、V:Niobium and vanadium are also strong C, N compound formation element, can play the role of fining austenite grains, be added in steel A small amount of niobium or vanadium can form the carbon of a certain amount of niobium, nitride, so as to hinder Austenite Grain Growth, therefore, quench Martensite lath size after fire is smaller, greatly improves the intensity of steel.Therefore by its content control 0.031~0.035% it Between.
Mo：Molybdenum can significantly improve the quenching degree of steel, and the stacking fault energy of molybdenum is higher, add in the low temperature modeling that steel can be improved in steel Property and toughness.Therefore by the control of its content between 0.20~0.25%.
Ni：Nickel, which is added in steel, can improve the intensity of steel without significantly reducing its toughness.Simultaneously can improve steel processability and Solderability.In addition, nickel can improve the resistance to corrosion of steel, it can not only be acidproof, and the corrosion of energy alkali resistant and air.It so will Its content is limited to 0.06~0.10%.
Why the present invention takes de-scaling three times in entire 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.Additionally by one, two and final reduction rate control, it can be achieved that the even tissue and performance of strip are stablized.
Compared with prior art, the present invention its intensity is high, manufacturing process is short, and product surface quality is good, and thickness and precision is high, energy Enough reach the quality requirement of cold-rolled products, substantially save energy consumption；In addition, with existing medium thin slab Direct Rolling product phase Than intensity is significantly larger than existing product, is of great significance for automobile lightweight.
Description of the drawings
Fig. 1 is product metallographic structure figure of the present invention.
Specific embodiment
The present invention is described in detail below：
Table 1 is various embodiments of the present invention and the chemical composition comparative example of comparative example；
Table 2 is various embodiments of the present invention and the main technologic parameters comparative example of comparative example；
Table 3 is various embodiments of the present invention and the performance text list of 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, packet molten steel overheat is at 15~30 DEG C in control, and slab thickness is in 61~150mm, casting speed In 2.8~5.5 m/min；
4）It carries out strand and enters the de-scaling processing before soaking pit, and control the pressure of de-scaling water in 300~400 bar；
5）Carry out conventional soaking to strand, in weak oxide atmosphere in control soaking pit, even if 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 for 1150~ 1180℃；
7）The high-pressure water descaling before feed mill is carried out, and controls de-scaling water pressure in 280~420bar；
8）Rolling, and the first percentage pass reduction of control is：40~50%, the second percentage pass reduction is：40~50%, extreme trace Reduction ratio is：10~16%；Controlled rolling speed is in 3~8 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 840~880 DEG C；
9）It is 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）It is batched, and it is 615 ~ 645 DEG C to control coiling temperature；
11）The austenitizing after uncoiling blanking is carried out, control austenitizing temperature keeps the temperature 6~15 at 930~980 DEG C min；
12）Mould punching shapes, and 6~9 s of pressurize in mold；
13）It is quenched, control quenching cooling velocity is in 50~100 DEG C/s；Cooled to room temperature afterwards.
The chemical composition of 1 various embodiments of the present invention of table and comparative example（wt.%）
The main technologic parameters comparative example of 2 various embodiments of the present invention of table and comparative example
The mechanical property situation list of 3 various embodiments of the present invention of table and comparative example
From table 3 it can be seen that the intensity that the application is successfully realized invention steel by shorter technological process reaches More than 1700MPa is of great significance for the development for promoting automotive light weight technology.
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 tensile strength >=1700MPa hot forming steel of medium thin slab Direct Rolling is used, thin plate in the use The tensile strength of base Direct Rolling >=1700MPa hot forming steel, component and weight percent content are：C:0.26~ 0.30%, Si：0.31~0.35%, Mn：1.3~1.5%, P≤0.008%, S≤0.005%, Als：0.015~0.060%, Cr： 0.31~0.35%, Ti：0.031~0.035% or Nb：0.031~0.035% or V：0.031~0.035% or two of which more than With the mixing of arbitrary proportion, B：0.003~0.004%, Mo：0.20~0.25%, Ni：0.06~0.10%, N≤0.005%, Yu Wei Fe and inevitable impurity；Quenched metallographic structure is full lath martensite；Mechanical property：Yield strength >=1150 MPa, tensile strength >=1700MPa, elongation A80mm≥5%；Production stage：
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, packet molten steel overheat is at 15~30 DEG C in control, and slab thickness is in 61~150mm, and casting speed is 2.8 ~5.5 m/min；
4）It carries out strand and enters 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 heated, and controls strand charging temperature at 780~1000 DEG C, tapping temperature is 1150~1180 DEG C；
7）The high-pressure water descaling before feed mill is carried out, and controls de-scaling water pressure in 280~420bar；
8）Rolling, and the first percentage pass reduction of control is：40~50%, the second percentage pass reduction is：40~50%, extreme trace time pressure Rate is：10~16%；Controlled rolling speed is in 3~8 m/s；And water de-scaling is pressed in being carried out between the first passage and second time, De-scaling water pressure is 200~280bar；Finishing temperature is controlled at 840~880 DEG C；
9）It is 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）It is batched, and it is 615~645 DEG C to control coiling temperature；
11）The austenitizing after uncoiling blanking is carried out, control austenitizing temperature keeps the temperature 6~15 min at 930~980 DEG C；
12）Mould punching shapes, and 6~9 s of pressurize in mold；
13）It is quenched, control quenching cooling velocity is in 50~100 DEG C/s；Cooled to room temperature afterwards.
2. as described in claim 1 with the producer of tensile strength >=1700MPa hot forming steel of medium thin slab Direct Rolling Method, it is characterised in that：The operation of rolling of the medium thin slab is 6F producing lines or 1R+6F producing lines or 2R+6F in rolling mill layout Producing line or 7F producing lines or 3R+4F producing lines or 2R+5F producing lines or 1R+5F producing lines carry out.
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CN108823493A (en) * 2018-06-26 2018-11-16 武汉钢铁有限公司 The strong automobile structure steel of environmentally friendly superelevation and its production method
CN108754099A (en) * 2018-06-27 2018-11-06 武汉钢铁有限公司 Reduce the heat treatment method of 1700MPa grades of hot forming steel hydrogen-induced delayed fracture sensibility
CN109023115B (en) * 2018-09-29 2020-01-31 武汉钢铁有限公司 hot-rolled template pull sheet steel and manufacturing method thereof
CN110306123A (en) * 2019-07-26 2019-10-08 马鞍山钢铁股份有限公司 A kind of tensile strength >=1800MPa grades of high-toughness hot forming steel and its production method
CN110499460B (en) * 2019-08-22 2021-05-11 唐山钢铁集团有限责任公司 Cold-rolled steel strip for hot stamping forming and production method thereof
CN113684418A (en) * 2021-08-11 2021-11-23 北京理工大学重庆创新中心 High-hardenability hot-rolled hot-formed high-strength steel for tipping wagon carriage
CN114058968A (en) * 2021-11-19 2022-02-18 鞍钢股份有限公司 High-plasticity hot forming steel with oxidation resistance for automobile and hot forming process
CN116837296A (en) * 2023-08-22 2023-10-03 北京理工大学重庆创新中心 Preparation method and application of anti-oxidation hot forming steel suitable for thick specification

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