CN106191678A - By the tensile strength of medium thin slab Direct Rolling >=1700MPa hot forming steel and production method - Google Patents

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

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CN106191678A
CN106191678A CN201610713646.3A CN201610713646A CN106191678A CN 106191678 A CN106191678 A CN 106191678A CN 201610713646 A CN201610713646 A CN 201610713646A CN 106191678 A CN106191678 A CN 106191678A
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steel
rolling
1700mpa
cooling
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CN106191678B (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 the tensile strength of medium thin slab Direct Rolling >=1700MPa hot forming steel, its component and wt%: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%, more than Ti:0.031～0.035% or Nb:0.031～0.035% or V:0.031～0.035% or 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%.Production stage: desulfurizing iron；Electric furnace or converter smelting and refine；Continuous casting；Enter the de-scaling before soaking pit to process；Soaking；Heating；High-pressure water descaling before feed mill；Rolling；Cooling；Batch；Austenitizing；Mould punching shapes；Quenching.Flow process of the present invention is short, and product surface quality is good, and thickness and precision is high, it is possible to reach the prescription of cold-rolled products, high without resilience, the dimensional accuracy of part after smoothly completing complex deformation, and deformation, is significant for automobile lightweight.

Description

With the tensile strength of medium thin slab Direct Rolling >=1700MPa hot forming steel and production Method
Technical field
The present invention relates to a kind of auto parts and components steel and production method thereof, specifically belong to one medium thin slab direct Tensile strength >=1700MPa hot forming the steel of rolling and production method, and the product thickness being applicable to produce is more than 2 to 10mm.
Background technology
Along with Automobile Design and manufacture are gradually sent out by automobile industry development and automobile industry to energy-saving and environmental protection, safe direction Exhibition, automotive light weight technology becomes the main flow direction of significant period of time Automobile Design at present and in the future.
Research finds, complete vehicle weight and the energy resource 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 not reducing crashworthiness and comfortableness, adopt and automobile weight in working order can be greatly reduced.But along with intensity Improving constantly, the forming property of steel plate can worse and worse, and the unimach of especially more than 1700MPa, in forming process Cracking, resilience and accessory size can be there is and do not reach the problems such as permissible accuracy, and also pressing equipment be proposed higher simultaneously Requirement, i.e. need large-tonnage stamping machine and high abrasion mould, and the mold use cycle also had large effect.Mesh The front domestic cold forming pressing equipment also not having to shape more than 1700MPa and mould.
Currently, the tensile strength of domestic and international existing hot forming steel all can not arrive 1700MPa and more than, and all use 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.There is the technological process of production longer, relatively costly deficiency.Some impact resistant or load bearing component are all adopted Improve impact resistant and bearing capacity with multiple part combination components, and cause being greatly improved the cost of raw material and being processed into This.
Along with the development of steel and iron industry, medium thin slab continuous casting and rolling technique has obtained tremendous development, uses medium thin slab even Casting continuous rolling process can produce ＞ 2.0～10 mm specification steel plate and steel band with Direct Rolling, and some can only use cold rolling high-strength originally The Thin Specs part of steel or the structure for increase intensity employing multiple parts composition the most progressively use casting and rolling process directly to roll Ultrahigh-strength steel plates processed is replaced.Yield strength (the R such as Patent exploitation that China Patent Publication No. is CN 102965573AeL) >=700MPa, tensile strength (RmThe engineering structure high strength steel of) >=750MPa, its component percentages is: 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 for Fe and is inevitably mingled with；Its production stage, for smelting and being casting continuously to form base, enters Row soaking, control soaking temperature is at 1200～1300 DEG C, and soaking time is 20～60min；Roll, and control start rolling temperature Being not less than 1200 DEG C, finishing temperature is at 870～930 DEG C；Carry out section cooling, in rate of cooling for being not less than under 20 DEG C/s cooling To coiling temperature；Batch, and control coiling temperature at 580～650 DEG C.China Patent Publication No. is CN 103658178A A kind of short route of patented invention method of producing high-strength thin strip steel, the strip steel yield strength (R that inventedeL) >= 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 For Fe and inevitable impurity, it is cast into 1.0～2.0mm thick Cast Strips, casting rate 60～150m/min after smelting, rolls System, control finishing temperature 850～1000 DEG C；Use atomization cooling, rate of cooling 50～100 DEG C/s, batch, control to batch Temperature is 520～660 DEG C.The tensile strength of above-mentioned two documents is the lowest, it is impossible to meet high-end body of a motor car to more than 1700MPa The demand of superhigh intensity.
Summary of the invention
The invention reside in the intensity rank overcoming prior art to exist low, it is impossible to meet user to superhigh intensity part demand Deficiency, it is provided that a kind of both can meet the Automobile Design requirement to superhigh intensity mechanical property, complicated change can have been smoothly completed again Without resilience after shape, and deformation, tensile strength >=1700MPa hot forming steel that the dimensional accuracy of part is high and production method.
Realize the measure of above-mentioned purpose:
With the tensile strength of medium thin slab Direct Rolling >=1700MPa hot forming steel, its component and weight percent content be: 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 its In the two or more mixing with arbitrary proportion, B:0.003～0.004%, Mo:0.20～0.25%, Ni:0.06～0.10%, N≤ 0.005%, remaining for Fe and inevitable impurity；Metallographic structure after quenching is full lath martensite；Mechanical property: surrender is strong Degree >=1150 MPa, tensile strength >=1700MPa, percentage elongation A80mm≥5%。
Produce the method with the tensile strength >=1700MPa hot forming steel of medium thin slab Direct Rolling, it is characterised in that: its Step:
1) desulfurizing iron, and control S≤0.002%, after skimming, molten iron exposed surface is not less than 96%；
2) conventional electric furnace or converter smelting, and conventional refinery；
3) carrying out continuous casting, in control, bag molten steel overheat is at 15～30 DEG C, and slab thickness is 61～150mm, and casting speed is 2.8 ～5.5 m/min；
4) carry out the de-scaling before strand enters soaking pit to process, and control the pressure of de-scaling water at 300～400 bar；
5) strand is carried out conventional soaking, control soaking pit interior in weak oxide atmosphere, even if remaining oxygen is 0.5～5.0% in stove；
6) entering to heat to strand, and control strand charging temperature at 780～1000 DEG C, tapping temperature is 1150～1180 ℃；
7) carry out the high-pressure water descaling before feed mill, and control de-scaling water pressure 280～420bar；
8) rolling, and control the first percentage pass reduction and be: 40～50%, the second percentage pass reduction is: 40～50%, extreme trace time pressure Rate is: 10～16%；Controlled rolling speed is at 3～8 m/s；And setting-out de-scaling in carrying out between the first passage and second time, De-scaling water pressure is 200～280bar；Control finishing temperature at 840～880 DEG C；
9) cooling down, the type of cooling is that the mode of section cooling or Water-Curta in Cooling or encryption cooling is cooled to coiling temperature；
10) batch, and to control coiling temperature be 615 ~ 645 DEG C；
11) carrying out the austenitizing after uncoiling blanking, control austenitizing temperature is at 930～980 DEG C, and is incubated 6～15 min；
12) mould punching shapes, and pressurize 6～9 s in mould；
13) quench, control quenching rate of cooling at 50～100 DEG C/s；After naturally cool to room temperature.
It is: the operation of rolling of described medium thin slab is that 6F produces line or 1R+6F produces line or 2R+ at rolling mill layout 6F produces line or 7F produces line or 3R+4F produces line or 2R+5F produces line or 1R+5F produces line and carries out.
Each element and the effect of main technique and mechanism in the present invention
C: carbon is strong solution strengthening element, and the acquisition to superhigh intensity plays a decisive role, the carbon content tissue shape to final products State and performance have considerable influence, but content is the highest, are easily formed substantial amounts of pearlite or bayesian in the cooling procedure after finish rolling Body, martensite, its content is the highest, and intensity is the highest, thus causes plasticity to reduce, the blanking difficulty before forming.So protecting On the premise of card heat treatment reinforcement, carbon content is difficult to too high.Therefore its content is limited to 0.26～0.30% scope.
Si: silicon has stronger solid solution strengthening effect, can improve the intensity of steel, and meanwhile, silicon can improve the quenching degree of steel, has and subtracts Few austenite effect of change in volume when martensite transfor mation, thus effectively control the generation of hardening flaw；When lonneal Carbon diffusion can be hindered, delay martensite to decompose and the speed of carbide agglomeration, make steel hardness when tempering decline relatively slow, Significantly improve steel belt roof bolt stability and intensity.So, its content is limited to 0.31～0.35% scope.
Mn: manganese plays solution strengthening effect, can remove the FeO in steel simultaneously, significantly improve the quality of steel.Can also be with sulfide Generating dystectic MnS, when hot-working, MnS has enough plasticity, makes steel not produce hot-short phenomenon, alleviates harmful work of sulfur With, improve the hot-working character of steel.Manganese can reduce phase driving force, makes " C " curve move to right, and improves the quenching degree of steel, expands γ Phase region, separately it can reduce the Ms point of steel, therefore can ensure to obtain martensite under suitable rate of cooling.So, its content is limited It is scheduled on 1.3～1.5% scope.
Cr: chromium can reduce phase driving force, and when also reducing phase transformation, the forming core of carbide is grown up, so improving the through hardening of steel Property.It addition, chromium can improve steel belt roof bolt stability.So, its content is limited to 0.31～0.35% scope.
B: boron is strongly to improve quenching degree element, and the boron element adding trace in steel can significantly improve the quenching degree of steel.But It is that its content is less than 0.003%, or higher than 0.004%, the effect to improving quenching degree is inconspicuous.So, for considering to produce Actual and quenching degree effect, is limited to 0.003～0.004% scope by its content.
Als, it plays deoxidation in steel, should ensure that there is a certain amount of dissolved aluminum in steel, otherwise can not play its effect, But too much aluminum also can make to produce aluminum system in steel to be mingled with, and is unfavorable for smelting and the casting of steel.Steel adds appropriate aluminum simultaneously Nitrogen in steel, the oxygen atom adverse effect to performance can be eliminated.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 hot continuous rolling heating process subsequently the most partially Gather crystal boundary, make the fragility of steel significantly increase.It is simultaneously based on cost consideration and does not affect the performance of steel, its content is controlled Less than 0.008%.
S: sulfur is very harmful element.Sulfur in steel often exists with the oxide morphology of manganese, this sulphide inculsion meeting The toughness of deterioration steel, and cause the anisotropy of performance, therefore, need to sulfur content in steel be controlled the lowest more good.Based on to system Cause this consideration, sulfur content in steel is controlled below 0.005%.
N: nitrogen can be combined formation titanium nitride in the steel add titanium with titanium, and this second phase at high temperature separated out is conducive to strong Change matrix, and improve the welding performance of steel plate.But nitrogen content is higher than 0.005%, and nitrogen is higher with the solubility product of titanium, when high temperature Steel will form the titanium nitride that granule is thick, the plasticity of serious infringement steel and toughness；It addition, higher nitrogen content can make stable Micro alloying element content needed for nitrogen element increases, thus increases cost.Therefore its content is controlled below 0.005%.
Ti: titanium is that strong C, N compound forms element, and the purpose adding Ti in steel is the N element in fixing steel, but excess Ti can be combined with C thus reduce hardness and the intensity of martensite after test steel quenches.It addition, the quenching degree to steel that adds of titanium has Certain contribution.So, its content is limited to 0.031～0.035% scope.
Nb, V: niobium and vanadium are also that strong C, N compound forms element, can play the effect of fining austenite grains, add in steel A small amount of niobium or vanadium just can form the carbon of a certain amount of niobium, nitride, thus hinder Austenite Grain Growth, and therefore, it is quenched Martensite lath size after fire is less, is greatly improved the intensity of steel.Therefore its content is all controlled 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, and the low temperature that can improve steel in addition steel is moulded Property and toughness.Therefore its content is controlled between 0.20～0.25%.
Ni: nickel addition steel can improve the intensity of steel and do not significantly reduce its toughness.Can improve simultaneously steel processability and Solderability.It addition, nickel can improve the resistance to corrosion of steel, can not only be acidproof, and can alkali resistant and the corrosion of air.So will Its content is limited to 0.06～0.10%.
Why the present invention takes three de-scalings in whole production process, is due to by controlling de-scaling passage with suitable De-scaling water pressure, the iron scale of belt steel surface can be removed as far as possible, thus ensure that strip steel has good surface matter Amount.Control additionally by one, two roads and end percentage pass reduction, even tissue and the stable performance of strip steel can be realized.
Compared with prior art, its intensity is high, and manufacturing process is short, and product surface quality is good for the present invention, and thickness and precision is high, energy Enough reach the prescription of cold-rolled products, significantly save energy resource consumption；It addition, with existing medium thin slab Direct Rolling product phase Ratio, its intensity is significantly larger than existing product, is significant for automobile lightweight.
Accompanying drawing explanation
Fig. 1 is product metallographic structure figure of the present invention.
Detailed description of the invention
Below the present invention is described in detail:
Table 1 is the chemical composition value list of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters value list of various embodiments of the present invention and comparative example；
Table 3 is the performance detection case list of various embodiments of the present invention and comparative example.
Various embodiments of the present invention are all produced by following technique:
1) desulfurizing iron, and control S≤0.002%, after skimming, molten iron exposed surface is not less than 96%；
2) conventional electric furnace or converter smelting, and conventional refinery；
3) carrying out continuous casting, in control, bag molten steel overheat is at 15～30 DEG C, and slab thickness is 61～150mm, and casting speed is 2.8 ～5.5 m/min；
4) carry out the de-scaling before strand enters soaking pit to process, and control the pressure of de-scaling water at 300～400 bar；
5) strand is carried out conventional soaking, control soaking pit interior in weak oxide atmosphere, even if remaining oxygen is 0.5～5.0% in stove；
6) entering to heat to strand, and control strand charging temperature at 780～1000 DEG C, tapping temperature is 1150～1180 ℃；
7) carry out the high-pressure water descaling before feed mill, and control de-scaling water pressure 280～420bar；
8) rolling, and control the first percentage pass reduction and be: 40～50%, the second percentage pass reduction is: 40～50%, extreme trace time pressure Rate is: 10～16%；Controlled rolling speed is at 3～8 m/s；And setting-out de-scaling in carrying out between the first passage and second time, De-scaling water pressure is 200～280bar；Control finishing temperature at 840～880 DEG C；
9) cooling down, the type of cooling is that the mode of section cooling or Water-Curta in Cooling or encryption cooling is cooled to coiling temperature；
10) batch, and to control coiling temperature be 615 ~ 645 DEG C；
11) carrying out the austenitizing after uncoiling blanking, control austenitizing temperature is at 930～980 DEG C, and is incubated 6～15 min；
12) mould punching shapes, and pressurize 6～9 s in mould；
13) quench, control quenching rate of cooling at 50～100 DEG C/s；After naturally cool to room temperature.
The chemical composition (wt.%) of table 1 various embodiments of the present invention and comparative example
The main technologic parameters value list of table 2 various embodiments of the present invention and comparative example
Table 3 various embodiments of the present invention and comparative example mechanical property situation list
From table 3 it can be seen that the application by shorter technological process be successfully realized the intensity of invention steel reach 1700MPa with On, for advancing the development of automotive light weight technology to be significant.
This detailed description of the invention is only and most preferably enumerates, the not restricted enforcement to technical solution of the present invention.

Claims (3)

1., with the tensile strength >=1700MPa hot forming steel of medium thin slab Direct Rolling, its component and weight percent content be: 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 its In the two or more mixing with arbitrary proportion, B:0.003～0.004%, Mo:0.20～0.25%, Ni:0.06～0.10%, N≤ 0.005%, remaining for Fe and inevitable impurity；Metallographic structure after quenching is full lath martensite；Mechanical property: surrender is strong Degree >=1150 MPa, tensile strength >=1700MPa, percentage elongation A80mm≥5%。
2. produce the method with the tensile strength >=1700MPa hot forming steel of medium thin slab Direct Rolling described in claim 1, It is characterized in that: its step:
1) desulfurizing iron, and control S≤0.002%, after skimming, molten iron exposed surface is not less than 96%；
2) conventional electric furnace or converter smelting, and conventional refinery；
3) carrying out continuous casting, in control, bag molten steel overheat is at 15～30 DEG C, and slab thickness is 61～150mm, and casting speed is 2.8 ～5.5 m/min；
4) carry out the de-scaling before strand enters soaking pit to process, and control the pressure of de-scaling water at 300～400 bar；
5) strand is carried out conventional soaking, control soaking pit interior in weak oxide atmosphere, even if remaining oxygen is 0.5～5.0% in stove；
6) heating strand, and control strand charging temperature at 780～1000 DEG C, tapping temperature is 1150～1180 DEG C；
7) carry out the high-pressure water descaling before feed mill, and control de-scaling water pressure 280～420bar；
8) rolling, and control the first percentage pass reduction and be: 40～50%, the second percentage pass reduction is: 40～50%, extreme trace time pressure Rate is: 10～16%；Controlled rolling speed is at 3～8 m/s；And setting-out de-scaling in carrying out between the first passage and second time, De-scaling water pressure is 200～280bar；Control finishing temperature at 840～880 DEG C；
9) cooling down, the type of cooling is that the mode of section cooling or Water-Curta in Cooling or encryption cooling is cooled to coiling temperature；
10) batch, and to control coiling temperature be 615～645 DEG C；
11) carrying out the austenitizing after uncoiling blanking, control austenitizing temperature is at 930～980 DEG C, and is incubated 6～15 min；
12) mould punching shapes, and pressurize 6～9 s in mould；
13) quench, control quenching rate of cooling at 50～100 DEG C/s；After naturally cool to room temperature.
3. the side produced with the tensile strength >=1700MPa hot forming steel of medium thin slab Direct Rolling as claimed in claim 2 Method, it is characterised in that: the operation of rolling of described medium thin slab is that 6F produces line or 1R+6F produces line or 2R+6F at rolling mill layout Produce line or 7F produces line or 3R+4F produces line or 2R+5F produces line or 1R+5F produces line and carries out.
CN201610713646.3A 2016-08-24 2016-08-24 With the tensile strength >=1700MPa hot formings steel and production method of medium thin slab Direct Rolling Active CN106191678B (en)

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Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
CN108754319A (en) * 2018-06-08 2018-11-06 武汉钢铁有限公司 Using the tensile strength >=1800MPa grades of hot forming steel and method of the production of ESP producing lines
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
CN109023115A (en) * 2018-09-29 2018-12-18 武汉钢铁有限公司 A kind of hot rolling template pulling-on piece steel and its manufacturing method
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
CN110499460A (en) * 2019-08-22 2019-11-26 唐山钢铁集团有限责任公司 A kind of heat stamping and shaping cold-rolled strip and its production method
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
WO2023087352A1 (en) * 2021-11-19 2023-05-25 鞍钢股份有限公司 High-plasticity thermoformed steel having oxidation resistance for automobile, and thermoforming 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

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004204286A (en) * 2002-12-25 2004-07-22 Nippon Steel Corp High impact resistant square steel pipe, and production method therefor
CN103205627A (en) * 2013-03-28 2013-07-17 宝山钢铁股份有限公司 Low-alloy high-performance wear-resistant steel plate and manufacturing method thereof
CN103320702A (en) * 2013-06-26 2013-09-25 武汉钢铁(集团)公司 Thermoforming steel with tensile strength of 1,700MPa level and production method thereof
WO2015147216A1 (en) * 2014-03-26 2015-10-01 新日鐵住金株式会社 High-strength hot-formed steel sheet member

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004204286A (en) * 2002-12-25 2004-07-22 Nippon Steel Corp High impact resistant square steel pipe, and production method therefor
CN103205627A (en) * 2013-03-28 2013-07-17 宝山钢铁股份有限公司 Low-alloy high-performance wear-resistant steel plate and manufacturing method thereof
CN103320702A (en) * 2013-06-26 2013-09-25 武汉钢铁(集团)公司 Thermoforming steel with tensile strength of 1,700MPa level and production method thereof
WO2015147216A1 (en) * 2014-03-26 2015-10-01 新日鐵住金株式会社 High-strength hot-formed steel sheet member

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108754319A (en) * 2018-06-08 2018-11-06 武汉钢铁有限公司 Using the tensile strength >=1800MPa grades of hot forming steel and method of the production of ESP producing lines
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
CN109023115A (en) * 2018-09-29 2018-12-18 武汉钢铁有限公司 A kind of hot rolling template pulling-on piece steel and its manufacturing method
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
CN110499460A (en) * 2019-08-22 2019-11-26 唐山钢铁集团有限责任公司 A kind of heat stamping and shaping cold-rolled strip 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
WO2023087352A1 (en) * 2021-11-19 2023-05-25 鞍钢股份有限公司 High-plasticity thermoformed steel having oxidation resistance for automobile, and thermoforming 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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