CN108754319A - Using the tensile strength >=1800MPa grades of hot forming steel and method of the production of ESP producing lines - Google Patents
Using the tensile strength >=1800MPa grades of hot forming steel and method of the production of ESP producing lines Download PDFInfo
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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
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- 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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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Abstract
采用ESP产线生产的抗拉强度≥1800MPa级热成形钢，其组分及wt%：C：0.28～0.40%，Si：0.15～0.40%，Mn：1.40～1.60%，P≤0.01%，S≤0.01%，Als：0.015～0.050%，Cr≤0.80%，N≤0.005%，B：0.002～0.005%，Mo≤0.50%，Nb+Ti：0.025～0.090%；生产方法：冶炼并连铸成板坯；粗轧；均热处理；经常规高压除鳞后精轧；层流冷却；加热；经酸洗后冲压成型。本发明通过复合添加Nb、Ti，并控制组分中的Cr、B、Mo等元素，以及采用ESP短流程工艺生产抗拉强度为1800MPa级热冲压成形用钢，不仅能保证其力学性能，且能减少生产过程中板卷反复加热、开卷等工序，还能取消冷轧和退火热处理工序，降低生产成本。
The tensile strength ≥1800MPa grade hot-formed steel produced by the ESP production line, its composition and wt%: C: 0.28-0.40%, Si: 0.15-0.40%, Mn: 1.40-1.60%, P≤0.01%, S ≤0.01%, Als: 0.015～0.050%, Cr≤0.80%, N≤0.005%, B: 0.002～0.005%, Mo≤0.50%, Nb+Ti: 0.025～0.090%; production method: smelting and continuous casting Slab; rough rolling; soaking treatment; finish rolling after conventional high-pressure descaling; laminar cooling; heating; stamping after pickling. The present invention adds Nb and Ti in combination, controls Cr, B, Mo and other elements in the components, and adopts the ESP short-flow process to produce steel for hot stamping forming with a tensile strength of 1800 MPa, which can not only ensure its mechanical properties, but also It can reduce the repeated heating and uncoiling of coils in the production process, and can also cancel the cold rolling and annealing heat treatment processes to reduce production costs.
Description
Technical field
The present invention relates to a kind of automobile component steel and production method, definitely belong to the tension produced using ESP producing lines
Intensity >=1800MPa grades of hot forming steel and method.
Background technology
With increasingly sharpening for environmental problem, automotive light weight technology has become the key problem of current automobile manufacturing field.It adopts
Vehicle mass reduction design is carried out with high-strength steel, is the preferably way for meeting automotive light weight technology demand and improving crashworthiness
Diameter.However currently, for producing 1000MPa grades or more of super-high strength steel, iron and steel enterprise must use specialized super
High-strength steel equipment is manufactured；Meanwhile there are part punchings to spring back the skills such as difficult to control, poor dimensional precision for Automobile Enterprises manufacture
Art problem.
The birth of hot press-formed technology has well solved above-mentioned problem.Hot press-formed technology is that will have high through hardening
Property steel plate blank be heated to austenitizing temperature, and keep the temperature the once time and be allowed to uniform austenitic；Then use conveying device
Plate under the condition of high temperature, which is sent into, to be had stamping in the mold of cooling system, while being protected to part by mold
Pressure quenching, it is final to obtain superhigh intensity punching parts.The technology can be carried out hot press-formed using iron and steel enterprise's existing weaponry and equipment
Sheet metal raw material produces, and the superelevation at 1500MPa grades of intensity or more is then fabricated by hot press-formed specialized apparatus
Strong auto parts and components.It has many advantages, such as that organization of production is at low cost, part forming precision is high, part forming performance is good, rapidly at
For the hot technology of auto parts and components manufacture field.
Currently, the 1800MPa grades of hot press-formed production process routes with sheet metal raw material are usually both at home and abroad：Molten steel smelting
Refining → continuous casting → cooling → heating strand → hot continuous rolling → cooling → batches → and uncoiling → pickling → cold rolling → batches → uncoiling →
Heating → annealing → cooling → is batched.In above-mentioned production technology, raw material is needed in processes such as hot rolling, cold rolling, annealings
It undergoes uncoiling repeatedly and batches, heat and cooling treatment, the production cost of repetition process necessarily lead to the final thin steel produced
Panel products are at high price.
Such as the document that Chinese Patent Application No. is CN 201310258918.1, a kind of tensile strength 1700MPa is developed
Grade hot forming steel, component and weight percent content are：C：0.27 ~ 0.50%, Si：0.28 ~ 0.50%, Mn：1.20 ~ 1.60%,
Cr：0.32 ~ 0.60%, Ti：0.025 ~ 0.055%, B：0.002 ~ 0.005%, Als：0.010 ~ 0.06%, P≤0.012%, Nb：
0.010 ~ 0.035% or Mo：0.30 ~ 0.45% or both mixing be no more than 0.50%, S≤0.008%, N≤0.005%, O≤
0.005%；Production method:Desulfurizing iron, converter smelting and strand；By heating strand, roughing, finish rolling, section cooling, batch, acid
It washes and heating under cold rolling, annealing, smooth, finishing and shearing, protective atmosphere, molding, quenching, lonneal, for use.The document is
1700MPa grades of hot forming steel productions, production technology complexity, high energy consumption are carried out in conjunction with traditional mode of production flow.
Chinese Patent Application No. is the document of CN 201510790931.0, discloses a kind of tensile strength 1500MPa grades of heat
Stamping to use sheet metal and its CSP production methods, component and weight percent content are：C：0.20~0.25%, Si：
0.25~0.40%, Mn：1.00~1.30%, P≤0.025%, S≤0.01%, Als：0.015~0.035%, N≤
0.005%, B≤0.005%, Nb：0.020~0.060%, Ti：0.010~0.040%, remaining for iron and inevitably it is micro-
Secondary element.Production process route includes：Smelting molten steel, vertical bending type CSP sheet blank continuous castings, de-scaling, the soaking of roller-bottom type continuous tunnel furnace,
Six rack hot continuous rollings of TMCP, section cooling, batch, uncoiling pickling, it is smooth, batch.The method of the present invention eliminate plate cold rolling and
Annealing heat-treats process replaces traditional cold rolled sheet product with hot rolled sheet product, reduces comprehensive production cost.Also China is special
Profit application No. is the document of CN 201610713629.X, disclose a kind of tensile strength with sheet billet Direct Rolling >=
The thin hot forming steel of 1700MPa and production method, 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%, Ti：0.031~0.035% or
Nb：0.031~0.035% or V：0.031~0.035% or in which 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%.Production stage：Desulfurizing iron；Electric furnace or converter smelting
Refining and refining；Continuous casting；Enter the processing of the de-scaling before soaking pit；Soaking；Heating；High-pressure water descaling before feed mill；Rolling；It is cold
But；It batches；Austenitizing；Mould punching shapes；Quenching.Two documents using CSP productive technology of short flow carried out heat at
The production of shape steel, opposite traditional mode of production flow have the advantage that energy consumption is few, production cost is low.However, thickness can only be produced
The sheet metal in 1.2mm or more is spent, for needing the manufacture demand of more light-weighted automobile component, then cannot be satisfied.This Shen
Thickness please can not only be produced in the steel plate of 1.2mm or more, can more produce thickness 0.7 to the sheet metal no more than 1.2mm, and be
Quality stability.Deficiency of the prior art in terms of product thickness specification can effectively be supplemented；In addition, using ESP sheet blank continuous castings
Continuous rolling technology on the basis of existing short process production technology, make full use of continuous casting billet high temperature energy, in time to high temperature strand into
Row production rolling, realizes that lower roll-force generates larger drafts, can be further reduced production consumption, reduce material production
Cost.
Chinese Patent Application No. is the document of CN 201610766506.2, is disclosed a kind of based on ESP sheet blank continuous castings company
The method of flow production DP600 steel is rolled, raw material include by mass percentage：The C of the .10% of 0 .045~0,0 .20~0
.6% the Mn of Si, the .0% of 1 .2~2, the Cr of the .0% of 0 .1~1 ,≤0 .05% Nb ,≤0 .05% S ,≤0
.015% P, remaining is ferro element；Raw material are carried out to converter smelting successively and LF stoves are smelted；It will smelt to be formed from LF stoves
Molten steel by ESP producing lines generate different-thickness hot-strip；Wherein, in ESP producing lines, the temperature of finish rolling outlet is not less than
820℃；Determine ratio needed for the ferrite and martensite in hot-strip successively by secondary cooling hot-strip.The document is adopted
The tensile strength 600MPa two-way steels produced with ESP, are the existing maximum intensity grade product produced based on ESP producing lines, tension
Intensity is relatively low cannot to meet the needs of high-end body of a motor car is to 1800MPa or more superhigh intensitys.
Invention content
One kind is provided the invention reside in complex process of the existing technology, high energy consumption, the deficiency of low production efficiency is overcome
Under the premise of proof strength rank, production link can be reduced, reduces energy consumption, shortens being produced using ESP producing lines for production cycle
Tensile strength >=1800MPa grades of hot forming steel and method.
Realize the measure of above-mentioned purpose：
Tensile strength >=1800MPa grades of hot forming the steel produced using ESP producing lines, component and weight percent content are：C：
0.28~0.40%, Si：0.15~0.40%, Mn：1.40~1.60%, P≤0.01%, S≤0.01%, Als：0.015~
0.050%, Cr≤0. 80%, N≤0.005%, B：0.002~0.005%, Mo≤0.50%, Nb+Ti：0.025~0.090%,
Remaining is Fe and inevitable impurity；Nb or Ti are not zero.
Preferably：The weight percent content of Nb+Ti is 0.025~0.090%；Two elements are appointed in control range
Meaning addition.
Using the method for tensile strength >=1800MPa grades of hot forming steel of ESP producing lines production, step：
1）It smelts and is casting continuously to form slab；
2）Roughing is carried out, and controls single pass reduction ratio and is not less than 60%；
3）All heat-treated is carried out, control soaking temperature is at 1200~1250 DEG C；
4）Finish rolling is carried out after conventional high pressure descaling, finishing temperature is at 815~865 DEG C；
5）Section cooling is carried out to 575~650 DEG C；
6）It is heated, heating temperature keeps the temperature 3 ~ 10min at this temperature at 875~950 DEG C；
7）The punch forming after pickling, the quenching velocity controlled therebetween in mold are not less than 20 DEG C/S, are cooled to 180 DEG C or less.
It is：When punch forming need not be carried out in time, batched after section cooling, after naturally cool to again
Room temperature；When to punch forming, according still further to step 6）And 7）It carries out.
Preferably：Heating temperature is at 900~930 DEG C.
The effect of each element and main technique and mechanism in the present invention：
C ：Carbon is basic element and most economical, effective intensified element in steel.Carbon content design it is relatively low, drop stamping at
Intensity declines after shape；But carbon content is excessively high, reduces the plasticity of steel, and unfavorable to weldability.Therefore from economy and comprehensive
It can consider, carbon percentage composition control range is 0.28~0.40% in the present invention.
Si ：Silicon is solution strengthening element, is solid-solubilized in ferrite, is conducive to improve base material and hot press-formed rear material
Intensity.With the increase of silicone content, the intensity of steel significantly improves, and plasticity is decreased obviously, and welding performance declines.Therefore, silicon contains
It is 0.15~0.40% to measure control range.
Mn：Manganese has solution strengthening effect, is to improve one of strength of materials important element；But manganese content addition is excessively high to be easy
It is unfavorable to weldability.Therefore the manganese upper limit is set as 1.60%, it is 1.40~1.60% that the present invention, which adds manganese content,.
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, the brittleness of steel is made to significantly increase.Based on cost consideration and the performance of steel is not influenced simultaneously, its content is controlled 0
.01% following.
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 in 0 .01% or less.
Als：Aluminium adds for deoxidation, when Als contents are less than 0.015%, cannot play its effect；It is another
Aspect, since the aluminium of addition volume is easy to form aluminium oxide agglomerate, aluminium content control range is 0.015~0.050%.
Cr:Chromium is the important element for the quenching degree for improving steel, is dissolved into the stability for improving austenite in austenite, has
The quenching degree for helping improve steel obtains martensitic structure；Meanwhile chromium can improve steel belt roof bolt stability.And chromium content is more than 0.
It is more than needed to improve the effect of quenching degree for it after 80%.Therefore chromium content controls below 0. 80% in the present invention.
N:Nitrogen can improve the intensity of steel；However, nitrogen and niobium, titanium binding force are strong, particle will be formed in steel at high temperature
Coarse niobium nitride, titanium nitride, the serious plasticity and toughness for damaging steel；In addition, higher nitrogen content can make to stablize nitrogen institute
The micro alloying element content needed increases, to increase cost.Therefore the content of nitrogen should be reduced as possible, nitrogen control in the present invention
System is in 0 .005% or less.
B:Boron is strong raising quenching degree element, and denier, which need only be added, just apparent influence, and quenching degree can be at double
Raising, to save the metallic element of other costlinesses.Micro boron element is added in steel can significantly improve the quenching degree of steel.But
Boron content is less than 0 .002%, or is higher than 0 .005%, to improving the effect unobvious of quenching degree.Therefore, in the present invention
Boron content is controlled in the .005% ranges of 0 .002~0.
Mo：Molybdenum is the element for improving quenching degree, is dissolved into the stability for improving austenite in austenite, helps to improve steel
Quenching degree to obtain martensitic structure；And molybdenum content is more than that the effect of its quenching degree is more than needed after 0.5%, and cost is higher.Therefore originally
Molybdenum content control is below 0.5% in invention.
Nb+Ti：：Niobium, titanium are strong C, N compound formation elements.A small amount of niobium is added in steel can form a certain amount of niobium
Carbon, nitride it is quenched strong to greatly improve steel hot forming to hinder Austenite Grain Growth, fining austenite grains
Degree and toughness；The purpose that a small amount of titanium is added in steel is the N element in fixed steel, and B is avoided to be combined with N.But excessive niobium, titanium can be with
C is combined, and forms coarse carbonitride, to reduce the hardness and strength of martensite after experiment steel quenches.Therefore, by its total content
Control is in 0.025~0.090% range.
Controlling for the present invention is not less than 60% with roughing single pass reduction ratio, is since the technique can be effectively by thickness
It is 8~20mm intermediate slabs that 80~120mm continuous-cast blanks are rolled into thickness through roughing mills, and required thickness is provided for follow-up finish rolling
Middle thick stock raw material；In addition, larger roughing reduction ratio can make coarse continuous casting billet austenite structure be changed into flat Ovshinsky
Body tissue is converted into tiny austenite structure, fining austenite grains size using subsequent heat recrystallization.
The present invention why by heating and temperature control at 875~950 DEG C, and at this temperature keep the temperature 3 ~ 10min, be due to
It is 875 DEG C that all structural transformations of high-strength steel that the present invention is developed, which are austenite finishing temperature Ac3,.Realize it is hot press-formed before
Material is 100% austenite structure, and heating temperature should be not less than 875 DEG C；But excessively high temperature, it is thick to be easy to cause austenite grain
Greatly, also result in the plate low strength, yielding after heating, be not easy to it is hot press-formed during plate transmission with it is accurate
Positioning.Soaking time is less than 3min, cannot achieve plate complete austenitizing；But soaking time is long, is easy to cause austenite
Coarse grains, strength reduction.Therefore, by heating and temperature control at 875~950 DEG C, and 3 ~ 10min models are kept the temperature at this temperature
It encloses.
Why the present invention, which controls the quenching velocity in mold, is not less than 20 DEG C/S, is the thin steel developed by the present invention
Plate is changed into the critical cooling rate of 100% martensite during quenching treatment, otherwise cannot fully quench strong needed for reaching
Degree.
Compared with prior art, the present invention it is by compound addition Nb, Ti, and the elements such as Cr, B, Mo in component are controlled,
And use ESP abbreviated systems production tensile strength for 1800MPa grades of hot press-formed steel, it not only can guarantee its power
Learn performance, and can reduce coiled sheet in production process heat repeatedly, uncoiling, the processes such as curling, moreover it is possible to cancel cold rolling and annealing it is hot at
Science and engineering sequence reduces production cost.
Description of the drawings
Fig. 1 is sheet metal typical case metallographic structure of the present invention：Ferrite+pearlite；
Fig. 2 is typical metallographic structure after sheet metal quenching of the present invention：Martensite.
Specific implementation mode
The present invention is described in detail below：
Table 1 is the chemical composition list of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example；
Table 3 is the performance test results list of various embodiments of the present invention and comparative example.
Various embodiments of the present invention follow the steps below production：
1）It smelts and is casting continuously to form sheet billet；
2）Roughing is carried out, and controls single pass reduction ratio and is not less than 60%；
3）All heat-treated is carried out, control soaking temperature is at 1200~1250 DEG C；
4）Finish rolling is carried out after conventional high pressure descaling, and controls its finishing temperature at 815~865 DEG C；
5）Section cooling is carried out, 575~650 DEG C are cooled in the case where cooling velocity is 10~20 DEG C/S；
6）It is heated, heating temperature keeps the temperature 3 ~ 10min at this temperature at 875~950 DEG C；
7）The punch forming after pickling, the quenching velocity controlled therebetween in mold are not less than 20 DEG C/S, are cooled to 180 DEG C or less.
The chemical composition of 1 each case study on implementation of the present invention of table（wt.%）
The main technologic parameters comparative example of 2 various embodiments of the present invention of table and comparative example
The performance test results of 3 various embodiments of the present invention of table and comparative example
From table 3 it can be seen that by ESP short route rolling mill practices, realize invention steel tensile strength reached 1800MPa with
On, while its intensity is significantly larger than existing ESP producing lines product strength, has important meaning for promoting automotive light weight technology level to be promoted
Justice.
Present embodiment is only the best example, not to the restricted implementation of technical solution of the present invention.
Claims (5)
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| CN109433825A (en) * | 2018-11-13 | 2019-03-08 | 燕山大学 | The method and high-strength steel sheet of a kind of short route production high-strength steel sheet and its application |
| CN109706377A (en) * | 2019-03-01 | 2019-05-03 | 本钢板材股份有限公司 | A thick gauge PHS1500 steel suitable for hot forming and its production process |
| 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 |
| CN111748736A (en) * | 2020-06-24 | 2020-10-09 | 武汉钢铁有限公司 | A kind of 1800MPa grade low hydrogen-induced delayed cracking sensitivity hot forming steel and its production method |
| CN112210724A (en) * | 2020-08-10 | 2021-01-12 | 唐山钢铁集团有限责任公司 | ESP (electronic stability program) production-based high-strength hot forming steel and method |
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| CN113913700A (en) * | 2021-10-26 | 2022-01-11 | 江苏沙钢集团有限公司 | 1700 MPa-grade hot forming steel and production method thereof |
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