CN103556048B - Production method for two-phase automobile steel plate with low yield-strength ratio and high strength - Google Patents
Production method for two-phase automobile steel plate with low yield-strength ratio and high strength Download PDFInfo
- Publication number
- CN103556048B CN103556048B CN201310507894.9A CN201310507894A CN103556048B CN 103556048 B CN103556048 B CN 103556048B CN 201310507894 A CN201310507894 A CN 201310507894A CN 103556048 B CN103556048 B CN 103556048B
- Authority
- CN
- China
- Prior art keywords
- steel
- annealing
- strength
- rolling
- steel plate
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a two-phase automobile steel plate with low yield-strength ratio and high strength and a production method of the two-phase automobile steel plate, belonging to the technical field of steel for automobiles. The two-phase automobile steel plate comprises the following chemical components: 0.1-0.40wt% of C, 3.0-8.0wt% of Mn, less than or equal to 0.020wt% of P and less than or equal to 0.02wt% of S; on the basis, the two-phase automobile steel plate can be additionally provided with one or more of the following elements: 0.1-3.0wt% of Ni, 0.2-3.0wt% of Cr, 0.1-0.8wt% of Mo, 0.3-2.3wt% of Si, 0.5-2.0wt% of Cu, 0.0005-0.005wt% of B, 0.02-0.10wt% of Nb, 0.002-0.25wt% of [N], 0.05-0.25wt% of Ti, 0.02-0.25wt% of V, 0.015-0.060wt% of Al, 0.002-0.005wt% of RE (Rare Earth) and 0.005-0.03wt% of Ca. The two-phase automobile steel plate has the advantages that the two-phase automobile steel plate with low yield strength, high tension strength and favorable elongation can be produced through annealing within short time; the performance indexes of the two-phase automobile steel plate are as follows: two-phase steel with the tension strength of 980MPa has the yield-strength ratio of not larger than 0.55 and the elongation of larger than 22%, and two-phase steel with the tension strength of 1180MPa has the yield-strength ratio of not larger than 0.55 and the elongation of larger than 17%.
Description
Technical field
The invention belongs to the production technical field of automobile steel coiled sheet, in particular, provide a kind of low yield strength ratio, high-strength vehicle dual phase sheet steel and production method, by continuous annealing production line produce a kind of have excellent formability, high-strength vehicle steel dual phase steel coiled sheet, its tensile strength is at more than 1GP, but the ratio of yield strength and tensile strength is between 0.45-0.65, there are enough unit elongation simultaneously, in raising auto sheet intensity with while realizing loss of weight object, also ensure easy plasticity during steel plate punched simultaneously.
Background technology
Along with the raising of automotive light weight technology and security requirement, require that the intensity of automobile structure steel improves constantly, to realize loss of weight with thinner steel plate under the condition meeting security prerequisite.In many automobile steels, dual phase steel (DP steel) has excellent mechanical property and processability, becomes desirable automotive sheet.In AHSS plate (AHSS) tandem product developed, high strength dual phase steel plate is one of kind that in automobile, application surface is the widest.In IISI's ultralight steel car body plan-advanced car concept (ULSAB-AVC) and U.S.'s young mobile Partnership Program (PNGV) project; the bicycle consumption of DP steel is 162.25kg, accounts for 74.3% of car load AHSS plate total mass; North America dual phase steel consumption in 2010 accounts for 45% of automobile steel total amount.DP600, DP780 and DP1000 steel developed at present both at home and abroad, is suitable for producing the structural part of automobile and safety component etc., as longeron, crossbeam and stiffener etc.But along with the significantly raising of steel plate tensile strength, usually also improve and unit elongation decline along with yield strength thereupon.Yield strength raises and causes material to be difficult to distortion, and the load that therefore power of stamping machine and mould bear all will significantly improve, and die life declines; In addition, yield strength raises and causes yield tensile ratio to increase, and the uniform elongation of material declines, and unit elongation declines and steel plate then can be caused to ftracture when punching press thus scrap.Therefore, improving the intensity of autobody sheet simultaneously, being ensured the easy plasticity of steel plate by low yield strength (namely maintaining low yield tensile ratio) and high unit elongation, is the mechanical performance index had of desirable automotive sheet.But high tensile strength and low yield strength, high-elongation are all runed counter under normal conditions, this just needs the composition to steel, tissue carries out ingehious design to achieve the above object.
Table 1 Nippon Steel formula dual phase steel product performance
| The trade mark | Yield strength/MPa | Yield strength/MPa | Unit elongation, % | Yield tensile ratio, % | Thickness, mm |
| DP590 | 318 | 610 | 31 | 52 | 1.6 |
| DP780 | 437 | 829 | 22 | 53 | 1.6 |
| DP980 (type A) | 630 | 1006 | 17 | 63 | 1.6 |
| DP980 (type B) | 716 | 1015 | 15 | 71 | 1.6 |
| DP1180 | 900 | 1199 | 11 | 75 | 1.6 |
Table 2 Japanese JFE company dual phase steel product performance
Table 3 meter tal fibre company dual phase steel product performance
Table 4 Pu Xiang company dual phase steel product performance
Table 1 to table 4 sets forth the performance index of external advanced iron and steel enterprise about each trade mark of DP product made from steel, this shows, for the dual phase steel (namely tensile strength is more than 980MPa) of DP980 rank, Nippon Steel Corp product requirement SMYS 630-716MPa, unit elongation 15-17%; Its SMYS of JFE Products 530MPa, unit elongation 12-14%; The SMYS of meter Ta Er Products at 662MPa, unit elongation 13%; Pu item Products SMYS is minimum is 490MPa, but unit elongation is only 6-7%.And for the dual phase steel (namely tensile strength is 1180MPa) of DP1180 rank, its yield strength of Nippon Steel Corp's product is 900MPa, and unit elongation is 11%; JFE Products yield strength is 710MPa, and unit elongation is only 7-11%.And the present invention at maintenance DP980 and DP1180 two rank dual phase steel high-tensiles simultaneously, significantly can reduce its yield strength and improve its unit elongation, the plasticity performance of this steel plate is significantly improved.This improvement in performance realizes mainly through new Composition Design and microstructure ultra-fining treatment.In existing industrialized dual phase steel, its Mn content is many in 1-3.5%(weight percentage) between; And the present invention adopts the Composition Design of 3.0-8.5%Mn content, and carbon content still between regular zone (0.1-0.4%).The design of this high Mn content makes the hardening capacity of steel significantly increase, even if even if cooling also can obtain martensitic stucture comparatively slowly after hot rolling reeling, when this martensitic stucture only needs a short period of time continuous annealing (being less than 10 minutes), just on martensite lath circle, austenite crystal and the annealing ferrite crystal grain of submicron-scale can be formed by forming core, the austenite crystal that part is tiny simultaneously can pass through interfacial diffusion fast enriching Mn and C, obtaining ultra-fine martensite and ferrite after causing cooling is main duplex structure, and containing the residual fine austenite crystal grain due to rich Mn and C, this super fine organization result in low yield strength (depending on ferritic phase), high tensile strength (depending on martensitic phase), and simultaneously because Mn content in steel is significantly higher than usual automobile steel, can further enrichment C and Mn at annealed rear section fine austenite crystal grain, the stability of these austenite crystals significantly increase cause cooling after still remain, and then in follow-up distortion, there is the plasticity that deformation induced trans-formation (TRIP effect) also improves steel plate while gaining in strength, describe in detail below.
Summary of the invention
The object of the present invention is to provide a kind of low yield strength ratio, high-strength vehicle dual phase sheet steel and production method, the dual phase steel automobile sheetsteel volume of low yield strength, high-tensile and good unit elongation can be manufactured by the continuous annealing production line of existing industrialization (in annealing time 10 minutes).
The present invention is based on the partition of reasonable chemical composition design and alloying element, key is in steel plate containing enough austenitizing stable element Mn, and the initial tissue before the continuous annealing of final two-phase region is martensitic stucture, the ferrito-martensite that can form submicron-scale is after annealing main tissue, simultaneously containing the fine austenite tissue of enrichment C and Mn, and then ensure that the low yield strength of this steel, high-tensile and good unit elongation.Although the constituent class of steel of the present invention and the high-strength high-ductility automobile steel of the third generation (CN101638749A patent) seemingly, but because annealing temperature is different, cause organizing completely different, the former matrix is ferrite and martensite, and the latter is ferrite and austenite, finally cause mechanical property also very not identical.Essential characteristic of the present invention is:
1, in the chemical composition of steel, mainly realized by 0.1-0.4wt%C and 3.00-8.00wt%Mn alloying.
2, before final two-phase region continuous annealing, its structural state is martensite, and can not have size more than the carbide of more than 50nm or cementite;
3, application claims by heat steel to suitable two-phase region temperature no longer than 10 minutes, that austenite forms austenite by ferrite to austenitic reverse transformation at ferrite grain boundaries place forming core on the one hand, the tiny transition carbide (size is less than 30nm) formed early stage on the other hand can complete solid solution thus the carbon of enrichment and manganese have been discharged, and causes reverse transformation process to be accelerated and the more rich manganese of austenite.Thus after continuous annealing in short-term, tiny, the austenite that is evenly distributed of size of more than 30% and the α phase matrix of ultra-fine size just can be obtained in the finished product tissue.
4, can be prepared the high-strength vehicle steel continuous annealing coiled sheet of two ranks by the technology of the present invention, yield strength corresponding to 980MPa tensile strength rank is no more than 540MPa, and namely yield tensile ratio is less than 0.55, and minimum unit elongation is 21%; Yield strength corresponding to 1180MPa tensile strength rank is no more than 650MPa, and yield tensile ratio is less than 0.55, and minimum unit elongation is 17%.This index is all better than the like product of existing external advanced Iron And Steel Company.
Can also be improved further by following technology or reach performance on the basis of the above: Ni, Mo, Cr, B etc. 1, can be added and improve further the hardening capacity of steel or the refinement such as low-temperature impact toughness, interpolation Nb, V, Ti original austenite grain, add Cu, V etc. and improve the intensity of steel by precipitation strength and add Si etc. and improve intensity and suppress Carbide Precipitation etc., add [N] and regulate austenitic stability etc.; 2, controlled the homogeneity of the heterogeneous microstructure of steel by the rolling technology such as hot rolling or warm-rolling, refining grain size, for finished heat treatment provides desirable weave construction.The present invention's high-performance cold rolled and hot-rolled high-strength auto sheet be applicable under existing industrial condition is produced, the production of high-performance section bar and Bar Wire Product etc.Be equally applicable to realize high performance product, as thermoformed parts etc. by heat treatment.
Key component scope of the present invention and processing parameter are described as follows:
The chemical composition of steel of the present invention is: C:0.1-0.40wt%, Mn:3.0-8.0wt%, P≤0.020wt%, S≤0.02wt%, and surplus is Fe and inevitable impurity.Separately can be descended a kind of or multiple element: Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:0.0005-0.005wt%, Nb:0.02-0.10wt%, [N] on this basis: 0.002-0.25wt%, Ti:0.05-0.25wt%, V:0.02-0.25wt%, Al:0.015-0.060wt%, RE(rare earth): 0.002-0.005wt%, Ca:0.005-0.03wt%.
The effect of each element of the present invention and proportioning are according to as follows:
C: as main gap solution strengthening element, the intensity of quenched martensite steel is played a decisive role.Adverse transformation austenite stability, quantity, size, shape and distribution can be regulated and controled by the partition of carbon; But carbon content is too high will worsen the performance of steel, and C content should control within the scope of 0.1-0.40wt%.
Mn:Mn has the effect of the hardening capacity improving steel.Mn expands austenitic area element, by the partition again of Mn in warm treating processes, realize the generation of adverse transformation austenite.In the present invention, Mn is the one of the chief elements controlling the stability of adverse transformation austenite, distribution and size thereof.For ensureing high-ductility and the intensity of steel, Mn content should control within the scope of 3.0-8.0%.
Ni:Ni is austenitizing stable element, effectively can reduce Ms point, and can improve material plasticity and low-temperature flexibility, but Ni price is high, its content should control below 2.0% simultaneously.
P: form microsegregation when solidification of molten steel, during heating temperatures, segregation, to crystal boundary, makes the fragility of steel enlarge markedly after austenite subsequently, thus Delayed hydride cracking susceptibility is raised.Therefore, P content should control below 0.020%.
S: inevitably impurity, forms MnS inclusion and can worsen the toughness of steel at grain boundary segregation, thus reduce the toughness plasticity of steel, and Delayed hydride cracking susceptibility is raised.Therefore, S content should control below 0.015%.
Mo: the hardening capacity effectively improving steel, can also strengthen crystal boundary.Content is less than 0.20% and is difficult to function as described above, but content is saturated more than 0.80% above-mentioned action effect, and cost is higher, should control within the scope of 0-0.8wt%.
Cr: effectively can improve the hardening capacity of steel and prevent high temperature surface oxidation, Cr content should control at 0.1-3.0wt%.
Cu: realizing precipitation strength by separating out ε-Cu, improving the intensity of steel, adding scope 0.1-2.00wt%.
B: hardening capacity and the purification crystal boundary that can significantly improve steel.Content lower than 0.0005% time more than act on not obvious, higher than 0.0050% time effect increase not obvious.Therefore, as added, B content should control within the scope of 0.0005-0.0050wt%.
Si: suppress Carbide Precipitation, improves the partition effect of C.When Si content is below 0.30%, above effect can not be played; Si content higher than 2.30% time, above effect is saturated, and may affect toughness.Therefore, Si content should control within the scope of 0.30-2.30wt%.
Nb: forming carbonitride can crystal grain thinning, the niobium of solid solution simultaneously can improve Unhydrated cement temperature, realizes austenitic flattening easily through controlled rolling.Lower than 0.02% time above-mentioned effect not obvious, higher than 0.10% time effect increase not obvious, reach capacity.Nb content should control within the scope of 0.01-0.10wt%.
Ti: be a kind of strong carbonitride-forming elements, the carbonitride of small and dispersed distribution can be formed, play the effect of fining austenite grains.Ti content should control within the scope of 0.01-0.25wt%.
V: with tiny carbonitride formed exist time, can crystal grain thinning; When existing with solution, can hardening capacity be improved, thus improve intensity.Adding in right amount can improving SNR, higher than 0.15% time easily form macrobead carbonitride, make toughness plasticity decline on the contrary.In addition, V also has precipitation strength effect, can further improve the intensity of steel.V content should control within the scope of 0.02-0.50wt%.
Al: can effectively deoxidation and crystal grain thinning, improves toughness.Content lower than 0.015% time more than act on not obvious, higher than 0.060% time effect increase not obvious, and thick aluminate may be formed, worsen the toughness of steel.Therefore, Al content should control within the scope of 0.015-0.060wt%.
[N]: combine with Al, Ti, Nb, V etc. and form compound, thus crystal grain thinning, but also can segregation crystal boundary and reduce grain-boundary strength.In addition, [N] is austenitic area expansion element, and it can improve the stability of adverse transformation austenite.[N] content should control within the scope of 0.002-0.35wt%.
RE: play deoxidation and desulfidation, and make inclusion modification, thus the toughness plasticity of steel can be improved.Lower than 0.001% time more than act on not obvious, higher than 0.050% time effect increase not obvious, reach capacity.Therefore, as added, RE content should control within the scope of 0.001-0.050wt%.
Ca: deoxidation and desulfurization, and inclusion is out of shape, thus the toughness plasticity of steel can be improved.S content in the addition of Ca and molten steel is 3:1.Therefore, Ca content should control within the scope of 0.005-0.030wt%.
The technical parameter of production technique of the present invention and control is:
(1) steel smelting with solidify: be applicable to converter, electric furnace and induction furnace and smelt, smelting composition is: 0.1-0.4wt%C and 3.0-8.00wt%Mn, P≤0.020wt%, S≤0.02wt%, and remaining is Fe and inevitable impurity,
(2) solidify: adopt continuous casting to produce strand or die casting production ingot casting;
(3) hot continuous rolling of strand or ingot casting:
Hot continuous rolling: by strand through 1100-1250 DEG C of heating, carry out 5-20 passes by roughing mill, hot rolling is to 30-50mm thickness specification, and connect after unit carries out 5-7 passes to 3-25mm by heat, batch at 250-700 DEG C after rolling, volume is heavily no more than 15 tons;
(4) cold rolling: after above-mentioned hot continuous rolling involves in row cleanup acid treatment, after cold continuous mill group is directly rolled 0.8-4.0mm, to obtain cold-rolled steel sheet;
Or, above-mentioned hot continuous rolling volume is reduced cold rolling processing load through the slow cooling of bell-type coil annealing with softening tissue, then carries out pickling, cold rolling;
(5) when the cold-rolled steel sheet obtained contains thicker carbide or cementite, then need the continuous annealing production line utilizing steel mill, steel plate heating is heated rapidly to Ac3+30 to 80 DEG C and carries out first annealing austenitizing, after insulation 3-10min, high-pressure air is chilled to soon within the scope of 150-350 DEG C and batches, and speed of cooling is not less than 10 DEG C/s;
When not carbide-containing or cementite, then obtain the martensite lath of uniform-dimension through solution treatment, or omit this operation and directly enter two-phase region continuous annealing operation described in (6);
(6) cool winding off after volume through pretreated annealing fast after the annealing of 5-10 minute on industrial continuous annealing production line, during heating, its rate of heating is greater than 50 DEG C/s; Being cooled to 200 DEG C of times during cooling is no more than 50 seconds; Continuous annealing temperature T scope is as follows according to C and Mn cubage in composition of steel:
For 980MPa rank steel annealing temperature be
1025-12×[%wtMn]-89×[%wtC]≤T(K)≤1055-12×[%wtMn]-89×[%wtC]
For 1080MPa rank steel annealing temperature be
1040-12×[%wtMn]-89×[%wtC]≤T(K)≤1070-12×[%wtMn]-89×[%wtC]
Following rule is followed in the selection of annealing temperature and annealing time: when annealing temperature capping, annealing time then removes the limit; And the former removes the limit, the latter's capping.
First advantage of the present invention is, the Composition Design (mainly through C and Mn) of simple economy, just can produce compared with currently available products through once simple continuous annealing process, its intensity rank remains unchanged but the two-phase automobile steel of plasticity better (low yield strength ratio, high-elongation);
The present invention be advantageous in that the two-phase automobile steel just can being produced low yield strength, high-tensile and good unit elongation by existing industrial continuous annealing production line through short-cycle annealing, its performance index reach following requirements: for tensile strength 980MPa rank dual phase steel, yield tensile ratio is no more than 0.55, and unit elongation is greater than 22%; For 1180MPa rank dual phase steel, its yield tensile ratio is no more than 0.55, and unit elongation is greater than 17%.
Accompanying drawing explanation
Fig. 1 is the relation of final residual austenite mark and annealing temperature.
Embodiment
Embodiment:
The present embodiment mainly in the exploitation of automobile with continuous annealing steel plate, the pre-treatment of process of the test simulation cold-rolling of steel plate steel plate and continuous annealing process.But this technique is equally applicable to medium-thick plate, section bar and Bar Wire Product.
The smelting of steel:
Steel of the present invention by the chemical composition of converter smelting as table 5, can cast out the continuously cast bloom of about 200-220mm, is rolling to the hot rolled coil of 3mm through hot continuous mill through continuous caster, its coiling temperature >500 DEG C, is cold-rolled to 1.6mm.The annealing of subsequent anneal in laboratory of cold-reduced sheet is simulated on machine and is completed.Cold-rolled steel sheet is divided into two batches, (A) after 850 DEG C of solid solution half an hour, air cooling after taking out; (B) without solution treatment.Then this cold-rolled steel sheet is quickly heated up to 670-710 be incubated 10 minutes after rapid cooling, then measure the residual austenite mark in the finished product and mechanical property, respectively as shown in Fig. 1 and table 6.
The chemical composition of table 5 invention steel, weight percentage
| C | Mn | P | S | |
| 1 | 0.1 | 5.0 | 0.01 | 0.005 |
| 2 | 0.20 | 5.0 | 0.009 | 0.002 |
The mechanical mechanics property of the steel plate that table 6 is composition shown in table 5 after 670-710 DEG C of annealing in 10 minutes
Claims (2)
1. a production method for low yield strength ratio, high-strength vehicle dual phase sheet steel, is characterized in that, the technical parameter of production technique and control is:
(1) steel smelting with solidify: be applicable to converter, electric furnace and induction furnace and smelt, smelting composition is: 0.1-0.4wt%C and 3.0-8.00wt%Mn, P≤0.020wt%, S≤0.02wt%, and remaining is Fe and inevitable impurity,
(2) solidify: adopt continuous casting to produce strand or die casting production ingot casting;
(3) hot continuous rolling of strand or ingot casting:
Hot continuous rolling: by strand through 1100-1250 DEG C of heating, carry out 5-20 passes by roughing mill, hot rolling is to 30-50mm thickness specification, and connect after unit carries out 5-7 passes to 3-25mm by heat, batch at 250-700 DEG C after rolling, volume is heavily no more than 15 tons;
(4) cold rolling: after above-mentioned hot continuous rolling involves in row cleanup acid treatment, after cold continuous mill group is directly rolled 0.8-4.0mm, to obtain cold-rolled steel sheet;
(5) when the cold-rolled steel sheet obtained contains thicker carbide or cementite, then need the continuous annealing production line utilizing steel mill, steel plate heating is heated rapidly to Ac3+30 to 80 DEG C and carries out first annealing austenitizing, after insulation 3-10min, high-pressure air is chilled to soon within the scope of 150-350 DEG C and batches, and speed of cooling is not less than 10 DEG C/s;
When not carbide-containing or cementite, then obtain the martensite lath of uniform-dimension through solution treatment, or omit this operation and directly enter step (6);
(6) cool winding off after volume through pretreated annealing fast after the annealing of 5-10 minute on industrial continuous annealing production line, during heating, its rate of heating is greater than 50 DEG C/s; The time being cooled to 200 DEG C during cooling is no more than 50 seconds; Continuous annealing temperature T scope is as follows according to C and Mn cubage in composition of steel:
For 980MPa rank steel annealing temperature be
1025-12 × [%wtMn]-89 × [%wtC]≤T (K)≤1055-12 × [%wtMn]-89 × [%wtC] for 1080MPa rank steel annealing temperature is
1040-12×[％wtMn]-89×[％wtC]≤T(K)≤1070-12×[％wtMn]-89×[％wtC]；
The chemical composition of described dual phase sheet steel is: C:0.1-0.40wt%, Mn:3.0-8.0wt%, P≤0.020wt%, S≤0.02wt%, and surplus is Fe and inevitable impurity; Another lower one or multiple element: Ni:0.1-3.0wt%, Cr:0.2-3.0wt%, Mo:0.1-0.8wt%, Si:0.3-2.3wt%, Cu:0.5-2.0wt%, B:0.0005-0.005wt%, Nb:0.02-0.10wt%, [N]: 0.002-0.25wt%, Ti:0.05-0.25wt%, V:0.02-0.25wt%, Al:0.015-0.060wt%, RE:0.002-0.005wt%, Ca:0.005-0.03wt% on this basis.
2. method according to claim 1, is characterized in that, in step (4), above-mentioned hot continuous rolling volume is reduced cold rolling processing load through the slow cooling of bell-type coil annealing with softening tissue, then carries out pickling, cold rolling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310507894.9A CN103556048B (en) | 2013-10-24 | 2013-10-24 | Production method for two-phase automobile steel plate with low yield-strength ratio and high strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310507894.9A CN103556048B (en) | 2013-10-24 | 2013-10-24 | Production method for two-phase automobile steel plate with low yield-strength ratio and high strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103556048A CN103556048A (en) | 2014-02-05 |
| CN103556048B true CN103556048B (en) | 2015-04-29 |
Family
ID=50010392
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201310507894.9A Active CN103556048B (en) | 2013-10-24 | 2013-10-24 | Production method for two-phase automobile steel plate with low yield-strength ratio and high strength |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103556048B (en) |
Families Citing this family (29)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106811698B (en) * | 2015-12-02 | 2018-04-24 | 鞍钢股份有限公司 | A kind of high strength steel plate and its manufacture method based on tissue precise controlling |
| CN105803321B (en) * | 2016-03-23 | 2018-01-26 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of 980MPa levels cold-rolled biphase steel of ultra-fine grain containing vanadium and preparation method thereof |
| CN107554292B (en) * | 2016-06-30 | 2020-11-27 | 宁波高发汽车控制系统股份有限公司 | Electronic accelerator pedal assembly |
| CN105925912B (en) * | 2016-07-11 | 2018-01-26 | 攀钢集团攀枝花钢铁研究院有限公司 | Tensile strength 780MPa levels cold-rolled biphase steel containing vanadium and preparation method thereof |
| CN106350739B (en) * | 2016-09-14 | 2019-07-23 | 钢铁研究总院 | Low-alloy superplasticity steel and preparation method in low-carbon in high strain rate |
| CN106801198B (en) * | 2017-02-07 | 2018-02-09 | 和县隆盛精密机械有限公司 | A kind of alloy-steel casting and its Technology for Heating Processing suitable for mechanical arm bool |
| CN107058869B (en) * | 2017-05-22 | 2019-05-31 | 钢铁研究总院 | Ultralow yield tensile ratio 980MPa grades of cold-rolled biphase steels and its manufacturing method |
| CN107641700B (en) * | 2017-09-20 | 2019-01-25 | 武汉钢铁有限公司 | Method based on CSP process production thin gauge hot rolling DP1180 steel |
| CN107974631B (en) * | 2017-12-01 | 2019-07-30 | 安徽工业大学 | A kind of method of various dimensions enhancing plasticising production high strength and ductility superhigh intensity third generation automobile steel |
| WO2019127240A1 (en) * | 2017-12-28 | 2019-07-04 | GM Global Technology Operations LLC | Steel for hot stamping with enhanced oxidation resistance |
| CN108265169B (en) * | 2018-01-18 | 2019-06-07 | 华北理工大学 | A kind of high strength steel treatment process |
| MX2020010292A (en) * | 2018-03-30 | 2020-10-28 | Ak Steel Properties Inc | Low alloy third generation advanced high strength steel and process for making. |
| WO2019222950A1 (en) | 2018-05-24 | 2019-11-28 | GM Global Technology Operations LLC | A method for improving both strength and ductility of a press-hardening steel |
| US11612926B2 (en) | 2018-06-19 | 2023-03-28 | GM Global Technology Operations LLC | Low density press-hardening steel having enhanced mechanical properties |
| CN109023130A (en) * | 2018-08-07 | 2018-12-18 | 马鞍山钢铁股份有限公司 | Economical medium managese steel of cold rolling containing Nb of one kind and preparation method thereof |
| CN109266812B (en) * | 2018-10-10 | 2020-10-16 | 安阳钢铁股份有限公司 | Low-yield-ratio high-strength quenched and tempered steel for coal mine hydraulic support and manufacturing method thereof |
| CN109536837B (en) * | 2018-12-10 | 2021-03-09 | 钢铁研究总院 | high-N-content ultrafine-grain 1200 MPa-grade cold-rolled dual-phase steel and production process thereof |
| JP7288184B2 (en) * | 2019-03-22 | 2023-06-07 | 日本製鉄株式会社 | Method for producing hot-dip Zn-Al-Mg plated steel sheet |
| US11530469B2 (en) | 2019-07-02 | 2022-12-20 | GM Global Technology Operations LLC | Press hardened steel with surface layered homogenous oxide after hot forming |
| CN110184543B (en) * | 2019-07-04 | 2021-07-20 | 广西大学 | Low-nickel high-strength automobile steel plate and manufacturing method thereof |
| CN111187893B (en) * | 2020-02-24 | 2021-06-29 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for enhancing uniformity of 780DP high-hole-expansion cold-rolled dual-phase steel |
| CN111455282B (en) * | 2020-05-11 | 2021-03-16 | 武汉钢铁有限公司 | Quenching distribution steel with tensile strength more than or equal to 1500MPa produced by adopting short process and method |
| CN113926892A (en) * | 2020-06-29 | 2022-01-14 | 宝山钢铁股份有限公司 | Stamping forming process and application of hot-rolled ultrahigh-strength dual-phase steel part with tensile strength of more than or equal to 980MPa |
| CN111893393B (en) * | 2020-08-20 | 2021-11-23 | 山东华星新材料科技有限公司 | Mo-Ti alloy wear-resistant medium manganese steel and preparation method thereof |
| CN112430785A (en) * | 2020-11-20 | 2021-03-02 | 内蒙古科技大学 | High-strength steel containing rare earth and preparation method thereof |
| CN114214573B (en) * | 2021-12-17 | 2022-12-02 | 西安交通大学 | Ferrite-martensite dual-phase steel and preparation method thereof |
| CN114807777B (en) * | 2022-04-27 | 2023-06-16 | 鞍钢股份有限公司 | 500 MPa-level steel for automobile axle housing for hot stamping and production method thereof |
| CN114807780B (en) * | 2022-04-27 | 2023-07-14 | 鞍钢股份有限公司 | 600 MPa-level steel for automobile axle housing for hot stamping and production method thereof |
| CN114836696B (en) * | 2022-04-27 | 2023-06-20 | 鞍钢股份有限公司 | 390 MPa-level steel for automobile axle housing for hot stamping and production method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101638749A (en) * | 2009-08-12 | 2010-02-03 | 钢铁研究总院 | Automobile steel with low cost and high strength ductility balance and preparation method thereof |
| CN103147000A (en) * | 2013-03-20 | 2013-06-12 | 钢铁研究总院 | Polygonal ferrite-acicular ferrite two-phase steel plate/belt and production method thereof |
-
2013
- 2013-10-24 CN CN201310507894.9A patent/CN103556048B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101638749A (en) * | 2009-08-12 | 2010-02-03 | 钢铁研究总院 | Automobile steel with low cost and high strength ductility balance and preparation method thereof |
| CN103147000A (en) * | 2013-03-20 | 2013-06-12 | 钢铁研究总院 | Polygonal ferrite-acicular ferrite two-phase steel plate/belt and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103556048A (en) | 2014-02-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103556048B (en) | Production method for two-phase automobile steel plate with low yield-strength ratio and high strength | |
| CN101638749B (en) | Automobile steel with low cost and high strength ductility balance and preparation method thereof | |
| CN102031456B (en) | Steel plate for stamping and quenching and thermoforming method of steel plate | |
| CN106086685B (en) | With the thin hot forming steel of tensile strength >=1500MPa of sheet billet Direct Rolling and production method | |
| CN100439543C (en) | Hot-rolled super-strength martensitic steel and method for manufacturing same | |
| CN102758133B (en) | 1000MPa-level automobile steel with high product of strength and elongation and manufacturing method thereof | |
| CN106086684B (en) | With the thin hot forming steel of tensile strength >=1900MPa of sheet billet Direct Rolling and production method | |
| CN102839329B (en) | Cold-rolling double-phase-steel steel plate with tensile strength of 450 MPa, and preparation method thereof | |
| CN108754319A (en) | Using the tensile strength >=1800MPa grades of hot forming steel and method of the production of ESP producing lines | |
| CN102031455A (en) | Steel plate for stamping and quenching and manufacturing method thereof | |
| CN106119692A (en) | By the tensile strength of medium thin slab Direct Rolling >=1500MPa hot forming steel and production method | |
| CN106191678B (en) | With the tensile strength >=1700MPa hot formings steel and production method of medium thin slab Direct Rolling | |
| CN103060678A (en) | Medium temperature deformation nanometer austenite enhanced plasticized steel and preparation method thereof | |
| CN104328360A (en) | Double-phase twinborn induced plastic super-strength automobile steel plate and preparation method thereof | |
| CN104726767A (en) | High-strength cold-rolled steel plate with TRIP (transformation induced plasticity) effect and production method thereof | |
| CN101348883A (en) | Niobium and titanium composite added ultra-low carbon baking hardening steel plate and manufacturing method thereof | |
| CN101363099A (en) | Cold rolled dual-phase sheet steel with 1000MPa grade tensile strength and preparation method thereof | |
| CN103361560A (en) | Cold-rolled hot-molded steel plate and production method thereof | |
| CN102199732B (en) | Boron containing steel plate for heat treatment and manufacturing method thereof | |
| CN103233161A (en) | Low-yield-ratio high-strength hot-rolled Q&P steel and manufacturing method thereof | |
| CN104513927A (en) | High-strength high-rigidity steel plate with tensile strength of 800 MPa and preparation method thereof | |
| CN106086683B (en) | With the thin hot forming steel of tensile strength >=1700MPa of sheet billet Direct Rolling and production method | |
| CN106222555B (en) | With the thin hot forming steel of tensile strength >=1300MPa of sheet billet Direct Rolling and production method | |
| CN104278194A (en) | High-strength high-plasticity cold-rolled steel plate for automobiles and production method thereof | |
| CN102021483B (en) | Cold-rolled dual-phase steel plate with 1,200 MPa-level tensile strength and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |