CN104328347A - Alloy steel for high-strength plates and preparation method of alloy steel - Google Patents
Alloy steel for high-strength plates and preparation method of alloy steel Download PDFInfo
- Publication number
- CN104328347A CN104328347A CN201410629911.0A CN201410629911A CN104328347A CN 104328347 A CN104328347 A CN 104328347A CN 201410629911 A CN201410629911 A CN 201410629911A CN 104328347 A CN104328347 A CN 104328347A
- Authority
- CN
- China
- Prior art keywords
- steel
- strength
- alloy
- steel alloy
- rolling
- 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.)
- Granted
Links
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 36
- 238000002360 preparation method Methods 0.000 title claims abstract description 19
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 52
- 239000010959 steel Substances 0.000 claims abstract description 52
- 238000001816 cooling Methods 0.000 claims abstract description 32
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 31
- 239000000203 mixture Substances 0.000 claims abstract description 26
- 238000005096 rolling process Methods 0.000 claims abstract description 17
- 230000007704 transition Effects 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 238000005266 casting Methods 0.000 claims abstract 2
- 238000002844 melting Methods 0.000 claims abstract 2
- 230000008018 melting Effects 0.000 claims abstract 2
- 238000005275 alloying Methods 0.000 claims description 5
- 229910045601 alloy Inorganic materials 0.000 abstract description 11
- 239000000956 alloy Substances 0.000 abstract description 11
- 238000000034 method Methods 0.000 abstract description 11
- 230000008569 process Effects 0.000 abstract description 8
- 238000001953 recrystallisation Methods 0.000 abstract description 4
- 239000010955 niobium Substances 0.000 description 14
- 229910000859 α-Fe Inorganic materials 0.000 description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- 239000011572 manganese Substances 0.000 description 10
- 229910052710 silicon Inorganic materials 0.000 description 8
- 239000000126 substance Substances 0.000 description 8
- 230000009466 transformation Effects 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical group [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 7
- 229910001563 bainite Inorganic materials 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 7
- 239000010703 silicon Substances 0.000 description 7
- 238000005728 strengthening Methods 0.000 description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 5
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000005452 bending Methods 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 3
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 3
- 229910000885 Dual-phase steel Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000006378 damage Effects 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 239000004033 plastic Substances 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 239000003351 stiffener Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 101000993059 Homo sapiens Hereditary hemochromatosis protein Proteins 0.000 description 1
- 239000005864 Sulphur Substances 0.000 description 1
- 208000027418 Wounds and injury Diseases 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 239000004568 cement Substances 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 239000000295 fuel oil Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 208000014674 injury Diseases 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000004064 recycling Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
-
- 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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/007—Ferrous alloys, e.g. steel alloys containing silver
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- C21D2211/001—Austenite
Landscapes
- 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 Steel (AREA)
Abstract
The invention discloses alloy steel for high-strength plates. The basic composition of the alloy steel comprises the following components in percentage by weight: 0.30-0.38% of C, 0.5-0.8% of Mn, 0.9-1% of Si, 0.01-0.6% of Al, 2.0-2.2% of Cr, 0.08-0.1% of Nb, 0.02-0.06% of Ag, 1.5-1.6% of Cu, 0.01-0.02% of W, not more than 0.02% of P, less than 0.012% of S and the balance of Fe and inevitable impurities. The preparation method comprises the following steps: melting an alloy and casting; re-heating a steel billet at the heating temperature of 1200 DEG C-1210 DEG C; and rolling: performing initial rolling for thermal deformation in a temperature range of recrystallization of austenite and performing final rolling in the temperature range which is lower than the recrystallization temperature of the austenite but higher than a transition point of Ar3 by adopting three passes, wherein the final rolling temperature is 900-950 DEG C. Through the reasonable and cheap alloy composition design and a staged cooling process after rolling, the tensile strength of a hot-rolled steel plate is not less than 1200MPa, the yield strength is not less than 550MPa, the yield-strength ratio is low, and the extension rate A80 (test sample with JIS13A gauge length of 80mm) is not less than 13%.
Description
Technical field
The present invention relates to a kind of steel alloy, be specifically related to a kind of high-strength panel steel alloy and preparation method thereof.
Background technology
Along with the development of automobile industry, more and more higher to the requirement of vehicle safety, the demand of the in short supply and environmental protection of the energy also requires that vehicle alleviates deadweight to reduce fuel oil consumption simultaneously, therefore the requirement of strength of vehicles steel plate is improved constantly, simultaneously also more and more, thinner to the performance requriements division of labor of different sites steel plate, advanced high-strength steel (AHSS) or ultrahigh-strength steel (Ultra-HSS) arise at the historic moment.The steel grade that usual tensile strength is greater than 700MPa can be classified as ultrahigh-strength steel.Superstrength has very high tensile strength and high deformation absorbs energy, is applicable to the components such as manufacturing structure part, stiffener, safety member.
The alloying elements such as Nb, Ti, Ni, Cr, Mo and Cu are added in general employing, the intensity of steel is improved by schedule of reinforcements such as solution strengthening, precipitation strength and precipitation strengths, so just cause complex manufacturing and steel cost to increase, be also unfavorable for the recoverable of iron and steel.Along with people are to the attention of green metallurgical and recycling economy, how efficent use of resources, reduce the focus that manufacturing cost becomes research.The design philosophy that present inventor makes full use of " water is as alloying element ", only with the economical rationality composition of carbon, manganese, silicon, the least possible interpolation expensive alloying elements, ultrahigh-strength steel multi-phase Steels is obtained by controlling roller repairing mode, its Main Tissues is the ferrite (likely containing a small amount of residual austenite) that bainite and martensite and small and dispersed distribute, and tensile strength is higher than 1000MPa, and yield tensile ratio is low, unit elongation reaches 20%, and has good cold-bending property.
In the world about the manufacture method of hot-rolled high-strength steel plate has formed multinomial patent, but mainly concentrate on Hi-Stren steel (HSLA), dual phase steel (DP) and phase change induction plasticity steel (TRIP), for the hot-rolled super-strength steel plate (thickness of slab 1.5mm ~ 6mm) of automobile more than 1000MPa, not yet seek unity of standard.
Summary of the invention
For achieving the above object, technical scheme of the present invention is, design of material mainly uses the conventional deoxidant element of the steel-making such as Si, Mn, Al be main alloy element, is suitably equipped with Cu, Cr, Nb, Ag, W microalloying.
High-strength panel steel alloy provided by the invention its basic composition is the composition of following mass percent:
Al:0.01 ~ 0.6, Si:0.9 ~ 1, Mn:0.5 ~ 0.8, C:0.30 ~ 0.38 Cr 2.0 ~ 2.2, Nb 0.08 ~ 0.1 Ag0.02 ~ 0.06 Cu 1.5 ~ 1.6 W 0.01 ~ 0.02, P :≤0.02S:<0.012 all the other be Fe and inevitable impurity.
A preferred embodiment of high-strength panel steel alloy of the present invention is: in above-mentioned chemical composition, add C:0.32 ~ 0.36%, more select C:0.33 ~ 0.35%, more select C:0.34%.
Another preferred embodiment of high-strength panel steel alloy of the present invention is: in above-mentioned chemical composition, add Mn:0.6 ~ 0.7%, more select Mn:0.65%.
Another preferred embodiment of high-strength panel steel alloy of the present invention is: in above-mentioned chemical composition, add Al:0.01 ~ 0.6, more select Al:0.02 ~ 0.1, more select Mn:0.05.
Another preferred embodiment of high-strength panel steel alloy of the present invention is: in above-mentioned chemical composition, add Nb 0.08 ~ 0.1, more selects Nb 0.09.
Another preferred embodiment of high-strength panel steel alloy of the present invention is: in above-mentioned chemical composition, add Cu 1.5 ~ 1.6, more selects Cu 1.55.
Below, high-strength panel steel alloy of the present invention and the chemical composition of high-strength panel steel alloy made with this steel grade are done as describing in detail.
C: determine that the microstructure of steel is formed, the intensity of steel can be significantly improved, greatly can reduce welding property time too high, by weight percentage, content 0.30 ~ 0.38 should be adopted;
Mn: manganese is displaced type alloying element, the intensity of steel is improved by solution strengthening crystal grain thinning, being containing compensating the main and most economical strengthening element causing loss of strength because C content reduces in bainite and martensite steel, the intensity of the rear steel plate of quenching can be improved.Manganese is the element of stable austenite, can reduce austenitic transformation temperature, promotes the dissolving of carbon in austenite, improves the hardening capacity of steel.But avoid too high Fe content, because the too high activity that can reduce carbon in austenite of Fe content, this promote the formation of carbide, and hinder ferrite transformation, make the enrichment of carbon in process of cooling drop to minimum, cannot quench and obtain martensite.Too high manganese is also easy to segregation, worsens the performance of steel.About silicon and manganese, the relative quantity that must adjust interpolation, to control distribution and the volume fraction of phase, should adopt content 0.5 ~ 0.8 by weight percentage;
Si: silicon plays solution strengthening effect in steel, can suppress the precipitation of carbide when content is more, promote that ferrite is formed, thus carbon is diffused in austenite.Silicon or analogous element serve as the effect of ferrite stabilizer, not only accelerate the formation of proeutectoid ferrite, and hinder the precipitation of cementite between bainite Formation period, accelerate carbon be diffused into austenite mutually in, improve the hardening capacity of steel.Add silicon and coordinate sub-sectional cooling technique to promote ferrite is separated out, be conducive to the reduction yield strength of steel and yield tensile ratio, and make steel after phase transformation terminates, a small amount of residual austenite may be remained with, make steel also have certain plasticity while intensity is high.Because the present invention does not add the steel that Nb, V and Ti also can obtain the superstrength of good extending performance, therefore, require to add element silicon, by weight percentage, silicone content should be adopted to be 0.9 ~ 1;
Al: have similar effect with Si, promote that proeutectoid ferrite generates the formation that can suppress cementite, but too high levels damages strong plasticity, by weight percentage, should adopt content 0.01 ~ 0.6;
Nb: niobium to the effect of grain refining clearly, the recovery and recrystallization of deformed austeaite is hindered by NbC strain induced precipitate in course of hot rolling, when controlled rolling and controlled cooling model make the deformed austeaite of non-recrystallization zone rolling be organized in phase transformation, change tiny phase-change product into, improve the intensity of steel.By weight percentage, content 0.08 ~ 0.1 should be adopted.
Ag: recrystallize strengthening element, can make up the decline of intensity.By weight percentage, content 0.02 ~ 0.06 should be adopted.
W: promote that proeutectoid ferrite generates the formation simultaneously suppressing cementite.By weight percentage, content 0.01 ~ 0.02 should be adopted.
Sulphur and phosphorus are inevitable impurity elements in steel, and it is more low better to wish.Sulphur forms plastic occluded foreignsubstance manganese sulfide with chemical combination such as manganese in steel, especially to the horizontal plastic property of steel and toughness unfavorable, it is more low better therefore to wish.。Phosphorus is also the harmful element in steel, the plasticity of grievous injury steel plate and toughness.
Adopt chemical composition used in the present invention can produce a kind of high-strength panel steel alloy.
A preparation method for high-strength panel steel alloy, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
Wherein, reheat in step at slab, soaking time is pressed thickness and is calculated for 2 minutes/millimeter.
Wherein, in cooling step, between first stage cooling and subordinate phase cool, stop 2 ~ 10 seconds.
Ultrahigh-strength steel obtains high strength mainly through phase transformation strengthening (bainite and martensite), and requires higher unit elongation, so wish that having soft in tissue is ferrite mutually.Because intensity is higher than 1200MPa, therefore ferrite content can not be too high.The key addressed this problem is in the process of cooling after finish to gauge, obtains each phase constitution that ratio is suitable: the ferrite of bainite, bainite and certain content, likely also containing a small amount of residual austenite.Therefore in process of cooling, following phase transition process is needed: after finish to gauge, rapidly steel is cooled to austenite and ferrite two-phase region temperature range; Because element silicon helps lend some impetus to ferrite transformation, rapidly ferrite transformation can occur at this temperature range air cooling, in phase transition process, carbon and manganese element diffuse in remaining austenite; After air cooling, steel plate is forced to be cooled to low temperature to batch, force, in process of cooling, bainite and martensite phase transformation to occur at second segment.
After Unhydrated cement finish to gauge, the tissue of steel is made up of the austenite be out of shape.Rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C; Cooling: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.Detailed rolling, process for cooling.
By rationally cheap design of alloy with roll rear sub-sectional cooling technique and make the tensile strength of hot-rolled steel sheet reach to be more than or equal to 1200MPa, yield strength is more than or equal to 550MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) is more than or equal to 13%.And there is good cold-bending property.Can be used for stiffener and the safety member of automobile.
Embodiment
Embodiment 1
A kind of high-strength panel steel alloy its basic composition is the composition of following mass percent: C:0.30Mn:0.5 Si:0.9 Al:0.01 Cr 2.0, Nb 0.08 Ag0.02 Cu 1.5 W 0.01, P :≤0.02 S:<0.012 all the other be Fe and inevitable impurity.
A preparation method for steel alloy high-strength panel, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
The tensile strength of hot-rolled steel sheet reaches 1270MPa, yield strength 560MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) 13%.And there is good clod wash.
Embodiment 2
A kind of high-strength panel steel alloy its basic composition is the composition of following mass percent: C:0.38Mn:0.8 Si:1 Al:0.6 Cr 2.2, Nb 0.1 Ag 0.06 Cu1.6 W 0.02, P :≤0.02 S:<0.012 all the other be Fe and inevitable impurity.
A preparation method for steel alloy high-strength panel, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
The tensile strength of hot-rolled steel sheet reaches 1270MPa, yield strength 570MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) 13%.And there is good clod wash.
Embodiment 3
A kind of high-strength panel steel alloy its basic composition is the composition of following mass percent: C:0.32Mn:0.6 Si:0.95 Al:0.05 Cr 2.1, Nb 0.09 Ag0.04 Cu 1.5 W 0.015, P :≤0.02 S:<0.012 all the other be Fe and inevitable impurity.
A preparation method for steel alloy high-strength panel, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
The tensile strength of hot-rolled steel sheet reaches 1280MPa, yield strength 570MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) 14%.And there is good clod wash.
Embodiment 4
A kind of high-strength panel steel alloy its basic composition is the composition of following mass percent: C:0.37Mn:0.7 Si:1 Al:0.2 Cr 2.2, Nb 0.09 Ag0.05 Cu 1.5 W 0.01, P :≤0.02 S:<0.012 all the other be Fe and inevitable impurity.
A preparation method for steel alloy high-strength panel, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
The tensile strength of hot-rolled steel sheet reaches 1280MPa, yield strength 570MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) 14%.And there is good clod wash.
Embodiment 5
A kind of high-strength panel steel alloy its basic composition is the composition of following mass percent: C:0.33Mn:0.5 Si:0.9 Al:0.4 Cr 2.1, Nb 0.1 Ag0.04 Cu 1.5W 0.01, P :≤0.02 S:<0.012 all the other be Fe and inevitable impurity.
A preparation method for steel alloy high-strength panel, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
The tensile strength of hot-rolled steel sheet reaches 1260MPa, yield strength 570MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) 14%.And there is good clod wash.
Embodiment 6
A kind of high-strength panel steel alloy its basic composition is the composition of following mass percent: C:0.35Mn:0.5 Si:0.9Al:0.4 Cr 2.1, Nb 0.1 Ag0.04 Cu 1.5 W 0.01, P :≤0.02 S:<0.012 all the other be Fe and inevitable impurity.
A preparation method for steel alloy high-strength panel, described preparation method comprises the following steps:
1) alloy is melted refine and cast;
2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
The tensile strength of hot-rolled steel sheet reaches 1250MPa, yield strength 570MPa, low yield strength ratio, unit elongation A80 (JIS13A gauge length 80mm sample) 13%.And there is good cold-bending property.
Claims (7)
1. a high-strength panel steel alloy, it is elementary composition is the composition of following mass percent: C:0.30 ~ 0.38Mn:0.5 ~ 0.8Si:0.9 ~ 1Al:0.01 ~ 0.6Cr 2.0 ~ 2.2, Nb 0.08 ~ 0.1Ag 0.02 ~ 0.06Cu 1.5 ~ 1.6W 0.01 ~ 0.02, P :≤0.02S:<0.012 all the other be Fe and inevitable impurity.
2. steel alloy as claimed in claim 1, it is characterized in that, described C content is 0.32 ~ 0.36%.
3. steel alloy as claimed in claim 2, it is characterized in that, described C content is 0.34%.
4. steel alloy as claimed in claim 1, it is characterized in that, described Mn content is 0.6 ~ 0.7%.
5. steel alloy as claimed in claim 4, it is characterized in that, described Mn content is 0.65%.
6. steel alloy as claimed in claim 1, it is characterized in that, described Cu content is 1.55%.
7. the preparation method of high-strength panel steel alloy as described in claim 1-6, is characterized in that step is as follows:
(1) above-mentioned alloying element proportionally to be prepared burden melting casting;
(2) steel billet reheats: Heating temperature is 1200 DEG C ~ 1210 DEG C;
(3) rolling: breaking down thermal distortion in the temperature range of austenite generation recrystallize, in the temperature range lower than austenite generation recrystallize but higher than Ar3 transition point, adopts 3 passages, carries out finish to gauge; Finishing temperature is 900-950 DEG C;
(4) cool: the first stage, be first cooled to 500 DEG C with the speed of cooling of 15 DEG C/s; Subordinate phase, is cooled to 200 DEG C with the speed of cooling of 40 DEG C/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410629911.0A CN104328347B (en) | 2014-11-10 | A kind of high-strength panel steel alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410629911.0A CN104328347B (en) | 2014-11-10 | A kind of high-strength panel steel alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN104328347A true CN104328347A (en) | 2015-02-04 |
| CN104328347B CN104328347B (en) | 2017-01-04 |
Family
ID=
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07102320A (en) * | 1993-10-05 | 1995-04-18 | Kobe Steel Ltd | Production of high strength steel wire excellent in weldability |
| CN1910301A (en) * | 2004-01-14 | 2007-02-07 | 新日本制铁株式会社 | Hot dip galvanized high strength steel sheet having excellent plating adhesion and hole expansibility, and its production method |
| CN1978688A (en) * | 2005-12-06 | 2007-06-13 | 鞍钢股份有限公司 | Hot-rolled black skin surface steel plate with firmly adhered oxide layer and manufacturing method thereof |
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07102320A (en) * | 1993-10-05 | 1995-04-18 | Kobe Steel Ltd | Production of high strength steel wire excellent in weldability |
| CN1910301A (en) * | 2004-01-14 | 2007-02-07 | 新日本制铁株式会社 | Hot dip galvanized high strength steel sheet having excellent plating adhesion and hole expansibility, and its production method |
| CN1978688A (en) * | 2005-12-06 | 2007-06-13 | 鞍钢股份有限公司 | Hot-rolled black skin surface steel plate with firmly adhered oxide layer and manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101008066B (en) | Hot rolling martensite steel plate with tensile strength higher than 1000Mpa and its production method | |
| CN101191174B (en) | Hot-rolling phase change induction plasticity steel with 750MPa-level extension strength and preparation method thereof | |
| CN103014554B (en) | Low-yield-ratio high-tenacity steel plate and manufacture method thereof | |
| CN103352167B (en) | A kind of low yield strength ratio high strength bridge steel plate and manufacture method thereof | |
| CN109023036B (en) | Ultrahigh-strength hot-rolled complex-phase steel plate and production method thereof | |
| CN100439543C (en) | Hot-rolled super-strength martensitic steel and method for manufacturing same | |
| CN106011643B (en) | A kind of tensile strength 590MPa grades of cold-rolled biphase steels and preparation method thereof | |
| CN104451410B (en) | Steel for 600MPa-level high-strength steel bars and thermal mechanical rolling method thereof | |
| CN101376944B (en) | High-strength high-tensile ratio cold-rolled steel sheet and manufacturing method thereof | |
| CN102174685B (en) | 800 MPa grade cold-rolling dual-phase steel and manufacturing method thereof | |
| CN102251170A (en) | Ultrahigh-strength bainitic steel and manufacture method thereof | |
| CN102876970B (en) | Steel with yield strength larger than or equal to 390 MPa for high-rise buildings and production method of steel | |
| CN104357744A (en) | Tensile strength more than or equal to 780MPa grade hot-rolled dual phase steel and production method thereof | |
| CN103882330A (en) | Low-yield-ratio ultrahigh-strength non-quenched and tempered steel plate and production method thereof | |
| CN104513927A (en) | High-strength high-rigidity steel plate with tensile strength of 800 MPa and preparation method thereof | |
| CN103237906A (en) | Method for manufacturing high-strength cold-rolled/hot-rolled DP steel having a tensile strength grade of 590 MPa and excellent workability, as well as little deviation in the material properties thereof | |
| CN104264038A (en) | 440 MPa-grade continuous-annealed and cold-rolled structural steel plate and production process thereof | |
| CN103014545B (en) | High-strength steel plate with 900 Mpa-level yield strength and preparation method of steel plate | |
| CN101270436B (en) | Hot-rolled polyphase steel plate and method for manufacturing same | |
| CN106498296A (en) | Manufacturing method of high-strength steel with yield strength of 1100MPa | |
| CN104451402A (en) | 700MPa-grade hot-rolled dual-phase steel and manufacturing method thereof | |
| CN110284066B (en) | Thin-gauge low-yield-ratio pipeline steel and manufacturing method thereof | |
| CN102953004A (en) | High-strength complex phase steel plate and manufacturing method thereof | |
| CN102676926A (en) | Complex phase steel plate and manufacturing method thereof | |
| CN105714186A (en) | Continuous annealing low-alloy and high-strength steel plate and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C41 | Transfer of patent application or patent right or utility model | ||
| TA01 | Transfer of patent application right |
Effective date of registration: 20161017 Address after: 214000 Jiangsu city of Wuxi province in Northeast Town Xishan District Wang Zi Cun Mao Ziqiao No. 255 Applicant after: Guo Dong Address before: Lake town of Xishan District 214000 Jiangsu city of Wuxi Province Green River Dang Village No. 11 Applicant before: Hua Yuye |
|
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CB03 | Change of inventor or designer information | ||
| CB03 | Change of inventor or designer information |
Inventor after: Jin Yongbao Inventor before: Hua Yuye |
|
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20170801 Address after: 226200 No. 188 Binhai Avenue, Binhai Industrial Park, Nantong, Jiangsu, Qidong Patentee after: Qidong Haina Special Steel Co., Ltd. Address before: 214000 Jiangsu city of Wuxi province in Northeast Town Xishan District Wang Zi Cun Mao Ziqiao No. 255 Patentee before: Guo Dong |
|
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20170104 Termination date: 20191110 |