CN103649355A - Hot-rolled high-strength steel strip with improved HAZ-softening resistance and method of producing said steel - Google Patents
Hot-rolled high-strength steel strip with improved HAZ-softening resistance and method of producing said steel Download PDFInfo
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- CN103649355A CN103649355A CN201280034223.9A CN201280034223A CN103649355A CN 103649355 A CN103649355 A CN 103649355A CN 201280034223 A CN201280034223 A CN 201280034223A CN 103649355 A CN103649355 A CN 103649355A
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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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- 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
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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
- 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
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
Hot-rolled high-strength micro-alloyed steel strip with improved HAZ-softening resistance having a microstructure comprising martensite, tempered martensite and/or bainite.
Description
The present invention relates to have improvement the softening resistivity of HAZ-hot-rolled high-strength steel band and the method for producing described steel.
Traditionally, by austenitizing and the manufacture of quenching, there is the steel of high-yield strength, but by this technology, may not realize surface quality and the impelling strength for example optimized.Preparation expense is also high.
EP1375694 recorded by hot rolling, produce there is good processing characteristics and welding property high strength, the method for high-ductility steel.But it is softening that the inventor finds that these steel are easy to HAZ-.Serve as reasons welding or hot intensive cutting operation of heat affected zone (HAZ) changed the region of the base material of its microstructure and character.From welding process and cooling heat more subsequently, caused surrounding the variation in the region of this weld seam.The heat affected zone that forms the weld seam in contiguous this steel is one of the most common region of weld failure.Modern thermo-mechanical rolling (TMCP) steel, due to their poor chemical composition, and low carbon content especially, therefore needs the welding setting carefully controlled to realize in weld seam HAZ intensity fully.For conventional soft steel and some TMCP pipe line steel, for example X70 and X80, HAZ is softening is often the result due to the welding sequence of the high calorie of heat dissipation input slowly in HAZ.For the TMCP steel of higher level, X100 for example, due to ultra fine grain size and the leading microstructure of its bainite and martensite of base metal, HAZ is softening can even be occurred under medium welding heat input.Hardness in HAZ and the reduction of intensity are the thin spot through the pipeline configuration of welding.Therefore,, according to the character of base material and welding conditions, it is important limiting this softening degree occurring.About the softening field that is subject to maximum research of HAZ, be high-strength medium plate, for example, for pipe applications, and the AHSS applying for automobile more in the recent period.
WO2007/129676 relates to the hot pressing steel part of being manufactured by high-carbon cold-rolled steel sheet material, this steel sheets by austenitizing, hot pressing to produce steel part and to be quenched to realize the minimum tensile strength of 1.8GPa.Treat that cold rolling hot-rolled steel contains at least 50% ferrite.
EP2028284 discloses weldless steel tube and EP1662014 discloses low-carbon hot-rolling steel board, and it is batching between 450～650 ℃ and is again being heated to rapidly subsequently between 550～750 ℃ to realize three-phase ferrite, bainite and island martensite body tissue.
The object of the invention is to realize high-strength hot-rolled steel band, it is not easy to HAZ-than present obtainable high-strength hot-rolled steel band and softens.
Aspect first, by have improvement the softening resistivity of HAZ the steel band of hot-rolled high-strength microalloying reached this object, the thickness that it has between 2～16mm, has the microstructure that comprises martensite, tempered martensite and/or bainite, and wherein this steel contains in % by weight:
● 0.07～0.30% C;
● 0.8～2.0% Mn;
● 0.01～0.08% Al
sol;
● 0.2～1.5% Cr;
● 0.1～0.7% Mo;
● 0.0005～0.005 B;
● 0.01～0.07% Nb;
● maximum 0.5% Si;
● maximum 0.03% P;
● maximum 0.015% S;
● maximum 0.05% Ti;
● maximum 0.1% V;
● maximum 0.2% Cu;
● maximum 0.2% Ni;
● maximum 0.008% N;
● optionally maximum 0.015% the calcium of controlling for sulphide shape adds;
● other elements of the amount in impurity level, surplus is iron;
The yield strength of this steel band is 960MPa at least.
All composition % all provide with % by weight, unless otherwise specified.
Thinking of the present invention is based on the following fact, by selecting the combination of the chemical element of described amount, and the particularly existence of niobium and molybdenum, can keep good sclerosis.Due to low manganese and carbon content, during castingprocesses, structure of steel is not critical for the segregation of manganese and carbon.The verify local relief of the coiling temperature in band of this rigidity is not critical, and it has promoted steel production, and the homogeneity of its mechanical properties is had to advantageous effect, and this has active influence to the planeness of the finished product and unrelieved stress again.This steel sheets height is applicable to welding and laser cutting, and it has good fatigue strength simultaneously, is not subject to described Effects of Heat Treatment.And, this steel sheets there is excellent bending property, good impelling strength and when tempering to softening good resistivity.Subsequently, the obtainable existence of separating out element for the solution of separating out of the cooling period of HAZ after welding guaranteed HAZ soften resistivity obvious improvement.
Can be for example by laser by the steel thermal cutting according to the present invention fixed shape of fidelity that is as the criterion.Observed and in laser cutting article, realized remarkable level and smooth cutting surfaces.On the other hand, strength difference (this region is located close to hardened zone) between the base material He Ruan district that has found to produce in the cutting process of technology is little or non-existent, and this is also due to the obtainable existence of separating out element for the solution of separating out subsequently of the cooling period after this thermal cutting.These have favorable influence to fatigue strength jointly.In addition, relatively low carbon content has reduced the peak hardness of hardened zone, and though make the processing of article or in actual use this cutting surfaces to embrittlement and cracking insensitive.
Aspect control intensity, carbon is important element, but need to be not limited to a certain degree to provide the well balanced of toughness, welding property and processability.Between this C content is remained to relatively low 0.07～0.30% to realize good toughness (all composition % all represent with % by weight).Be combined with low temperature coiling temperature, this microstructure will contain martensite and/or bainite.Definite amount depends on composition, the rate of cooling on runoff table and coiling temperature strongly.Under relatively low C content, this Ms temperature will be quite high, and therefore, martensite is self-tempering to a certain extent.According to requirement of strength, found suitable carbon window.For having at least steel of the yield strength of 960MPa, preferably carbon content is at least 0.07 and/or maximum 0.13%.For thering is at least steel of the yield strength of 1100MPa, carbon content is preferably at least 0.13 and/or maximum 0.18%, and for having at least steel of the yield strength of 1300MPa, carbon content is preferably at least 0.19%, more preferably between at least 0.23 and/or maximum 0.30%.
Suitable greatest carbon content is 0.27%, or even 0.25%.
The element of picture manganese, chromium, molybdenum and boron, provides the hardenability that promotes bainite and/or martensitic formation.This manganese content is restricted to 0.8～2.0%.When manganese surpasses this upper limit, the risk of segregation becomes obviously, and this can deleteriously affect the homogeneity of microstructure.During lower than 0.8% level, to the effect of hardenability, be inadequate.Suitable minimum manganese level is 1.1%.
Add boron to promote hardenability.The formation of avoiding boron nitride is important, because it will make boron invalid for the raising of hardenability.According to the titanium in composition of the present invention act as protection boron because Ti forms titanium nitride, and therefore do not form BN.The amount of the boron of alloying is 0.0005%B (being 5ppm) at least, but is no more than 0.005%B (being 50ppm) to reduce grain-size and to improve hardenability.If add titanium as alloy element, the amount of titanium is generally at least 0.01%Ti, but is no more than 0.05%, with in conjunction with nitrogen N and prevent the generation of boron nitride BN.Within the scope of the invention alternative is to come in conjunction with nitrogen with aluminium, and protects thus boron.For example, in the situation that the formation of TiN particle is regarded as not needing (because they to the summer than the effect of toughness), by aluminium, protect free boron to can be preferred selection.
During hot rolling, niobium analyzes at austenite middle part, and the retardation by austenitic recrystallize has contribution to the grain refining of the microstructure of final transformation thus.In addition, be retained on the turn the niobium in solution, particularly under rate of cooling, to reducing transition temperature, there is strong effect faster, so it be also favourable for hardenability.Under low coiling temperature (500 ℃ of <), expection niobium is little by the contribution of precipitation strength, because this temperature is too low for separating out of thin NbC.Suitable Nb content is at least 0.02%, preferably at least 0.025%.
In this case, V has the effect similar but not stronger with Nb.But the major cause of the interpolation of Nb and V is to improve the softening resistivity of HAZ-.In the relevant portion of HAZ, thermal cycling has made to reach the temperature allowing by the precipitation strength of Nb and V, has therefore caused the increase of hardness, and this is because coiling temperature by low remains on separating out of element in solution.It is believed that main contribution is produced by Nb and V carbide, nitride or carbonitride.On compared with low degree, think and can form the MoC precipitate with similar effect.If existed, suitable minimum V content is 0.04%.
According to steel of the present invention, be aluminium deoxidation or aluminium-silicon killed steel, so that oxygen level is down to minimum value, to do not react between carbon and oxygen at solidificating period.Therefore the amount that is added into the aluminium of steel at production period comprises need to be for those of deoxidation.The amount keeping in the finished product is (also referred to as soluble aluminium (Al
sol)) be 0.01～0.08%Al.In the context of the present invention, aluminium content means soluble aluminium.
Except aluminium, silicon also serves as reductor in steel of the present invention.It start from approximately at least 0.10%Si and at the most 0.50%Si also serve as solution strengthening thing, this On Impact Toughness and processing characteristics have useful effect.Higher than 0.5%, the surface quality that silicon deleteriously affects steel is to unacceptable degree, and is accompanied by the silicone content increasing, and the removal of the hot rolling iron scale by pickling becomes more difficult.
The phosphorus P as impurity comprising should be for maximum 0.03%, and sulphur S should be even lower, and should be restricted at most 0.015%, this means and limit these content to realize good impelling strength and bending property.When if desired, the cored wire that contains Ca-Si or Ca-Fe (Ni) by employing is processed this melt and can be improved further performance.During calcium is processed, due to surface tension effects, aluminum oxide and silicon oxide inclusion are converted into calcium-aluminate and the silicate of the spherical form of melting.The calcium-aluminate inclusion of staying in molten steel has suppressed the formation of MnS hairline (stringer) at the solidificating period of steel.The composition of separating out of steel solidificating period Sulfide inclusion and this variation of pattern aspect are called oxide morphology or sulphide shape is controlled.This has caused spray nozzle clogging less during casting, and mechanical property, produces point because the long MnS hairline stretching serves as crackle preferably.The Ca that the general quantity of the calcium of the steel of controlling for sulphide shape is 0.0015～0.015%.Suitable maximum value is 0.005% Ca.
Chromium should be 0.2～1.5%.Molybdenum should be preferably 0.1%Mo～0.7%Mo.Add two kinds of elements to improve sclerosis and tempering resistivity.This makes separating out under higher coiling temperature become possibility, and can use it for and reduce and even prevent the softening of steel, and for alleviating the intensity fluctuation causing because local temperature difference is different due to the cooling period at coiled material.Suitable minimum molybdenum content is 0.15%.
Consider the cosmetic issue relevant to copper, preferably avoid with steel through being usually used in this strength level in element copper and mickel alloying for example.Because often copper is carried out to alloying to alleviate the harmful effect of copper, so this also needs in conjunction with nickel.Therefore preferably nickel and/or copper exist or more preferably do not exist completely with maximum impurity level.
According to the microstructure of steel of the present invention, be characterized as being the microstructure mainly being formed by tempered martensite, it is characterized in that the little carbide in Widmannstatten structure and/or bainite.Ideally, this microstructure is not containing ferrite and pearlite composition, because these will deleteriously affect strength level to be reached.In fact, perhaps the ferrite that has some small pieces is inevitably, but this amount can be no more than the obvious level that affects strength level.Should be by form under high transition temperature above-described harmful and the ferrite part of unwanted ferrite composition and the bainite forming under low transition temperature or ferrite side plate or acicular ferrite are known and separated subsequently.The former composition is unwanted, and the latter is not.
The hot-rolled steel band of the present invention that direct heat can be rolled to 2mm～16mm thickness is prepared as wear-resisting and has different SMYSs.Only by change to analyze within the scope of the invention and/or the rear rolling rate of cooling of band and/or batch before temperature, on market, general threshold value is 960,1100 and 1300MPa.Also can be by this kind of High Yield Stress Steel for target, the common desired performance of organization need structure iron in this target, for example good processing characteristics, welding property and impelling strength, this means that hot-rolled steel band according to the present invention also can shape as welding structure iron.In the steel that makes an explanation being analyzed in the following description book, all content % are % by weight, and the surplus of steel is iron Fe and inevitable impurity, unless otherwise defined.Even, for the one-tenth-value thickness 1/10 of the tropocal wood of 16mm at the most, also can reach the value of 960MPa.For the value of 12mm at the most, can reach 1100 and the value of 1300MPa.Higher thickness has caused lower rate of cooling to a certain extent, and has therefore caused the austenite of the less enrichment before changing mutually.This causes some lower strength level, means and adopts these poor compositions, and the tropocal wood that surpasses 12mm for thickness can not obtain S1100 or S1300 level.Preferably, minimum thickness is that 3mm and/or maximum ga(u)ge are 10mm.It should be noted that the intensity level as defined is in the present invention (being that tension specimen (by direction of motion of milling train) on the longitudinal direction of this band is obtained) measured in a longitudinal direction.Value in a lateral direction (being that tension specimen is obtained on the width of this band) may be different from value in a longitudinal direction, and conventionally than these height in intensity on longitudinal direction, and low on unit elongation.
In one embodiment, the carbon content of steel is 0.07～0.13%, and yield strength is 960MPa at least.
In one embodiment, the carbon content of steel is 0.13～0.18%, and yield strength is 1100MPa at least.
In one embodiment, wherein carbon content is at least 0.19%, and preferably between 0.23～0.30%, and yield strength is 1300MPa at least.
According to the suitable ultimate tensile strength of hot-rolled steel of the present invention, be 1700MPa.
According to second aspect, the present invention is embodied in the method for the preparation of the steel band of hot-rolled high-strength microalloying, this steel band has the thickness between 2～16mm, there is the softening resistivity of HAZ-of improvement and the yield strength of 960MPa at least, there is the microstructure that comprises martensite, tempered martensite and/or bainite, and wherein this steel contains in % by weight:
● 0.07～0.30% C;
● 0.8～2.0% Mn;
● 0.01～0.08% Al
sol;
● 0.2～1.5% Cr;
● 0.1～0.7% Mo;
● 0.0005～0.005 B;
● 0.01～0.07% Nb;
● maximum 0.5% Si;
● maximum 0.03% P;
● maximum 0.015% S;
● maximum 0.05% Ti;
● maximum 0.1% V;
● maximum 0.2% Cu;
● maximum 0.2% Ni;
● maximum 0.008% N;
● optionally maximum 0.015% the calcium of controlling for sulphide shape adds;
● with other elements of the amount of impurity level, surplus is iron.
This band is higher than Ar
3at temperature, carry out hot finishing, wherein the method comprises at least following steps:
● the final thickness of finish rolling to 2～16mm
● in maximum 10 seconds of the hot rolling pass from last, take the rate of cooling that to be enough to the Microstructural through rolling be the microstructure that comprises martensite and/or bainite, the coiling temperature of cooling this hot rolled band to 20～500 ℃.
This hot rolling technology is conventional hot rolling technology, no matter be the slab (being conventional continuous casting steel billet) from having the thickness of 150～350mm, or or starts lower than 150 (be sheet blank continuous casting or even Strip casting).Preferably steel during still for austenite finish rolling to provide, there is compact grained steel, and provide thus good impelling strength.Preferably coiling temperature is the low mechanical properties needing with realization.Preferably coiling temperature is lower than 400 ℃.By rapid cooling or direct quenching after hot rolling, the steel of preparation the type, has obtained excellent impelling strength, because occur from compact grained, phase transformation through the austenite of processing to martensite and/or bainite.It has also improved surface quality, because removed initial iron scale in scale breaker before rolling.And, do not need the additional annealing of very expensive length to process to dissolve all precipitates.In tropocal wood rolling line, in reheating furnace, reheat the warm rangeability of this slab to 1100 for the treatment of rolling～1250 ℃, and keep several hours.In this case, particular carbon compound is the dissolving of Cr and Mo carbide for example, and the homogenizing of tissue is as far as possible thoroughly.On the other hand, the growth of the austenite crystal under high Heating temperature does not make the finished product more crisp because the sluggishness first by the austenitic transformation during the recrystallize during the high temperature rolling in the starting stage of the operation of rolling and the thermo-mechanical rolling in the final stage of course of hot rolling cause the deformed austenite crystal grain that forms transformation refinement austenite crystal.Cooling period on runoff table, the austenite crystal of gross distortion changes very thin transmutation product into.This causes the high yielding stress of being combined with excellent impelling strength.If use sheet blank continuous casting and Direct Rolling facility (wherein element is not even also separated out as Cr and Mo carbide before rolling starts), preparation cost and production time also can further reduce.
According to the present invention, at steel, be still austenite, higher than Ar
3finishing temperature under this steel is made to final hot rolling thickness.Band cooling is not later than beginning in 10 seconds after last hot rolling pass, and it fully fast coolingly be take to allow austenitic transformation be bainite and/or martensitic microstructure, rate of cooling is preferably at least 30 ℃/s, be reduced to the coiling temperature of 20～500 ℃, be preferably reduced to the coiling temperature of 20～450 ℃.The result obtaining is generally nearly complete bainite and/or martensitic microstructure, makes bainite and/or martensite content be preferably at least 90 volume %, preferably at least 95 volume %.This microstructure also, preferably not containing the ferrite at high temperature forming and not containing perlite composition, therefore makes microstructure substantially be entirely bainite/martensite, and wherein for this purpose, ferrite side plate or acicular ferrite are considered to bainite structure.In the coiling temperature scope lower than 100 ℃, not by martenaging martempering, although under these low temperature, for low-carbon (LC) grade, but there are some self-temperings, and when coiling temperature is during at least 100 ℃, martensite is by tempering.At the temperature higher than 200 ℃, martensite is precipitated by tempering and this carbon.
In preferred embodiments, for the steel that contains maximum 0.12% carbon content, coiling temperature is maximum 450 ℃, and more preferably 425 ℃, the steel for containing at least 0.13% carbon content, is maximum 275 ℃, more preferably 250 or 225 ℃.
In one embodiment, the acceleration cooling period after hot rolling and before batching, rate of cooling is 5～100 ℃/s.
In one embodiment, final rolling temperature is higher than Ar
3and also lower than 920 ℃, and preferably also lower than 900 ℃.
According to the 3rd aspect, the production by steel according to the present invention for automobile, truck, shipbuilding, construction work, heave-load device, earth-moving equipment or liftmobile parts.
Utilize following non-limiting example further to explain the present invention.Table 1 has shown kind S700, S960, and the steel of each of S1100 and S1300 forms.
The composition of table 1. steel (except B and N(ppm), all in % by weight * 1000.All steel are all processed through Ca, imp=impurity level)
SEM microstructure shows that all hot-rolled steel samples all have the microstructure being mainly comprised of tempered martensite, are characterised in that the little carbide in Widmannstatten structure.High M due to these relatively low C steel
stemperature, and also owing to being used for simulating, batch cooling Slow cooling, therefore will cause martensitic tempering.The pattern of carbide that has shown several variants of the orientation relationship between carbide and matrix, is characterised in that tempered martensite.Austenite grain boundary is before also visible, and has shown some extension along rolling direction, as used optics metallographicobservation to arrive.Strength level depends on coiling temperature (referring to Fig. 1 of S1100 material and Fig. 2 of S1300 material) strongly, and it can be understood with reference to the needed microstructure being mainly comprised of tempered martensite.
Fig. 3 has shown the HAZ ramollescence in Y-axis according to steel of the present invention (a, c) and comparative steel (b, d).Clearly visible, with regard to the reduction of HAZ softening, steel of the present invention has surpassed comparative steel.Steel b and d are respectively S960-Nb and S960+Cr-Nb(referring to table 1), and a and c are respectively S960 base and S960+V.
Claims (12)
1. hot-rolled high-strength microalloy steel band, the thickness that it has 2～16mm, has the softening resistivity of HAZ-of improvement, have the microstructure that comprises martensite, tempered martensite and/or bainite, and wherein this steel contains in % by weight:
● 0.07～0.30% C;
● 0.8～2.0% Mn;
● 0.01～0.08% Al
sol;
● 0.2～1.5% Cr;
● 0.1～0.7% Mo;
● 0.0005～0.005 B;
● 0.01～0.07% Nb;
● maximum 0.5% Si;
● maximum 0.03% P;
● maximum 0.015% S;
● maximum 0.05% Ti;
● maximum 0.1% V;
● maximum 0.2% Cu;
● maximum 0.2% Ni;
● maximum 0.008% N;
● optionally maximum 0.015% the calcium of controlling for sulphide shape adds;
● other elements of the amount of impurity level, surplus is iron;
The yield strength of this steel band is 960MPa at least.
2. according to the steel of any one of aforementioned claim, it has at least 0.2% chromium content.
3. according to the steel of any one of aforementioned claim, it has the nickel content in impurity level.
4. according to the steel of any one of aforementioned claim, it has the copper content in impurity level.
5. according to the steel of any one of aforementioned claim, wherein carbon content is 0.07～0.13%, and has at least yield strength of 960MPa.
6. according to the steel of any one of claim 1～4, wherein carbon content is 0.13～0.18%, and it has at least yield strength of 1100MPa.
7. according to the steel of any one of claim 1～4, wherein carbon content is at least 0.19%, is preferably 0.23～0.30%, and has at least yield strength of 1300MPa.
8. the method for preparing hot-rolled high-strength microalloy steel band, this steel band has the thickness of 2～16mm, the softening resistivity of HAZ-with improvement, the yield strength of 960MPa at least, there is the microstructure that comprises martensite, tempered martensite and/or bainite, and wherein this steel contains in % by weight:
● 0.07～0.30% C;
● 0.8～2.0% Mn;
● 0.01～0.08% Al
sol;
● 0.2～1.5% Cr;
● 0.1～0.7% Mo;
● 0.0005～0.005 B;
● 0.01～0.07% Nb;
● maximum 0.5% Si;
● maximum 0.03% P;
● maximum 0.015% S;
● maximum 0.05% Ti;
● maximum 0.1% V;
● maximum 0.2% Cu;
● maximum 0.2% Ni;
● maximum 0.008% N;
● optionally maximum 0.015% the calcium of controlling for sulphide shape adds;
● other elements of the amount of impurity level, surplus is iron;
Higher than Ar
3at temperature, by this band hot finishing, wherein the method at least comprises the following steps:
● the final thickness of finish rolling to 2～16mm;
● after last hot rolling pass, in maximum 10 seconds, take the rate of cooling that to be enough to rolling Microstructural be the microstructure that comprises martensite and/or bainite, hot rolled band is cooled to the coiling temperature of 20～500 ℃.
9. method according to Claim 8, wherein coiling temperature is:
● for the steel that contains maximum 0.12% carbon content, maximum 450 ℃, or
● for the steel that contains at least 0.13% carbon content, maximum 275 ℃.
10. the method for according to Claim 8～9 any one, wherein the rate of cooling of the cooling period of the acceleration after hot rolling and before batching is 5～100 ℃/s.
The method of 11. according to Claim 8～10 any one, wherein final rolling temperature is higher than Ar
3and also lower than 920 ℃, and preferably also lower than 900 ℃.
12. according to the steel of claim 1～7 purposes in the production of the parts of automobile, truck, heave-load device, earth-moving equipment or liftmobile.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP11173383.8 | 2011-07-10 | ||
| EP11173383 | 2011-07-10 | ||
| PCT/EP2012/063515 WO2013007729A1 (en) | 2011-07-10 | 2012-07-10 | Hot-rolled high-strength steel strip with improved haz-softening resistance and method of producing said steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103649355A true CN103649355A (en) | 2014-03-19 |
| CN103649355B CN103649355B (en) | 2016-08-17 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201280034223.9A Active CN103649355B (en) | 2011-07-10 | 2012-07-10 | Have the HAZ-of improvement soften repellence hot-rolled high-strength steel band and the method that produces described steel |
Country Status (3)
| Country | Link |
|---|---|
| EP (1) | EP2729590B1 (en) |
| CN (1) | CN103649355B (en) |
| WO (1) | WO2013007729A1 (en) |
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| CN109680211A (en) * | 2018-12-28 | 2019-04-26 | 首钢集团有限公司 | A kind of manufacturing method of vehicle structure steel and its manufacturing method and automobile structure |
| CN113106336A (en) * | 2021-03-17 | 2021-07-13 | 唐山钢铁集团有限责任公司 | Ultrahigh-strength dual-phase steel capable of reducing softening degree of laser welding head and production method thereof |
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| CN113106336A (en) * | 2021-03-17 | 2021-07-13 | 唐山钢铁集团有限责任公司 | Ultrahigh-strength dual-phase steel capable of reducing softening degree of laser welding head and production method thereof |
| CN113106336B (en) * | 2021-03-17 | 2022-06-10 | 唐山钢铁集团有限责任公司 | Ultrahigh-strength dual-phase steel capable of reducing softening degree of laser welding head and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2729590A1 (en) | 2014-05-14 |
| WO2013007729A1 (en) | 2013-01-17 |
| CN103649355B (en) | 2016-08-17 |
| EP2729590B1 (en) | 2015-10-28 |
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