CN101802233A - Dual phase steel, by the flat product of this dual phase steel preparation and the method for preparing flat product - Google Patents
Dual phase steel, by the flat product of this dual phase steel preparation and the method for preparing flat product Download PDFInfo
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- CN101802233A CN101802233A CN200880103426A CN200880103426A CN101802233A CN 101802233 A CN101802233 A CN 101802233A CN 200880103426 A CN200880103426 A CN 200880103426A CN 200880103426 A CN200880103426 A CN 200880103426A CN 101802233 A CN101802233 A CN 101802233A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12951—Fe-base component
- Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
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Abstract
The invention provides dual phase steel, by the flat product of this dual phase steel preparation, and preparation method thereof, this flat product for example is a metal sheet.Except intensity with 950MPa at least and good deformable performance, this dual phase steel also has certain surface smoothness, make under the condition that adopts simple preparation method, the flat product that is equipped with by this steel is under the state of coating not or be provided with under the state of anticorrosive coating and can form the complicated parts that are shaped, such as bodywork component.The realization of this target is: steel of the present invention is by 20% to 70% martensite, 8% retained austenite and the ferrite and/or the bainite of surplus constitute at the most, and contain (in weight %): carbon: 0.10% to 0.20%, silicon: 0.10% to 0.60%, manganese: 1.50% to 2.50%, chromium: 0.20% to 0.80%, titanium: 0.02% to 0.08%, boron:＜0.0020%, molybdenum:＜0.25%, aluminium:＜0.10%, phosphorus :≤0.2%, sulphur :≤0.01%, nitrogen :≤0.012%; And the iron of surplus and unavoidable impurities.This metal sheet can be used as hot rolling band or cold rolling strap and uses.This metal sheet preferably has greater than 10% unit elongation with greater than the yield-point of 580MPa.
Description
The present invention relates to a kind of dual phase steel, it is organized basically and is made of the bainite under martensite and ferrite and each the corresponding situation, and may have the retained austenite part, and this dual phase steel has the tensile strength of 950MPa at least.The invention still further relates to by the flat product of this dual phase steel preparation and the method for preparing this flat product.
Common name used herein " flat product " generally includes and meets such steel band of the present invention and steel plate.
Need such steel in the body construction field, it has high strength and low weight on the one hand, also has good deformability on the other hand.Knownly carried out the characteristic combination of many trials during steel with these contradictions in preparation.
For example, patent documentation EP 1 431 107 A1 have disclosed and have a kind ofly not only had effective deep draw performance but also have steel, the flat product prepared therefrom of high tensile strength and prepare the method for described flat product.Except iron and unavoidable impurities, this known steel also contains (in weight %): 0.08% to 0.25% carbon, 0.001% to 1.5% silicon, 0.01% to 2.0% manganese, 0.001% to 0.06% phosphorus, 0.05% sulphur, 0.001% to 0.007% nitrogen and 0.008% to 0.2% aluminium at the most.Simultaneously, its average r value should be at least 1.2, be at least 1.3 in the r value on the rolling direction, becoming with respect to rolling direction 45 the degree directions on the r value be at least 0.9 and the cross-web direction in rolling direction on the r value be at least 1.2.In this known steel, the intensity enhancing effect is caused that by silicon with regard to effective coating performance of steel, having selected is the upper limit of 1.5 weight %.Emphasized that in addition manganese has active influence to intensity.In this respect, the upper limit of manganese content is set to 1.5%, this is because any value that exceeds this upper limit all can be accompanied by the reduction of r value, in order to optimize the r value of this known steel plate, the scope of manganese content is 0.04 weight % to 0.8 weight %, especially is that 0.04 weight % to 0.12 weight % is considered to favourable.
In order further to improve the intensity of described known steel, except the alloying element that other selectivity are added, can also be able to randomly contain: content is the boron of 0.0001 weight % to 0.01 weight %; Total content is titanium, niobium and/or the vanadium of 0.001 weight % to 0.2 weight %; And total content is tin, chromium, copper, nickel, cobalt, tungsten and/or the molybdenum of 0.001 weight % to 2.5 weight %.Because cost, the total content of these elements is restricted to each described upper limit.
If the steel described in the patent documentation EP 1431407A1 has the intensity above 850MPa, then they no longer have duplex structure, on the contrary, and they only organize by martensite or only constitute by the bainite under ferrite and each the corresponding situation.In addition, patent documentation EP 1,431 407 A1 do not provide such example, wherein when having minor amount of silicon or high-load relatively manganese, and the effect that can duplicate (for example) chromium, molybdenum, titanium or boron.On the contrary, the example that patent documentation EP 1 431 407 A1 provide proves: according to the prior art, intensity is suitably to cooperate by the Steel Alloy under the corresponding situation with each of the content that makes manganese and silicon to adjust basically.
Disclosed the feasible method of other preparation flat product among patent documentation EP 1 200 635 A1, wherein said flat product is made of high-intensity relatively dual phase steel, even and still have the favorable mechanical technical characteristic afterwards in experience annealing process (comprise overaging handle).The method of learning from the document, the steel band or the steel plate that mainly have ferrite-martensitic stucture have been prepared, wherein ratio of martensite is 4% to 20%, except iron with molten cause impurity, this steel band or steel plate also comprise (in weight %): 0.05% to 0.2% carbon, 1.0% silicon, 2.0% manganese, 0.1% phosphorus, 0.015% sulphur, 0.02% to 0.4% aluminium, 0.005% nitrogen, 0.25% to 1.0% chromium, 0.002% to 0.01% boron at the most at the most at the most at the most at the most.Ratio of martensite under each corresponding situation in the steel preferably adds up to about 5% to 20% of main martensite-ferrite tissue.Zhi Bei flat product has 500N/mm at least by this way
2Intensity, have good crystallized ability simultaneously, and need not to require for this purpose high-load especially specific alloy elements.
In the situation of the described steel of patent documentation EP 1 200 635 A1,, utilized the conversion influence of element boron in order to improve intensity.In this known steel, the effect that boron improves intensity is guaranteed in the following manner, wherein at least a alternative nitride organizer (preferred aluminium and additional titanium) is added in the steel.The effect that adds titanium and aluminium is in conjunction with nitrogen contained in the steel, makes boron can be used for forming the carbide that improves hardness.Under the support of the essential chromium content that exists, obtained the strength level higher by this way than similar steel.Yet the maximum strength of the steel of exemplary description is in each case all less than 900MPa among the patent documentation EP 1 200 635.
At last, patent documentation EP 1 559 797 A1 have disclosed a kind of high-intensity relatively dual phase steel, its tissue contains and surpasses 60% ferrite, 5% to 30% martensite, and, also comprise (in weight %) except iron and unavoidable impurities: 0.05% to 0.15% carbon, 0.5% silicon, 1% to 2% manganese, 0.01% to 0.1% aluminium, 0.009% phosphorus, 0.01% sulphur and 0.005% nitrogen at the most at the most at the most at the most.In order further to improve the intensity of this known steel, can be to wherein adding 0.01% to 0.3% molybdenum, 0.001% to 0.05% niobium, 0.001% to 0.1% titanium, 0.0003% to 0.002% boron and 0.05% to 0.49% chromium.The described known steel of alloying and acquisition has the tensile strength up to 700MPa by this way, and has good deformability and surface smoothness.Improvement described in patent documentation EP 1 559 797 A1 its objective is the mechanical characteristics of improving this steel, avoids the alloying of a large amount of relatively alloying element (such as silicon very crucial for surface smoothness, weldability and deformability, phosphorus and aluminium) simultaneously.
At the background of above-mentioned prior art, the objective of the invention is to develop steel and the flat product prepared therefrom that a kind of intensity is at least 950MPa and has good deformability.In addition, described steel should have certain surface smoothness, make and adopting under simple preparation method's the condition that the flat product that is equipped with by this steel is under the state of coating not or be provided with under the state of anticorrosive coating and can be deformed into the complicated parts that are shaped, such as bodywork component.In addition, also provide a kind of method that can easily prepare the flat product that obtains in the above described manner.
About this material, reached this purpose by the dual phase steel described in the claim 1 according to the present invention.In being subordinated to the claim of claim 1, set forth the favourable embodiment of this steel.
According to claim 20 of the present invention, a kind of flat product that has reached above-mentioned purpose is characterised in that it is made of such steel, and described steel constitutes according to the present invention and obtains.
At last, about the preparation method, reached above-mentioned purpose according to the present invention by the preparation method described in claim 26 and 27, wherein, method described in the claim 26 is relevant with the preparation of hot rolling band of the present invention, and the program technic described in the claim 27 is relevant with the preparation of cold rolling strap of the present invention.The claim of quoting claim 26 and 27 comprises the favourable variant form of the inventive method respectively.In addition, implement method of the present invention and the variant form thereof described in the claim, will be described particularly advantageous embodiment below for reality.
Steel of the present invention is characterised in that high strength with 950MPa at least, particularly has high strength above 980MPa and the conventional intensity that has also reached 1000MPa and Geng Gao.Simultaneously, this steel has the yield strength of 580MPa at least, particularly has the yield strength of 600MPa at least, and has at least 10% unit elongation A
80
Because the combination of high strength and good deformability, thus steel of the present invention be particularly suitable for preparing complicated that be shaped, to bear heavily stressed parts in actual use, required those in the body construction field for example.
Because steel of the present invention has duplex structure, so it has high strength, has favorable extensibility simultaneously.Like this, the alloy of steel of the present invention is so constructed, and makes its ratio of martensite be at least 20%, preferably surpasses 30%, and is maximum to 70%.Simultaneously, retained austenite part at the most 8% can be favourable, and maximum 7% or lower retained austenite ratio still less normally preferred.The remainder of the tissue of dual phase steel of the present invention is made of ferrite and/or bainite (bainite ferrite+carbide) respectively.
By regulating duplex structure, high strength and good elongation property have been obtained according to the present invention.This is to carry out close limit ground by the content to the various alloying elements except iron and unavoidable impurities that exist in the steel of the present invention to select to realize.
Like this, regulation carbon content of the present invention is 0.10 weight % to 0.20 weight %.Minimum carbon content is selected as 0.10 weight % so that can form the martensitic stucture with enough hardness, and regulates the desired characteristic combination of steel of the present invention.Yet if content surpasses 0.20 weight %, carbon can suppress the formation of desired ferrite/bainite tissue part.Higher carbon content also has negative influence to the welding suitability, and for example this is tangible especially for material of the present invention for the automotive engineering Application for Field.When the carbon content of steel of the present invention is 0.12 weight % to 0.18 weight %, during in particular for 0.15 weight % to 0.16 weight %, can utilizes the advantageous effect of the carbon in the steel of the present invention in mode especially reliably.
In addition, silicon has played the effect that improves intensity by sclerosis ferrite or bainite in steel of the present invention.In order to utilize this effect, stipulate that minimum silicone content is 0.10 weight %, when the silicone content of steel of the present invention at least 0.2 weight %, particularly during at least 0.25 weight %, silicon is brought into play its effect in reliable especially mode.Consider the following fact: the flat product that is equipped with by steel of the present invention will have the surface smoothness that is suitable for further processing most, and the coating that will be suitable for applying most if necessary, and then the upper limit of silicone content is set to 0.6 weight % simultaneously.Should go up in limited time when observing, the risk of grain boundary oxidation also minimizes.Be limited to 0.4 weight %, particularly 0.35 weight % by silicone content, even can avoid the disadvantageous effect of silicon more reliably the characteristic of steel of the present invention with steel of the present invention.
The manganese content of steel of the present invention is in the scope of 1.5 weight % to 2.50 weight %, in particular for 1.5 weight % to 2.35 weight %, to utilize the intensity raising effect of this element.Like this, the existence of manganese has promoted martensitic formation.If cold rolling strap is equipped with by steel of the present invention, and described cold rolling strap is in processing latter stage annealing, then suppressed to form perlite in the process of cooling after annealing according to manganese content given to this invention.When manganese content during, can utilize these active effects that manganese was produced that exist in the steel of the present invention in mode especially reliably at least 1.7 weight %, in particular at least 1.80 weight %.Yet for fear of the negative influence of manganese for deformability, welding suitability and coating performance, the upper limit of manganese content in steel of the present invention is set to 2.5 weight %.By manganese content being limited to 2.20 weight %, particularly 2.00 weight %, can get rid of manganese more reliably for the issuable negative influence of steel of the present invention.
Content is that the chromium of 0.2 weight % to 0.8 weight % also has intensity raising effect in dual phase steel of the present invention.When chromium content at least 0.3 weight %, particularly during at least 0.5 weight %, this effect is particularly evident.On the other hand, the chromium content of steel of the present invention is limited to 0.8 weight % simultaneously, with the risk of reduction grain boundary oxidation, and guarantees that steel of the present invention has good elongation property.In addition, should go up in limited time, obtain effectively to be provided with the surface of metal cover when observing.When the upper limit with the chromium content of steel of the present invention is set at maximum 0.7 weight %, particularly during 0.6 weight %, especially can avoids the negative influence of chromium content.
Content also helps to improve the intensity of steel of the present invention for the existence of the titanium of at least 0.02 weight %, because it forms meticulous TiC or Ti (C, N) settling and help grain refining.The other active effect of titanium is in conjunction with the nitrogen that may exist, thereby prevents to form boron nitride in steel of the present invention.These materials will bring very strong negative influence to the elongation property and the deformability of flat product of the present invention.Therefore, when adding boron when improving intensity, the existence of titanium guarantees that also boron can give full play to its effect.For this reason, can be advantageously, the add-on of titanium is greater than 5.1 times (that is, titanium content＞1.5 (3.4 * nitrogen contents)) of the nitrogen content under each corresponding situation.Yet too high titanium content causes high recrystallization temperature unfriendly, and when being equipped with final the treatment stage annealed flat cold-rolled bar product by steel of the present invention, this has passive especially influence.For this reason, the upper limit of titanium content is restricted to 0.08 weight %, particularly 0.06 weight %.When titanium content is 0.03 weight % to 0.055 weight %, particularly during 0.040 weight % to 0.050 weight %, can utilizes the active effect that characteristic produced of titanium for steel of the present invention in mode especially reliably.
By can randomly provide according to the present invention, content mostly is the boron of 0.002 weight % most, also can improve the intensity of steel of the present invention, situation when adding manganese, chromium and molybdenum respectively is the same, and when being equipped with cold rolling strap by steel of the present invention, critical cooling rate reduces after annealing.For this reason, according to the embodiment that especially has the guide effect put into practice of the present invention, boron content is at least 0.0005 weight %.Yet too high boron content can reduce the deformability of steel of the present invention simultaneously, and influences the formation of the desired duplex structure of the present invention unfriendly.Therefore, be 0.0007 weight % to 0.0016 weight % at content, particularly during 0.0008 weight % to 0.0013 weight %, the effect of optimum boron is provided in steel of the present invention.
Similar boron or chromium in above-mentioned content range, the molybdenum content that can randomly exist according to the present invention also helps to improve the intensity of steel of the present invention.In this respect, rule of thumb, the existence of molybdenum does not have negative influence for coating performance or its extension performance of the flat product that coats with metal cover.Actual tests shows, and content is up to 0.25 weight %, particularly during 0.22 weight %, can effectively utilizes the positive influence of molybdenum especially, considers it also is like this from economic point of view.Therefore, in addition content be that the molybdenum of 0.05 weight % also has active effect to the characteristic of steel of the present invention.If exist other intensity of q.s to improve element, then when molybdenum content be 0.065 weight % to 0.18 weight %, particularly during 0.08 weight % to 0.13 weight %, molybdenum produces desired effect particularly evidently in steel of the present invention.Yet if steel of the present invention contains the molybdenum that is less than 1.7 weight % and/or is less than the chromium of 0.4 weight %, the molybdenum that advantageously adds 0.05 weight % to 0.22 weight % has desired intensity to guarantee steel of the present invention.
When steel of the present invention is melted, come deoxidation and in conjunction with the nitrogen that may contain in the steel with aluminium.For this reason, if desired, can in steel of the present invention, add the aluminium that content is less than 0.1 weight %, when its content is in the scope of 0.01 weight % to 0.06 weight %, particularly 0.020 weight % to 0.050 weight %, can make aluminium produce desired effect in reliable especially mode.
In steel of the present invention, for fear of the formation of boron nitride, the content of nitrogen only allows for and is up to 0.012 weight % when particularly having boron at the same time.No longer validly as microalloy element, nitrogen content preferably is restricted to 0.007 weight % for the titanium that prevents from reliably to exist under each corresponding situation combines fully with nitrogen.
The phosphorus that is lower than the low levels of set upper limit of the present invention helps to make steel of the present invention to have good solderability.Therefore, according to the present invention, phosphorus content preferably is restricted to＜0.1 weight %, and particularly＜0.02 weight % obtains good especially result when phosphorus content is＜0.010 weight %.
If sulphur content is lower than set upper limit of the present invention, MnS or (Mn, Fe) formation of S is suppressed, thereby guarantees that steel of the present invention and flat product prepared therefrom have the good ductility energy then.It is especially true when sulphur content is lower than 0.003 weight %.
According to mode of the present invention, the flat product that is made of dual phase steel of the present invention can directly transmit (promptly need not carry out subsequently cold-rolled process), further to process as the form of the hot rolling band that obtains after the hot rolling.Therefore, can form the not parts of the height proof stress of coating state from the hot rolling band that obtains according to the present invention.If these parts especially will be avoided corrosion, then can before or after forming various parts, the hot rolling band sacrificial metal coating be set for it.
On the other hand, the less relatively flat product of thickness if desired, then the hot rolling band that is equipped with by steel of the present invention can at first experience cold rollingly, anneals subsequently, further process with the form as cold rolling strap, more than operation can randomly be implemented after applying the anticorrosive coating of metal.
If the sacrificial metal coating is set, then can plates and carry out by (for example) galvanizing, zinc-plated anneal or electrolysis for flat product of the present invention.If desired, can before coating, implement preoxidation process, want in the substrate of coating to guarantee that metal cover is combined under each corresponding situation reliably.
According to the present invention, for the form for preparing with the hot rolling band exists, and (described duplex structure is by 20% to 70% martensite to have the flat product of the tensile strength that is at least 950MPa and duplex structure, 8% retained austenite at the most, and the ferrite of surplus and/or bainite formation), the dual phase steel fusion that at first will constitute according to the present invention, melt casting is become prefabrication (such as slab or thin slab), then described prefabrication is reheated to or be stored in 1100 to 1300 ℃ initial hot-rolled temperature, under 800 to 950 ℃ final hot-rolled temperature, be the hot rolling band, and the hot rolling band of gained is being reeled under 570 ℃ the coiling temperature at the most the prefabrication hot rolling.
By in the scope of room temperature to 570 ℃, regulating the coiling temperature suitably, can regulate itself next without successive what further duplex structure of rolling hot rolling band, to obtain the combination of various desired characteristics.
If the hot rolling band that obtains according to mode of the present invention will remain coating not, perhaps to carry out the electrolysis plating and become hot rolling band with metal cover, then flat product needn't be annealed.On the other hand, if by galvanizing with the hot rolling band coated with metal cover, then at first under 600 ℃ the highest annealing temperature, anneal, be cooled to the temperature of plating bath subsequently, for example it can be zinc and bathes.After bathing, can be in a usual manner the hot rolling band of coating be cooled to room temperature by zinc.
If flat product of the present invention will provide with the form of cold rolling strap, the dual phase steel fusion that so for this reason will constitute according to the present invention, the steel melt of correspondence is cast as prefabrication (such as slab or thin slab), then described prefabrication is reheated to or be stored in 1100 to 1300 ℃ initial hot-rolled temperature, under 800 to 950 ℃ final hot-rolled temperature, be the hot rolling band with the prefabrication hot rolling, the hot rolling band is reeled under 500 to 650 ℃ coiling temperature, then that the hot rolling band is cold rolling, the cold rolling strap of gained is annealed under 700 to 900 ℃ annealing temperature, subsequently cold rolling strap is cooled off in a controlled manner.
The coiling temperature is 580 ℃ of preparation particularly advantageouies that have been proved to be for cold rolling strap at the most, because if exceed 580 ℃ coiling temperature, then the risk of grain boundary oxidation increases.Under low coiling temperature, the intensity of hot rolling band and yield strength improve, and make the hot rolling band is carried out the cold rolling difficulty more that becomes.Therefore, will be cold rolling for the hot rolling band of cold rolling strap preferably at least 530 ℃, particularly reel under at least 550 ℃ the temperature.
If cold rolling strap prepared in accordance with the present invention will remain coating not, perhaps to carry out the electrolysis plating, then in the successive annealing furnace, carry out anneal with independent job step.Heating rate is 1 to 50K/s, and the maximum annealing temperature that is reached is in 700 to 900 ℃ of scopes.Subsequently,, preferably be cooled, make in 550 to 650 ℃ temperature range, to reach the rate of cooling that is at least 10K/s, to restrain pearlitic formation through the annealed cold rolling strap in order to have a mind to regulate the combination of the desired characteristic of the present invention.After the temperature in reaching this critical range, band can be kept 10 to 300 seconds time, perhaps can directly be cooled to room temperature with 0.5 to 30K/s rate of cooling.
Yet, if cold rolling strap will pass through the hot-dip process coating, can be with annealing and the combination of coating step.In this case, cold rolling strap is with successive order each stove section by the hot dip process production line, and the leading temperature of each stove section is different and be up to 700 to 900 ℃, and heating rate should be chosen in 2 to 100K/s the scope in this case.After the annealing temperature that reaches under each corresponding situation, band was kept under this temperature 10 to 200 seconds.Subsequently band is cooled to the temperature of the plating bath (being typically zinc bathes) under each corresponding situation, is usually less than 500 ℃, in this case, in 550 to 650 ℃ temperature range internal cooling speed also should exceed 10K/s.Reaching this temperature after the stage, cold rolling strap can randomly keep 10 to 300 seconds under the temperature of each corresponding situation.Subsequently, with annealed cold rolling strap by the plating bath under each corresponding situation (preferred zinc is bathed).Subsequently, cold rolling strap is cooled to room temperature to obtain the cold rolling strap of conventional galvanizing, perhaps heating rapidly is cooled to room temperature subsequently to prepare zinc-plated annealed cold rolling strap.
If the hot rolling band by cold rolling be cold rolling strap, then proved advantageously, regulating cold rolling degree is 40% to 70%, particularly 50% to 60%, so that make rolling band reach sufficiently high intensity and available assembly project mathematic(al) parameter under each corresponding situation is reached optimum utilization.The thickness of cold rolling in this manner cold rolling strap of the present invention is generally 0.8 to 2.5 millimeter.
If desired, cold rolling strap can be at coating or is not experienced skin-pass under the coating state, and the skin-pass degree is adjusted to reaching 2%.
Followingly describe the present invention with reference to embodiment.
With the mode fusion of 16 kinds of steel melts 1 to 16 (its composition is as shown in table 1), and be cast as slab with routine.Subsequently slab is reheated in stove to 1200 ℃, and begin to carry out hot rolling from this temperature in the mode of routine.Final rolling temperature is 900 ℃.
For first campaign, the hot rolling band that obtains is like this reeled under 550 ℃ coiling temperature, its sharpness of regulation is+/-30 ℃, then with they cold rolling degree be respectively 50%, 65% with 70% condition under cold rolling to become thickness be 0.8 millimeter to 2 millimeters cold rolling strap.
Subsequently, according to above in the mode that general type is described, annealing and controlled process of cooling to the cold rolling strap of gained at the cold rolling strap that will transmit with coating state not.
Table 2 shows cold rolling degree and the thickness of strip of regulating under the structural state, mechanical characteristics, each corresponding situation of the cold rolling strap for preparing in first campaign of melt 1 to 16.
In the test of other three series, the hot rolling band that is prepared by melt 1 to 16 in the above described manner is being lower than 100 ℃ coiling temperature, is reeling 500 ℃ temperature and under 650 ℃ temperature respectively.Table 3 (the coiling temperature is 20 ℃), table 4 (coiling temperature=500 ℃) and table 5 (coiling temperature=570 ℃) show the characteristic of measuring at these hot rolling bands.The hot rolling band of Huo Deing not is to be intended for use cold rollingly like this, but can randomly be transported after being provided with the sacrificial metal coating further to be processed as parts.
Table 1
| Melt | ??C | ??Si | ??Mn | ??Al | ??Mo | ??Ti | ??Cr | ??B | ??P | ??S | ??N |
| ??1 | ??0.??149 | ??0.??30 | ??1.??97 | ??0.??007 | ??- | ??- | ??0.45 | ??0.00??04 | ??0.??003 | ??0.??004 | ??0.00??13 |
| ??2 | ??0.??150 | ??0.??30 | ??1.??97 | ??＜0.0??05 | ??- | ??0.??023 | ??0.45 | ??0.00??21 | ??0.??005 | ??0.??004 | ??0.??015 |
| ??3 | ??0.??152 | ??0.30 | ??1.??99 | ??0.??005 | ??- | ??- | ??0.46 | ??0.00??04 | ??0.??004 | ??0.??004 | ??0.00??14 |
| ??4 | ??0.??157 | ??0.30 | ??1.??97 | ??0.??005 | ??- | ??- | ??0.81 | ??0.00??05 | ??0.??004 | ??0.??004 | ??0.00??17 |
| ??5 | ??0.??153 | ??0.??30 | ??1.??50 | ??0.??005 | ??- | ??- | ??0.81 | ??0.00??04 | ??0.00??4 | ??0.??004 | ??0.00??15 |
| ??6 | ??0.??150 | ??0.??02 | ??1.??98 | ??＜0.0??05 | ??- | ??0.??023 | ??0.80 | ??0.00??22 | ??0.??004 | ??0.??005 | ??0.00??15 |
| ??7 | ??0.??152 | ??0.??60 | ??1.??97 | ??＜0.0??05 | ??- | ??0.??021 | ??0.45 | ??0.00??22 | ??0.??004 | ??0.??004 | ??0.00??24 |
| Melt | ??C | ??Si | ??Mn | ??Al | ??Mo | ??Ti | ??Cr | ??B | ??P | ??S | ??N |
| ??8 | ??0.??154 | ??0.??19 | ??2.??07 | ??0.??004 | ??- | ??0.??022 | ??0.??60 | ??0.00??11 | ??0.00??4 | ??0.00 | ??0.00??52 |
| ??9 | ??0.??16 | ??0.29 | ??1.8 | ??0.??032 | ??0.08 | ??0.04??6 | ??0.??52 | ??0.00??09 | ??0.??013 | ??0.??001 | ??0.00??4 |
| ??10 | ??0.??152 | ??0.28 | ??1.7 | ??0.??028 | ??0.??15 | ??0.??051 | ??0.3 | ??0.00??12 | ??0.??008 | ??0.??001 | ??0.00??45 |
| ??11 | ??0.14 | ??0.21 | ??1.7 | ??0.??036 | ??0.19 | ??0.??035 | ??0.??45 | ??0.00??10 | ??0.??011 | ??0.00??15 | ??0.00??42 |
| ??12 | ??0.??148 | ??0.24 | ??1.83 | ??0.??031 | ??0.??22 | ??0.??035 | ??0.??65 | ??0.00??12 | ??0.??010 | ??0.00??15 | ??0.00??42 |
| ??13 | ??0.??153 | ??0.29 | ??2.2 | ??0.??029 | ??0.??08 | ??0.??090 | ??0.59 | ??0.00??18 | ??0.??012 | ??0.00??13 | ??0.00??51 |
| ??14 | ??0.??19 | ??0.22 | ??1.75 | ??0.??033 | ??0.??18 | ??0.??052 | ??0.??51 | ??0.00??09 | ??0.??007 | ??0.00??20 | ??0.00??31 |
| ??15 | ??0.??12 | ??0.27 | ??2.??35 | ??0.??027 | ??- | ??0.??051 | ??0.5 | ??0.00??12 | ??0.??014 | ??0.00??12 | ??0.00??29 |
| ??16 | ??0.1 | ??0.??31 | ??2.??31 | ??0.??031 | ??0.22 | ??0.??086 | ??0.??66 | ??0.00??16 | ??0.??013 | ??0.00??16 | ??0.00??47 |
Above amount is all in weight %, and surplus is iron and unavoidable impurities.
Table 3
Table 4
Table 5
Claims (30)
1. dual phase steel, its tissue are by 20% to 70% martensite, 8% retained austenite and the ferrite and/or the bainite of surplus constitute at the most, and it has the tensile strength that is at least 950MPa, and has following composition (in weight %):
Carbon: 0.10% to 0.20%,
Silicon: 0.10% to 0.60%,
Manganese: 1.50% to 2.50%,
Chromium: 0.20% to 0.80%,
Titanium: 0.02% to 0.08%,
Boron:＜0.0020%,
Molybdenum:＜0.25%,
Aluminium:＜0.10%,
Phosphorus :≤0.2%,
Sulphur :≤0.01%,
Nitrogen :≤0.012%,
Surplus is iron and unavoidable impurities.
2. dual phase steel according to claim 1 is characterised in that its yield strength is at least 580MPa.
3. according to each the described dual phase steel in the aforementioned claim, be characterised in that its unit elongation A
80Be at least 10%.
4. according to each the described dual phase steel in the aforementioned claim, be characterised in that its phosphorus content＜0.1 weight %, particularly＜0.02 weight %.
5. according to each the described dual phase steel in the aforementioned claim, be characterised in that its carbon content is 0.12 weight % to 0.18 weight %.
6. according to each the described dual phase steel in the aforementioned claim, be characterised in that its silicone content is 0.20 weight % to 0.40 weight %.
7. according to each the described dual phase steel in the aforementioned claim, be characterised in that its manganese content is 1.50 weight % to 2.35 weight %.
8. according to each the described dual phase steel in the aforementioned claim, be characterised in that its chromium content is 0.30 weight % to 0.70 weight %.
9. according to each the described dual phase steel in the aforementioned claim, be characterised in that its titanium content is 0.030 weight % to 0.055 weight %.
10. according to each the described dual phase steel in the aforementioned claim, be characterised in that exist under the situation of nitrogen, the titanium content of described dual phase steel is greater than 5.1 times of the nitrogen content under each corresponding situation.
11. each the described dual phase steel according in the aforementioned claim is characterised in that, its boron content is 0.0005 weight % to 0.0020 weight %.
12. dual phase steel according to claim 11 is characterised in that, its boron content is 0.0007 weight % to 0.0016 weight %.
13. each the described dual phase steel according in the aforementioned claim is characterised in that, its molybdenum content is 0.05 weight % to 0.22 weight %.
14. dual phase steel according to claim 13 is characterised in that, its manganese content＜1.7 weight %.
15., be characterised in that its chromium content＜0.4 weight % according to claim 13 or 14 described dual phase steels.
16. each the described dual phase steel according in the aforementioned claim is characterised in that, its molybdenum content is 0.065 weight % to 0.150 weight %.
17. each the described dual phase steel according in the aforementioned claim is characterised in that, its aluminium content is 0.01 weight % to 0.06 weight %.
18. each the described dual phase steel according in the aforementioned claim is characterised in that, its sulphur content＜0.003 weight %.
19. each the described dual phase steel according in the aforementioned claim is characterised in that, its nitrogen content＜0.007 weight %.
20. each the described dual phase steel according in the aforementioned claim is characterised in that the content of its retained austenite is less than 7%.
21. a flat product, it is by constituting according to the dual phase steel that each obtained in the claim 1 to 20.
22. flat product according to claim 21 is characterised in that, it is for only passing through hot rolled hot rolling band.
23. flat product according to claim 21 is characterised in that, it is for by the cold rolling cold rolling strap that obtains.
24. each the described flat product according in the claim 21 to 23 is characterised in that it is provided with the sacrificial metal coating.
25. flat product according to claim 24 is characterised in that, described sacrificial metal coating makes by galvanizing.
26. flat product according to claim 24 is characterised in that, described sacrificial metal coating makes by zinc-plated annealing.
27. method for preparing the hot rolling band, this hot rolling band has tensile strength and the duplex structure that is at least 950MPa, described duplex structure is by 20% to 70% martensite, 8% retained austenite and the ferrite and/or the bainite of surplus constitute at the most, and this method comprises the following steps:
-will be according to the dual phase steel fusion of each acquisition in the claim 1 to 20,
-melt casting is become prefabrication, such as slab or thin slab,
-with described prefabrication reheat to or remain on 1100 to 1300 ℃ initial hot-rolled temperature,
-under 800 to 950 ℃ final hot-rolled temperature, described prefabrication is rolled into described hot rolling band, and
-described hot rolling band is reeled being at most under 570 ℃ the coiling temperature.
28. method for preparing cold rolling strap, this cold rolling strap has tensile strength and the duplex structure that is at least 950MPa, described duplex structure is by 20% to 70% martensite, 8% retained austenite and the ferrite and/or the bainite of surplus constitute at the most, and this method comprises the following steps:
-will be according to the dual phase steel fusion of each formation in the claim 1 to 20,
-melt casting is become prefabrication, such as slab or thin slab,
-with described prefabrication reheat to or remain on 1100 to 1300 ℃ initial hot-rolled temperature,
-under 800 to 950 ℃ final hot-rolled temperature, described prefabrication is rolled into the hot rolling band,
-described hot rolling band is reeled under 500 ℃ to 650 ℃ coiling temperature,
-behind coiling, described hot rolling band is carried out cold rolling,
-described cold rolling strap is annealed under 700 ℃ to 900 ℃ annealing temperature, and
-the annealed cold rolling strap is cooled off in a controlled manner.
29. method according to claim 28 is characterised in that, described hot rolling band with 40% to 70% cold rolling degree by the described cold rolling strap of cold rolling one-tenth.
30. according to claim 28 or the described method of claim 29, be characterised in that, in 550 ℃ to 650 ℃ temperature range, implement described controlled cooling with the rate of cooling of 10K/s at least.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP07114398A EP2028282B1 (en) | 2007-08-15 | 2007-08-15 | Dual-phase steel, flat product made of such dual-phase steel and method for manufacturing a flat product |
| EP07114398.6 | 2007-08-15 | ||
| PCT/EP2008/060381 WO2009021897A1 (en) | 2007-08-15 | 2008-08-07 | Dual-phase steel, flat product made of such dual-phase steel and method for producing a flat product |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101802233A true CN101802233A (en) | 2010-08-11 |
| CN101802233B CN101802233B (en) | 2013-08-14 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2008801034262A Active CN101802233B (en) | 2007-08-15 | 2008-08-07 | Dual-phase steel, flat product made of such dual-phase steel and method for producing flat product |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US20100273024A1 (en) |
| EP (1) | EP2028282B1 (en) |
| JP (1) | JP5486496B2 (en) |
| CN (1) | CN101802233B (en) |
| ES (1) | ES2387040T3 (en) |
| PL (1) | PL2028282T3 (en) |
| WO (1) | WO2009021897A1 (en) |
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2008
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Also Published As
| Publication number | Publication date |
|---|---|
| ES2387040T3 (en) | 2012-09-12 |
| JP5486496B2 (en) | 2014-05-07 |
| JP2010535946A (en) | 2010-11-25 |
| CN101802233B (en) | 2013-08-14 |
| WO2009021897A1 (en) | 2009-02-19 |
| PL2028282T3 (en) | 2012-11-30 |
| EP2028282B1 (en) | 2012-06-13 |
| US20100273024A1 (en) | 2010-10-28 |
| EP2028282A1 (en) | 2009-02-25 |
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