CN101316942A - Steel sheet for hot press forming having excellent heat treatment and impact property, hot press parts made of it and the method for manufacturing thereof - Google Patents
Steel sheet for hot press forming having excellent heat treatment and impact property, hot press parts made of it and the method for manufacturing thereof Download PDFInfo
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- CN101316942A CN101316942A CNA2006800448736A CN200680044873A CN101316942A CN 101316942 A CN101316942 A CN 101316942A CN A2006800448736 A CNA2006800448736 A CN A2006800448736A CN 200680044873 A CN200680044873 A CN 200680044873A CN 101316942 A CN101316942 A CN 101316942A
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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
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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
- C22C38/06—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Abstract
Disclosed is a steel sheet that exhibits an ultra-high strength after hot press forming followed by rapid cooling, and an enhanced yield strength after painting. The steel sheet has a composition comprising 0.1% to 0.5% by weight of C, 0.01% to 1.0% by weight of Si, 0.5% to 4.0% by weight of Mn, 0.1 % by weight or less of P, 0.03% by weight or less of S, 0.1 % by weight of soluble Al, 0.01% to 0.1% by weight of N, 0.3% by weight or less of W, and the balance Fe and other inevitable impurities. Further disclosed are a hot-pressed part made of the steel sheet and a method for manufacturing the hot-pressed part. The hot-pressed part achieves a high increment in yield strength after heat treatment for painting while ensuring an ultra-high tensile strength. Furthermore, the hot-pressed part exhibits superior adhesion to a coatinglayer, good surface appearance and improved corrosion resistance after painting.
Description
Technical field
The present invention relates to be used for the steel plate of hot compacting (hot press forming), described steel plate is mainly used in structure unit and the reinforcement of making car body, relates to the manufacture method of this steel plate, by the hot press parts of this steel plate manufacturing and the method for making hot press parts.More specifically, the present invention relates to be used for the steel plate of hot compacting, this steel plate has the yield strength that has improved after superstrength and the japanning behind the hot compacting, also relate to the manufacture method of this steel plate, hot press parts of being made by this steel plate and the method for making hot press parts.
Background technology
In recent years, relevant with safety with the life of car passenger regulations are more and more stricter.In this case, at present, the researchist has actively born for reducing the research work that car body weight and exploitation are used for the high tensile steel plate of lightweight car body, to improve the shock resistance of car body.Yet the intensity that improves the steel plate that is used for car body causes steel formability variation quite significantly.
For addressing this problem, some schemes have been proposed.For example, the Korean Patent communique proposes a kind of method of making the high tensile steel plate of high formability 2005-062194 number.The steel plate of this method manufacturing is phase transformation induced plasticity (TRIP) steel plate that utilizes the martensitic transformation of residual austenite, and has the tensile strength of about 980Mpa.
Yet, need to add unit as C or Mn and usually reach tensile strength greater than 980MPa, can cause the increase of production cost like this.In addition, at the press forging shaping of the steel plate of superstrength, because the high strength of steel plate, can take place such as the shape-holding property difference with to some problems of mould infringement at the press forging shaping.
For improving these problems, put forward various plans so far, as utilize the technology of hot compacting.For example, the Korean Patent communique proposes a kind of method of being made the finished product by cold-rolled steel sheet for 2003-049731 number, this method is to utilize low strength and the high working property of steel plate before heat-treating, steel plate is heat-treated and the press forging shaping cooling rapidly in mould then in the austenite one phase district.In addition, Japanese unexamined patent publication discloses for 2005-126733 number a kind ofly has the manufacture method of the steel plate of excellent high-temperature processibility to hot pressing, it is characterized in that adding Mo, Nb or their combination.
The method of prior art emphasizes to improve the importance of the tensile strength of the steel plate behind the hot compacting, still, because the yield strength of japanning back steel plate improves, make steel plate have good shock feature and have technology limitation.
During this period, Japanese unexamined patent publication 2003-034854 number proposes a kind of hot pressed parts that have based on the plated film of Fe-Al, and described plated film contains 0.1% Cr and Mn of its gross weight.The effect of Mn or Cr is to cause variation in the coating structure based on Fe-Al, causes improving solidity to corrosion.Yet, add Cr formation plated film and improved the surface viscosity of coating liquid, and make the concentration of coating liquid be difficult to be controlled at the constant level, causing can not be to carry out the problem of conventional coating operation at a high speed.
Summary of the invention
Technical problem
The invention provides a kind of steel plate that is used for hot compacting, the quick cooling of this steel plate after by thermal treatment has high-tensile, and reaches yield strength significantly improve after the thermal treatment of adopting for japanning.Based on these advantages, steel plate of the present invention obtains good shock feature.In addition, the good adhesive property of steel plate demonstration of the present invention and coating.In addition, other advantages of steel plate of the present invention are the solidity to corrosions that have after surface of good outward appearance and the good japanning.
Technical scheme
The present invention seeks to solve the problems referred to above in prior art field, therefore, one aspect of the present invention provides a kind of steel plate, its composition comprises: the carbon (C) of 0.1-0.5 weight %, 0.01-1.0 the silicon of weight % (Si), 0.5-4.0 the manganese of weight % (Mn), the phosphorus (P) that is less than or equal to 0.1 weight %, be less than or equal to 0.03 weight % sulphur (S), 0.1 the soluble aluminum of weight % (Al), 0.01-0.1 the nitrogen of weight % (N) is less than or equal to the tungsten (W) of 0.3 weight % and balance iron (Fe) and other unavoidable impurities.
Steel plate of the present invention can be hot-rolled steel sheet, cold-rolled steel sheet, or has the steel plate of the zinc coating (galvannealed layer) that is coated with aluminium coated, zinc coating or handles through diffusion annealing.
In the embodiments of the present invention, steel plate has the siliceous aluminium coated that is coated with, and coating wt is 40-80g/m
2Every side (g/m
2Per side).
In another embodiment of the present invention, steel plate can have zinc coating that forms on the surface or the zinc coating of handling through diffusion annealing, and this steel plate can contain the Mn of 1.0-4.0 weight %.
In the another embodiment of the invention, steel plate is formed also can comprise at least a element that is selected from down group: a) element of at least a Mo of being selected from and Cr, its amount is 0.01-2.0 weight %, b) at least a element that is selected from Ti, Nb and V, its amount is 0.001-0.1 weight %, c) at least aly be selected from following element: the Ni of the Cu of 0.005-1.0 weight % and 0.005-2.0 weight %, and d) B of 0.0001-0.01 weight %.
Another aspect of the present invention provides a kind of manufacturing to be coated with the method for zinc-plated (zinc-plated) steel plate, this method comprises: to satisfying the plate slab reheat to 1 of the steel composition that limits above, 100-1,300 ℃, make the plate slab behind the reheat be not less than the Ar3 transition point but be not higher than 1, carry out hot finishing (hot finishrolling) under 000 ℃ the temperature, this hot-rolled steel sheet is batched in 500-750 ℃; (coiled hot-rolledsteel sheet) carries out pickling to the rolling hot-rolled steel sheet, carries out cold rolling to the hot-rolled steel sheet after the pickling; Cold-rolled steel sheet was carried out galvanizing 10 seconds or time still less 450-500 ℃ of temperature range.This method also is included in carries out alloying 30 seconds time still less 440-580 ℃ of temperature range to galvanized cold-rolled steel sheet after zinc-plated.This method also is included in carries out in 750-900 ℃ temperature cold-rolled steel sheet being carried out the continuous annealing processing before the galvanizing.
Another aspect of the present invention provides a kind of hot press parts, and the steel microstructure of these parts comprises the martensitic structure more than or equal to 80%, and has the steel composition that limits above.
In the embodiments of the present invention, hot press parts can have the zinc coating that is coated with aluminium coated, zinc coating or handles through diffusion annealing.
In another embodiment of the present invention, aluminium coated layer (coatinglayer) contains the Fe of Si, 39-55% of 4.5-8.4% and the Al of surplus.
In the another embodiment of the invention, the yield strength variation (Δ YS) of hot press parts before japanning and after the japanning is more than or equal to 100MPa, is preferably greater than or equals 120MPa.
Another aspect of the present invention provides a kind of method of making hot press parts, this method is to carry out hot compacting by the steel plate that the steel that satisfies above-mentioned definition is formed, cool off this hot pressing steel plate rapidly with 10-500 ℃/second speed, make steel plate have martensitic structure more than or equal to 80%.
Steel plate can be hot-rolled steel sheet, cold-rolled steel sheet or be coated with the Aluminium Coated Steel plate.Hot compacting preferably carries out in the following manner, and at 800-1,000 ℃ of temperature range forms this hot steel plate, keeps this temperature range 10-1 simultaneously, 000 second with 1-100 ℃/second speed heating steel plate.
Be coated with aluminized steel plate and have the aluminium coated of being coated with, this coating weight is 40-80g/m
2Every side, and contain Si.
The steel plate of the steel plate zinc coating that can be steel plate galvanized or coating handle through diffusion annealing.In this case, steel plate preferably contains the Mn of 1.0-4.0%.Hot compacting carries out in the following manner,, 700-950 ℃ of temperature range this hot steel plate is formed with 1-100 ℃/second speed heating steel plate, keeps this temperature range 10-1 simultaneously, 000 second.Zinc-plated is to carry out in the following manner, 450-500 ℃ of temperature range cold-rolled steel sheet is carried out galvanizing 10 seconds time still less.Steel (galvannealed steel) with zinc coating that diffusion annealing handles is operated in the following manner: cold-rolled steel sheet is carried out galvanizing 10 seconds time still less 450-500 ℃ of temperature range, 440-580 ℃ of temperature range galvanized cold-rolled steel sheet is carried out alloying 30 seconds time still less then.
In the embodiments of the present invention, steel plate is made in the following manner: to plate slab reheat to 1,100-1, makes the plate slab behind the reheat be not less than Ar by 300 ℃
3Transition point but be not higher than under 1,000 ℃ the temperature and carry out hot finishing batches this hot-rolled steel sheet in 500-750 ℃; The rolling hot-rolled steel sheet is carried out pickling, carry out cold rolling the hot-rolled steel sheet after the pickling.This cold-rolled steel sheet can be 700-900 ℃ of continuous annealing.
Beneficial effect
Steel plate of the present invention has superstrength and improved yield strength after japanning.In addition, steel plate of the present invention has improved surface treatment character.Therefore, steel plate of the present invention can be used to make the structure unit and the reinforcement of automobile, thereby has reduced the weight of car body, and has greatly improved shock feature.
Implement best mode of the present invention
Describe illustrative embodiments of the present invention below in detail.
Steel of the present invention has the characteristic of thermal treatment-hardenability steel.Term " thermal treatment-hardenability " expression steel plate during heating treatment, when cooling, have low-temperature transformation phase (transformation phase), steel plate is strengthened.The steel plate that is used for hot compacting according to the present invention can be used for thermal treatment-hardenability rings territory, because a representation example of thermal treatment-hardenability steel is the high-strength steel that is used for hot compacting, this steel is by being shaped to steel in thermocompressor and cooling off this hot pressed steel rapidly and make.Used herein term " hot press parts " expression is a kind of by being the shape that requires with steel formability, heat-treats the high-strength parts of manufacturing then.According to the embodiment of the present invention, provide a kind of by in thermocompressor, steel being shaped and cooling off the high-strength hot pressure part that this hot pressed steel is made rapidly.Should be understood that hot press parts comprises by under the temperature and pressure condition or be the shape that requires with steel formability of the present invention at room temperature, heat-treats the high-strength parts of manufacturing then.Hot press parts can be used for various application, and for example, the structure unit of automobile and reinforcement, hot press parts have utilized the physical properties of steel of the present invention.
Be used for the mechanical properties of steel of hot compacting and the research process of surface property in improvement and finished the present invention.
(1) mechanical properties
Steel plate of the present invention is characterised in that, uses the element of tungsten (W) as the good thermal treatment-hardenability that guarantees steel plate, so that steel plate has superstrength.In addition, finished the present invention based on the following fact, that is, when being designed to the steel that adds tungsten (W) based on high nitrogen components system, the yield strength of steel significantly improves after japanning, and therefore, steel obtains good shock resistance.
(2) surface property
According to another embodiment, steel of the present invention can be hot-rolled steel sheet or cold-rolled steel sheet, and these steel plates can be chosen wantonly and carry out coating.Coating can be by the steel that is mainly used in the zinc coating (zinc-plated) of making automotive material, handles through zinc coating diffusion annealing or is mainly used in and makes the aluminium coating that heat supply is pressed into the steel plate of shape and carry out.
According to another implementation of the invention, steel plate carries out zinc-plated, and carries out hot compacting in low relatively temperature, with the binding property of raising with coating.The binding property of steel plate with hot compacting during temperature rise and variation, cause the solidity to corrosion of difference.Therefore, the low temperature during the hot compacting causes the fusible raising of steel plate and coating.Therefore, it is very important to make steel plate have enough intensity.According to another implementation of the invention, improved the binding property of steel plate and coating, and by zinc-plated to steel plate and reduce zinc-plated back steel plate and carry out the required temperature of hot compacting and make steel plate have sufficiently high intensity.
In addition, thermal treatment of the present invention-hardenability steel can be coated with and aluminize.Another embodiment according to the present invention, the surface property that adds the W-steel with high nitrogen components system can be improved based on the Si content in the Al-Si-Fe plated film by control.That is, when using siliceous aluminium coating liquid to form plated film on steel plate, even do not add any alloying element, the surface property of steel plate also can be improved because of the Si content of coated surface.
The following describes the composition of steel of the present invention.Herein, the percentage of component (%) is weight % in the composition.
Carbon (C) content is preferably 0.1-0.5%.
C is the principal element that is used for improving armor plate strength.The C add-on is preferably more than or equals 0.1%, to form hard phase, as austenite or martensite, to obtain superstrength.When C content less than 0.1% the time, although heat-treat, also still can not make steel plate meet the requirements of intensity in the austenite one phase district.And when C content greater than 0.5% the time, the toughness of steel plate and weldability be variation most probably.And, C content surpass 0.5% hot-rolled steel sheet is carried out pickling and rolling during can make steel plate be difficult to welding, and because armor plate strength significantly improves and the coating of steel plate and draw material (threading) degradation and the problem that causes not wishing occurring during annealing.
Silicon (Si) content is preferably 0.01-1.0%.
Si is that sosoloid strengthens element, and its effect is the intensity that improves steel plate.Si content less than 0.01% situation under, be difficult to remove the scale on surface (scale) of hot-rolled steel sheet.And when Si content greater than 1.0% the time, the manufacturing cost of steel plate increases.Si content is more preferably at 0.051-0.5%, but is not limited to this scope.
Manganese (Mn) add-on is preferably 0.5-4.0%.
Mn is that a kind of sosoloid strengthens element, makes very big contribution to improving armor plate strength, and plays a significant role to ferritic transformation from austenite delaying.When Mn content less than 0.5% the time, need high temperature to come the steel plate of thermal treatment in the austenite one phase district.Such high temperature has quickened the steel plate oxidation, although steel plate is carried out coating, but still can the solidity to corrosion of steel plate be had a negative impact.In addition, by also being difficult to make steel plate meet the requirements of superstrength at ferritic-austenitic two-phase region heat-treated steel plate.And when Mn content greater than 4.0% the time, have the danger of the weldability and the hot rolling characteristic difference of steel plate.Another embodiment according to the present invention, zinc-plated and when reducing steel plate after zinc-plated and carrying out the required temperature of hot compacting to steel plate when attempting, Mn content is preferably limited to the 1.0-4.0% scope, more preferably in the 2.0-4.0% scope.Mn can be used to reduce Ac
3The element of temperature.Higher Mn content helps reducing the required temperature of hot compacting.
The content of phosphorus (P) preferably is less than or equal to 0.1%.
P is the effective element that is used to strengthen steel, can make the processibility deterioration of steel when still adding excessive P.Therefore, P content is preferably limited to and is less than or equal to 0.1%.
The content of sulphur (S) preferably is less than or equal to 0.03%.S is the contained impurity element of steel.Because S can weaken the ductility and the weldability of steel plate, preferably S content is limited in and is less than or equal to 0.03%.
The content of soluble aluminum (Al) preferably is less than or equal to 0.1%.
Add solubility Al and make steel-deoxidizing.For this reason, the content of Al is adjusted to is less than or equal to 0.1%.When Al content greater than 0.1% the time, the excessive formation of the inclusion of aluminum oxide and so on rather than form AlN causes the amount of dissolved nitrogen (N) to descend.Therefore, the yield strength of steel plate slightly improves.
Nitrogen (N) content is preferably 0.01-0.1%.
N is the very important component of steel plate of the present invention.N is that sosoloid strengthens element, can combine with the element that forms nitride, improves the yield strength of steel plate.The N that should add q.s improves the yield strength after thermal treatment character and the japanning.Before japanning, the N of q.s keeps with the form that intragranular dissolves N, afterwards, stops the dislocation moving after painting, and to improve yield-point, this is the rapid major cause that improves of yield strength of steel plate.When N content does not have such effect less than 0.01% time expection.On the other hand, N content can make greater than 0.1% and be difficult to dissolving and water Cast Steel Plate, make the processibility of steel plate that disadvantageous deterioration take place, and produce pore when welding.N content is preferably limited to the 0.011-0.1% scope, more preferably in the 0.02-0.1% scope.
The content of tungsten (W) preferably is less than or equal to 3%.
W is the element that improves the thermal treatment-hardenability of steel plate, is a kind of very important element, can guarantee that steel plate has enough intensity because contain the throw out of W with helping.If W content surpasses 0.3%, this effect reaches capacity, and causes quite high production cost.Therefore, W content is preferably limited to and is less than or equal to 0.001%, and more preferably 0.001-0.3% most preferably is 0.001-0.1%.
The composition of steel plate of the present invention also comprises at least a element that is selected from down group: Mo, Cr, Ti, Nb, V, Cu, Ni and B.
Mo and Cr are the elements that improves the hardenability of steel plate.Ti, Nb and V are the elements that improves sedimentary formation in the steel plate.Cu and Ni are the elements that improves armor plate strength.B also is the element that improves the hardenability of steel plate.To describe these elements in detail below.
The content that is selected from least a element of Mo and Cr is preferably 0.01-2.0%.
Mo and Cr are used for improving the hardenability of steel plate, and improve the toughness of thermal treatment shaped steel plate.Therefore, the element (it is characterized in that impact can have high-absorbable) of at least a Mo of being selected from of interpolation and Cr is very effective in steel plate.In addition, improved hardenability, made it possible to prevent during hot forming in the steel plate not the intensity generation deterioration of the part that directly contacts with mould because having added the element of at least a Mo of being selected from and Cr.For this purpose, the add-on of Mo or Cr is preferably greater than or equals 0.01%.Although increased the add-on of Mo or Cr, the hardenability of steel plate is not fully improved, and the add-on that increases Mo or Cr can make the steel plate production cost that unnecessary increase takes place.Therefore, the add-on of Mo or Cr is preferably limited to and is less than or equal to 2.0%.The content of preferred Mo or Cr is 0.01-2.0%, most preferably is 0.01-0.5%.
The content that is selected from least a element of Ti, Nb and V is preferably 0.001-0.1%.
Ti, Nb and V are used for improving armor plate strength, reduce particulate diameter in the steel plate and improve the element of the thermal treatment character of steel plate.If the content of at least a element that is selected from Ti, Nb and V is less than 0.001%, this effect is insufficient.Simultaneously, if the content of these elements greater than 0.1%, can cause bigger production cost, and can not meet the requirements of intensity and yield strength because form excessive coal briquette (coal briquette) and nitride.
Preferably in steel plate, there is at least a following element that is selected from: 0.005-1.0 weight %Cu and 0.005-2.0 weight %Ni.
Cu is used for forming the Cu precipitation, to improve the element of armor plate strength.Cu content is less than 0.005% undercapacity that can cause steel plate.Cu content can cause steel plate processibility deterioration greater than 1.0%.
Ni is the element that is used for improving armor plate strength and thermal treatment character.For this reason, Ni content preferably is restricted to and is less than or equal to 0.005%.If Ni content is greater than 2.0%, the production cost of steel plate increases, and undesirable deterioration takes place the processibility of steel plate.
The content of B is preferably 0.0001-0.01%.
B is a kind of high hardenability element.Although only there is micro-B, can guarantee the high strength of steel after the thermal treatment.When B content is not less than 0.0001%, can make steel plate reach enough hardenabilities.Although increased the add-on of B, undesirable deterioration can take place in the hot workability of steel plate, and does not significantly improve the hardenability of steel plate.
According to exemplary embodiment, the composition that the present invention is used for the steel plate of hot compacting comprises component and surplus Fe and other unavoidable impurities of each content that limits above.When needing, can in forming, steel plate add other alloy elements.Though do not address in embodiments of the present invention, however, it should be understood that steel plate composition of the present invention does not foreclose other alloy elements.
If desired, steel plate of the present invention can have different shape.On steel plate of the present invention, apply various coating.For example, steel plate of the present invention can be hot-rolled steel sheet, cold-rolled steel sheet or cold rolled annealed steel plate.The steel plate that steel plate of the present invention can also be steel plate galvanized, handle through zinc coating diffusion annealing and be coated with aluminized steel plate.
As exemplified embodiment of the present invention, the following describes the method for making hot-rolled steel sheet, cold-rolled steel sheet and coating steel plate.
-hot rolling
At first, the preferred reheat to 1 of plate slab, 100-1,300 ℃.If carry out reheat in the temperature that is lower than 1,100 ℃, it is inhomogeneous that the microstructure of steel plate can become, and the dissolving again of at least a element that is selected from alloy element such as Ti and Nb is insufficient.And when the reheat temperature was higher than 1,300 ℃, the microstructure of steel plate can be thicker, and the possibility that occurs variety of issue when making steel plate is higher.
Then, make the plate slab of reheat be not less than Ar
3Transition point but be not higher than and carry out hot finishing under 1,000 ℃.If be lower than Ar
3Transition point temperature is carried out hot finishing, the possibility that exists the impatient sharp increase of thermal deformation resistant to add.And if carry out hot finishing being higher than 1,000 ℃, form blocked up oxide compound crust probably, it is coarse that steel plate can become.
Then, hot-rolled steel sheet preferably batches at 500-750 ℃.When coiling temperature is lower than 500 ℃, can form excessive martensite or bainite, cause the intensity of hot-rolled steel sheet excessively to improve.Excessively the intensity that improves can produce in making cold-rolled steel sheet cold rolling subsequently and load, and causes the problem as appearance poor.And be higher than under 750 ℃ the coiling temperature, excessive precipitation may cause chap.
If desired, hot-rolled steel sheet is carried out cold rolling, make cold-rolled steel sheet.
-cold rolling
The rolling hot-rolled steel sheet is carried out pickling and cold rolling.According to the embodiment of the present invention, cold rollingly preferably carry out with the 30-80% compression ratio.When cold rolling compression ratio less than 30% the time, be difficult to the shape that meets the requirements of thickness and proofread and correct steel plate.And when cold-rolled compression than greater than 80% the time, the possibility chipping at the steel plate edge is very high, may cause load (load) during cold rolling.
If desired, can anneal to cold-rolled steel sheet.
-annealing
Cold-rolled steel sheet carries out continuous annealing at 750-900 ℃.If annealing temperature is lower than 750 ℃, cold-rolled steel sheet can not reach enough processibilities.And if annealing temperature is higher than 900 ℃, can increases production cost and surface quality is descended.
-coating
Hot-rolled steel sheet, cold-rolled steel sheet or annealed cold-rolled steel sheet (below abbreviate " steel plate " as) carry out coating as required.According to the embodiment of the present invention, steel plate can be galvanized steel plate, the steel plate handled through zinc coating diffusion annealing or be coated with aluminized steel plate.The method of carrying out coating is had no particular limits, and its example comprises: hot dip process (hot dipping), plating, vacuum evaporation and coating (cladding).Consider productivity, preferred hot dip coating method.The following describes most preferred coating method, but the present invention is not necessarily limited to these methods.
-zinc coating (zinc-plated)
Steel plate carries out galvanizing.Zinc-platedly preferably carried out 10 seconds at 450-500 ℃.When being lower than 450 ℃ of temperature and carrying out hot dip process, can apply a spot of zinc.Carry out to apply excessive zinc when zinc-plated being higher than 500 ℃ of temperature.When time more than 10 seconds is carried out in hot dip process, can apply excessive zinc.
Then, galvanized cold-rolled steel sheet is cooled to room temperature, makes galvanized steel plate, and optional enlightening is carried out alloying thermal treatment to galvanized steel plate, the steel plate that manufacturing is handled through zinc-plated diffusion annealing.The steel plate of handling through zinc coating diffusion annealing can be at 440-580 ℃, and preferred 480-540 ℃ is carried out alloying thermal treatment 30 seconds time still less.Carry out alloying thermal treatment, during galvanizing, make the laminated aurification of galvanizing.When being lower than 440 ℃ of temperature and carrying out alloying thermal treatment, galvanized steel plate can be non-alloying.And when the temperature that is higher than 580 ℃ was carried out alloying thermal treatment, excessive alloying may take place.
-aluminium coating
Aluminium applies the general Al coating liquid that contains Si that uses to carry out.The Si content of Al coating liquid is in about 7-12% scope.The Al coating liquid contains unavoidable impurities, as Fe.
According to the embodiment of the present invention, be coated with the Aluminium Coated Steel plate and have and be coated with aluminized layer, this coating weight is the every side of 40-80g/m2, and contains Si.Owing to existing aluminium coat to obtain surface of good characteristic behind the hot compacting.Si content will change according to many process factors in the aluminium coat, as thickness of coating.For example, the Al coating liquid that contains 7-12%Si when usefulness carries out the aluminium coating, and the coating weight of Al coating is for being 40-80g/m
2During every side, Si content is about 5-12% in the coating.Importantly, the coating weight when aluminium coat is 40-80g/m
2Every side and when containing Si, the Si content in the Al-Si-Fe plated film that forms by hot compacting subsequently is about 4.5-8.4%, and this plated film reaches the surface of good characteristic.
The invention provides a kind of hot press parts.Hot press parts of the present invention is made in the following manner,, the steel plate of hot-rolled steel sheet, cold-rolled steel sheet or coating is carried out hot compacting that is, then cooling rapidly.Thermal treatment of the present invention-hardenability steel plate carries out hot compacting, and optional through Overheating Treatment, makes the superstrength parts.Hot compacting and thermal treatment are had no particular limits.
In the embodiments of the present invention, the mark of martensitic structure is preferably greater than or equals 80% in the hot press parts, and under this ratio, hot press parts reaches superstrength.Also preferred martensite phase structure.For example, the microstructure of hot press parts comprises the martensite more than or equal to 80%, and all the other percentage amounts are at least a structures that are selected from ferrite and bainite.According to the embodiment of the present invention,, yield strength is brought up to more than or equal to 100MPa, be preferably greater than or equal 120MPa hot press parts japanning and baking.
According to the embodiment of the present invention, hot press parts is carried out hot compacting.Preferred hot press parts has the aluminium coated of being coated with, and this coating weight is 40-80g/m
2Every side, and contain Si.As a result, on the surface of hot press parts, form Si-Fe-Al coating.When the steel plate with Al-Si plated film carried out hot compacting, the Fe that comprises in the steel plate diffused in the plated film of coating.At the bottom of the iron-based/Si that the coating interface exists diffuses in the plated film of coating.Coated surface preferably contains the Fe of Si, 39-55% of 4.5-8.4% and Al and other unavoidable impurities of surplus.Form plated film and can reach the effect of improving surface property.The surface-area of plated film is about 5 mouthfuls.
The following describes the method that the present invention makes hot press parts.
Hot-rolled steel sheet, cold-rolled steel sheet or coating steel plate carry out hot compacting, cooling rapidly then, and the martensitic structure percentage that makes steel plate is more than or equal to 80%.Cooling is preferably carried out with about 10-500 ℃/second speed rapidly.When cooling when carrying out less than 10 ℃/second speed, very difficult acquisition comprises the microstructure of martensite as main phase, thereby is difficult to meet the requirements of intensity.When cooling when carrying out greater than 500 ℃/second speed, need too much producing apparatus investment, therefore cause manufacturing cost to increase, and intensity as those samples of expection significantly do not increase.Therefore, speed of cooling is preferably limited to 10-500 ℃ of/second scope.
According to the embodiment of the present invention, hot compacting can carry out in the following manner, promptly, at 800-1,000 ℃ of temperature range heats steel plate with 1-100 ℃/second speed, forms hot steel plate in mould, simultaneously under described temperature range, keep 10-1,000 second.When the temperature that is lower than 800 ℃ is heat-treated, can not form the austenite of q.s, the result can not form enough martensite behind hot compacting, and this can cause being difficult to meet the requirements of intensity.And thermal treatment can manufacturing cost increase when the temperature that is higher than 1,000 ℃ is carried out, and austenite chap probably.When heating up, make efficient and be tending towards descending less than 1 ℃/second speed.And when heating up, need other producing apparatus greater than 100 ℃ of/second speed.Heat treatment period is during less than 10 seconds, and austenitic transformation is insufficient.And when heat treatment time surpassed 1,000 second, manufacturing cost increased, and austenite can chap.
On the other hand, the steel plate of coating zinc coating or the layer handled through zinc coating diffusion annealing more preferably at about 750-950 ℃, most preferably carries out hot compacting at about 750-850 ℃ preferably at about 700-950 ℃.Can select arbitrarily temperature range to carry out hot compacting, as long as can fully form austenite, and the binding property that can not damage with coating gets final product.
Mode of the present invention
For helping to understand the present invention, the most example embodiment of the present invention has been described in the following embodiments.Yet these embodiment do not constitute limitation of the scope of the invention.
Embodiment
Embodiment 1
At first, make plate slab with the composition shown in the table 1.Plate slab is 1,150-1, and 250 ℃ of reheat 1 hour carry out hot rolling and batch.Finish hot rolling 850-950 ℃ of temperature, and batch in 650 ℃.The parts of hot-rolled steel sheet carry out pickling, and carry out cold rollingly with 50% compression ratio, make cold-rolled steel sheet.
In the following manner, carry out zinc-plated to hot rolling and cold rolling steel plate.Steel plate is annealed at 800 ℃, slowly cools to 650 ℃ with 3 ℃ of/second speed, is cooled to 550 ℃ with 7 ℃ of/second speed, and 460 ℃ overaging (overaging) temperature continuous annealing.Then, the steel plate after the annealing carries out 5 seconds galvanizing, makes the steel plate of galvanizing.
On the other hand, in the following manner, to hot-rolled steel sheet and cold-rolled steel sheet coated with aluminum.Cold-rolled steel sheet is carried out degreasing, pre-treatment, preheats, heat-treats in the reducing atmosphere of nitrogen and hydrogen in 700 ℃ non-oxide process furnace.At this moment, heat-treat in the highest 820 ℃ of temperature.Steel plate after cooling heat is handled, and be immersed in the coating liquid in 680 ℃.Coating liquid comprises 8.5% Si, 2.4% Fe and the Al of surplus.For form the coating of 25-30 mouth thickness in each side, on the steel plate that applies, carry out gas wiping (gaswiping).Then, operation zinc flower (spangle) controller transfers to zero with the surperficial zinc flower of aluminising steel plate.
The parts of the steel plate of hot-rolled steel sheet, cold-rolled steel sheet and coating carry out room temperature and are shaped and aftertreatment, to make each trolley part.The rest part of steel plate carries out hot compacting, makes each trolley part.
Room temperature is shaped and aftertreatment is to carry out in the following manner, and with steel plate V-bending and forming, with 10 ℃/second speed, the temperature of steel plate is increased to 800-950 ℃ with being shaped afterwards, heats this steel plate 5 minutes, with 80 ℃/second speed hot steel plate is cooled off fast in room temperature.After this thermal treatment, will be processed into JIS#5 Elongation test sheet through heat treated steel plate.The Elongation test sheet seethed with excitement 20 minutes in 170 ℃ oil, simulated the quality with the structure unit after the japanning that is used for automobile of this testing plate manufacturing.Then, use general stretching testing machine that testing plate is carried out Elongation test.
Carry out hot compacting in following mode, steel plate is heated to 800-950 ℃, heated steel plate 5 minutes, hot steel plate is transferred in the mould, in mould, hot steel plate is processed in this temperature range with 10 ℃/second speed.After finishing processing, cool off the steel plate of making rapidly with 80 ℃ of/second speed at once.Then, the steel plate after the thermal treatment is cut into JIS#5 Elongation test sheet.The Elongation test sheet boils in 170 ℃ oil and boils 20 minutes, simulates the quality with structure unit after the japanning that is used for automobile of this testing plate manufacturing.
Use the microstructure of the finished product of respective steel of the present invention and comparative steel manufacturing to be shown in table 2.Physical properties at the finished product shown in the table 3.
Table 1
Table 2
Table 3
| Steel | YS(MPa) | TS(MPa) | El(％) | ΔYS(MPs) | Steel | YS(MPa) | TS(MPa) | El(％) | ΔYS(MPs) |
| A1-1 | 973 | 1487 | 7.3 | 193 | E1-1 | 1094 | 1494 | 6.6 | 136 |
| A1-2 | 982 | 1492 | 7.9 | 186 | E1-2 | 1105 | 1511 | 6.5 | 144 |
| B1-1 | 1017 | 1506 | 7.6 | 170 | F1-1 | 896 | 1146 | 9.1 | 56 |
| B1-2 | 1035 | 1521 | 7.4 | 175 | F1-2 | 912 | 1151 | 8.7 | 51 |
| C1-1 | 1025 | 1591 | 7.7 | 147 | F1-3 | 941 | 1156 | 7.8 | 35 |
| C1-2 | 1087 | 1597 | 7.2 | 135 | F1-4 | 925 | 1178 | 7.4 | 41 |
| C1-3 | 1130 | 1607 | 4.9 | 153 | F1-5 | 936 | 1165 | 7.6 | 40 |
| C1-4 | 1125 | 1598 | 5.3 | 145 | F1-6 | 905 | 1149 | 9.0 | 58 |
| C1-5 | 1127 | 1601 | 6.5 | 151 | G1-1 | 901 | 1125 | 6.6 | 54 |
| C1-6 | 1078 | 1593 | 7.9 | 142 | G1-2 | 915 | 1145 | 6.2 | 36 |
| D1-1 | 1202 | 1763 | 7.2 | 136 | H1-1 | 1048 | 1497 | 3.6 | 43 |
| D1-2 | 1215 | 1798 | 6.5 | 125 | H1-2 | 1063 | 1518 | 3.4 | 35 |
Result by table 1-3 can know, the steel plate that steel A1-E1 of the present invention that steel that the present invention limits forms makes hot-rolled steel sheet, cold-rolled steel sheet and coating is satisfied in use, make the finished product by shaping and aftertreatment or hot compacting by the steel plate of each hot-rolled steel sheet, cold-rolled steel sheet and coating, these the finished product show greater than 1, the superelevation tensile strength of 180MPa.In addition, the yield strength of the finished product changes greater than 100MPa before painting and after 170 ℃ of japannings are simulated 20 minutes, and this shows that the finished product have good shock feature, can be used for the structure unit and the reinforcement of car body.
On the contrary, each the finished product that uses comparative steel F-H (it is formed outside the steel compositing range that the present invention limits) to make can not reach and be higher than 1, the tensile strength of 180MPa or change greater than the yield strength of 100MPa.Particularly, use the finished product of the comparative steel F manufacturing of content outside each scope that the present invention limits of its C and N to meet the requirements of the martensite mark, show that tensile strength and yield strength increase slightly.In the finished product that the comparative steel G that uses its C, N and W content outside the present invention limits each scope makes, also observe these problems.In addition, use its N and W content to show that at the finished product that the present invention limits the comparative steel H manufacturing outside each scope yield strength improves slightly.
Embodiment 2
At first, make plate slab with the composition shown in the table 4.Plate slab is dissolved under vacuum, 1,150-1, reheat is 1 hour in the process furnace of 250 ℃ of temperature, carries out hot rolling and batches.Finish hot rolling 850-950 ℃ of temperature, and batch in 650 ℃.Hot-rolled steel sheet carries out pickling, and carries out cold rolling with 50% compression ratio.Cold-rolled steel sheet is annealed in 800 ℃, and carries out continuous annealing under 400 ℃ of overaging temperature.
Then, be heated to 460 ℃, carried out galvanizing 5 seconds, carried out alloying 10 seconds, make coating alloying, be cooled to room temperature, produce the hot-dip galvanized steel sheet of alloying at 500 ℃ through the annealed steel plate.Then, the steel plate of coating is heated to each temperature shown in the table 5,, transfers in the mould, in mould, process in the further heating 5 minutes of this temperature range with 10 ℃ of/second speed.After finishing processing, with 80 ℃ of/second speed the steel plate of making is cooled off rapidly at once.
Then, the steel plate after the thermal treatment is cut into JIS#5 Elongation test sheet.At the processing stand through 90 °-bending hot compacting, the bondability of zinc coating and each steel plate is to determine the binding property of coating by observation by light microscope.On this testing plate, paint, and testing plate was seethed with excitement 20 minutes in 170 ℃ oil, with the quality of the japanning structure unit that is used for automobile of simulating this this testing plate manufacturing.
Use the microstructure of the finished product of respective steel of the present invention and comparative steel manufacturing to be shown in table 4.Physical properties at the finished product shown in the table 5.
Table 4
Table 5
Data by table 4 and table 5 can know that material 1-6 of the present invention satisfies the composition of steel, and make under the creating conditions that the present invention limits, and these materials show greater than 1, the superelevation tensile strength of 470MPa.In addition, change greater than 100MPa before the finished product japanning simulation and 170 ℃ of yield strengths of painting after simulating 20 minutes, this shows that the finished product have good shock feature, can be used for the structure unit and the reinforcement of car body.In addition, the finished product have the excellent adhesion with corresponding coating.
On the contrary, comparative material 1-3,5 and 7 can not satisfy the heat-treat condition of the hot compacting of the present invention's qualification, makes by hot compacting under the high temperature, and these materials show the binding property with corresponding coating difference.
Particularly, comparative material 4 is to use its Mn and the comparative steel D of N outside each scope that the present invention limits to make, and this material can not meet the requirements of the martensite mark, shows that tensile strength and yield strength increase slightly.Use comparative steel D2, the comparative material 5 by the pyroprocessing manufacturing meets the requirements of intensity, but shows the binding property with the coating difference.
In addition, because comparative material 6 and 7 is to use its C and the N content comparative steel E2 outside the framework of the present definition to make, this material shows do not have high-tensile because its low C content can not reach enough martensitic structures after handling in thermal treatment and mould.In addition, comparative material 6 and 7 improves slightly because of its low nitrogen content shows yield strength.
Embodiment 3
At first, make plate slab with the composition shown in the table 6.Plate slab is dissolved under vacuum, 1,150-1, reheat is 1 hour in the process furnace of 250 ℃ of temperature, carries out hot rolling and batches.Finish hot rolling 850-950 ℃ of temperature, and batch in 650 ℃.Hot-rolled steel sheet carries out pickling, and carries out cold rolling with 50% compression ratio.Cold-rolled steel sheet is annealed in 800 ℃, and carries out continuous annealing under 400 ℃ of overaging temperature.
This cold-rolled steel sheet carries out the Al coating in the following manner.With cold-rolled steel sheet degreasing, pre-treatment, preheating in 700 ℃ non-oxide process furnace, in the reducing atmosphere of nitrogen and hydrogen, heat-treat.At this moment, heat-treat in the highest 820 ℃ temperature.Steel plate cooling after the thermal treatment is immersed in the coating liquid in 680 ℃.This coating liquid comprises 8.5% Si, 2.4% the Fe and the Al of surplus.For forming the thick coating of 25-30, on the steel plate that applies, carry out the gas wiping in every side.Then, operation zinc flower controller transfers to zero with the surperficial zinc flower of aluminising steel plate.
With 10 ℃ of/second speed, the cold-rolled steel sheet of coating is heated to 800-950 ℃, carry out high-temperature heat treatment, this temperature range reheat steel plate 5 minutes, hot steel plate is transferred in the mould this hot steel plate of processing in mould then.After finishing processing, with-80 ℃/second speed the steel plate that makes is cooled off rapidly at once.Then, will cut into JIS#5 Elongation test sheet through heat treated steel plate.The Elongation test sheet seethed with excitement 20 minutes in 170 ℃ oil, simulated the quality with structure unit after the japanning that is used for automobile of this testing plate manufacturing.Then, use general stretching testing machine that the painted testing plate is carried out Elongation test.
Be to estimate the solidity to corrosion of testing plate after japanning after the pyroprocessing, the steel plate of coating Al is heated to 800-900 ℃ kept 5 minutes, use water cooling then.Carry out phosphatizing and cation electrodeposition painting, then, that this painted steel plate is cross-sectional to predetermined depth.Salt-fog test and cyclic corrosion test are carried out in combination, and each circulation needs 8 hours, measures the width of the bubble that forms on the painted steel plate, to estimate the solidity to corrosion of painted steel plate.
Table 6
Table 7
The result of table 7 shows, uses each steel A3-H3 of the present invention of the steel composition that satisfies the present invention's qualification to make hot press parts, and the predetermined parts of described heat show greater than 1 the superelevation tensile strength of 470MPa.In addition, because steel plate is processed hot, therefore can process product with complicated shape.And the yield strength of hot press parts before japanning and after 170 ℃ of japanning simulations 20 minutes changes greater than 120MPa, and this shows that heat is scheduled to parts and has good shock feature, can be used for the structure unit and the reinforcement of car body.
On the contrary, the hot press parts that uses each comparative steel I3-J3 to make can not reach enough martensitic structure after the processing because of its low carbon content in thermal treatment and mould, do not have high-tensile, and japanning back yield strength only increases slightly.And the hot press parts that uses comparative steel K3 to make has reached sufficiently high tensile strength, but yield strength increases closely slightly.
Table 8
Result by table 8 can know obviously that steel A3-H3 of the present invention is to be less than or equal to 40g/m
2Amount is during coating, and the steel crystal profile that becomes after phosphatizing is unclear, and makes the solidity to corrosion deterioration because of each surperficial floor height Si content.In addition, when steel A3-H3 of the present invention with more than or equal to 80g/m
2Amount has the surface of good outward appearance when carrying out coating, but with the poor adhesion of each coating, and make the solidity to corrosion after the japanning poor because of the low Si content of each upper layer.
At this, the present invention has been described with reference to the embodiment of front.These embodiments do not constitute limitation of the scope of the invention.All changes with structure, operation and the effect substantially the same with the technology of the present invention spirit that discloses in the appended claims all within the scope of the present invention.
Claims (23)
1. steel plate with good thermal treatment and shock feature, this steel plate has the composition that comprises following component: the soluble aluminum (Al) of the manganese (Mn) of the carbon (C) of 0.1-0.5 weight %, the silicon (Si) of 0.01-1.0 weight %, 0.5-4.0 weight %, the phosphorus (P) that is less than or equal to 0.1 weight %, the sulphur (S) that is less than or equal to 0.03 weight %, 0.1 weight %, the nitrogen (N) of 0.01-0.1 weight %, be less than or equal to the tungsten (W) of 0.3 weight % and the iron of surplus (Fe) and other unavoidable impurities.
2. steel plate as claimed in claim 1 is characterized in that described steel plate is hot-rolled steel sheet, cold-rolled steel sheet, or has the steel plate of the zinc coating that is coated with aluminium coated, zinc coating or handles through diffusion annealing.
3. steel plate as claimed in claim 2 is characterized in that, described steel plate has the aluminium coated that is coated with that contains Si, and this coating weight is 40-80g/m
2Every side.
4. steel plate as claimed in claim 1 is characterized in that, the zinc coating that described steel plate has zinc coating or handles through diffusion annealing, and contain 1.0-4.0 weight %Mn.
5. as each described steel plate among the claim 1-4, it is characterized in that the composition of described steel plate also comprises at least a following element that is selected from:
A) be selected from least a element of Mo and Cr, its content is 0.01-2.0 weight %;
B) be selected from least a element of Ti, Nb and V, its content is 0.001-0.1 weight %;
C) be selected from following at least a element: 0.005-1.0 weight %Cu and 0.005-2.0 weight %Ni; With
D) 0.0001-0.01 weight %B.
6. a manufacturing has the method for the steel plate of good thermal treatment and shock feature, and this method comprises:
Plate slab carry out reheat to 1,100-1,300 ℃, this plate slab has the composition that comprises following component: the N of solubility Al, the 0.01-0.1 weight % of the Si of the C of 0.1-0.5 weight %, 0.01-1.0 weight %, the Mn of 1.0-4.0 weight %, the P that is less than or equal to 0.1 weight %, the S that is less than or equal to 0.03 weight %, 0.1 weight %, be less than or equal to the W of 0.3 weight %, and balance iron and other unavoidable impurities, be not less than Ar
3Transition point but be not higher than 1,000 ℃ temperature the plate slab of described reheat is carried out hot finishing, and in 500-75O ℃ hot-rolled steel sheet is batched;
The rolling hot-rolled steel sheet is carried out pickling, and carry out cold rolling the hot-rolled steel sheet of pickling;
Cold-rolled steel sheet was carried out galvanizing 10 seconds or time still less 450-500 ℃ of temperature.
7. method as claimed in claim 6, this method also be included in zinc-plated after, galvanized cold-rolled steel sheet was carried out alloying 30 seconds or time still less in 440-580 ℃ temperature range.
8. method as claimed in claim 6, this method also are included in before the galvanizing, in 750-900 ℃ of temperature range cold-rolled steel sheet are carried out continuous annealing.
9. as each described method among the claim 6-8, it is characterized in that the composition of described plate slab also comprises at least a following element that is selected from:
A) be selected from least a element of Mo and Cr, its content is 0.01-2.0 weight %;
B) be selected from least a element of Ti, Nb and V, its content is 0.001-0.1 weight %;
C) be selected from following at least a element: 0.005-1.0 weight %Cu and 0.005-2.0 weight %Ni; With
D) 0.0001-0.01 weight %B.
10. hot press parts with good thermal treatment and shock feature, these parts have the microstructure that comprises more than or equal to 80% martensitic structure, and have the described steel of claim 1 and form.
11. hot press parts as claimed in claim 10 is characterized in that, described parts have the zinc coating that is coated with aluminium coated, zinc coating or handles through short annealing.
12. hot press parts as claimed in claim 11 is characterized in that, described aluminium coated layer contains the Fe of Si, 39-55% of 4.5-8.4% and the Al of surplus.
13. hot press parts as claimed in claim 10 is characterized in that, described parts before japanning and afterwards yield strength changes delta YS more than or equal to 100MPa.
14., it is characterized in that described steel is formed and also comprised at least a following element that is selected from as each described hot press parts among the claim 10-13:
A) be selected from least a element of Mo and Cr, its content is 0.01-2.0 weight %;
B) be selected from least a element of Ti, Nb and V, its content is 0.001-0.1 weight %;
C) be selected from following at least a element: the Ni of the Cu of 0.005-1.0 weight % and 0.005-2.0 weight %; With
D) B of 0.0001-0.01 weight %.
15. a manufacturing has the method for the hot press parts of good thermal treatment and shock feature, this method comprises carries out hot compacting to the described steel plate of claim 1, with the quick described hot pressed steel plate of cooling of 10-500 ℃/second speed, make steel plate have martensitic structure more than or equal to 80%.
16. method as claimed in claim 15 is characterized in that, described steel plate is hot-rolled steel sheet, cold-rolled steel sheet or is coated with the Aluminium Coated Steel plate; Described hot compacting carries out in the following manner: with 1-100 ℃ of/second speed, the heating steel plate is at 800-1, and 000 ℃ of temperature range forms hot steel plate, keeps this temperature range 10-1 simultaneously, 000 second.
17. method as claimed in claim 15 is characterized in that, describedly is coated with aluminized steel plate and has the aluminium coated that is coated with that contains Si, coating weight is 40-80g/m
2Every side.
18. method as claimed in claim 15 is characterized in that, described steel plate is coated with the zinc coating that is coated with zinc coating or handles through short annealing on the surface, and contains the Mn of 1.0-4.0 weight %; Described hot compacting carries out in the following manner: with 1-100 ℃ of/second speed, the heating steel plate forms this hot steel plate 700-850 ℃ of temperature range, keeps this temperature range 10-1 simultaneously, 000 second.
19. method as claimed in claim 18 is characterized in that, zinc coating is by carrying out galvanizing 10 seconds 450-500 ℃ of temperature range to cold-rolled steel sheet or still less the time carries out.
20. method as claimed in claim 18, it is characterized in that, operate in the following manner through the zinc coating that diffusion annealing is handled: cold-rolled steel sheet was carried out galvanizing 10 seconds or time still less 450-500 ℃ of temperature range, galvanized cold-rolled steel sheet was carried out alloying 30 seconds or time still less 440-580 ℃ of temperature range.
21. method as claimed in claim 15 is characterized in that, this method comprises: with steel plate reheat to 1,100-1, is being not less than Ar by 300 ℃
3Transition point but be not higher than 1,000 ℃ of temperature carries out hot finishing to the plate slab of reheat, in 500-750 ℃ hot-rolled steel sheet is batched;
Hot-rolled steel sheet to rolling carries out pickling, carries out cold rolling to the hot-rolled steel sheet of pickling.
22. method as claimed in claim 21, this method also are included in 700-900 ℃ cold-rolled steel sheet carried out continuous annealing.
23., it is characterized in that the composition of described steel plate also comprises at least a following element that is selected from as each described method among the claim 15-22:
A) be selected from least a element of Mo and Cr, its content is 0.01-2.0 weight %;
B) be selected from least a element of Ti, Nb and V, its content is 0.001-0.1 weight %;
C) be selected from following at least a element: the Ni of the Cu of 0.005-1.0 weight % and 0.005-2.0 weight %; With
D) B of 0.0001-0.01 weight %.
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| CN102089451B (en) * | 2008-07-11 | 2013-03-06 | 新日铁住金株式会社 | Aluminum-plated steel sheet for hot pressing with rapid heating, process for producing same, and method of hot-pressing same with rapid heating |
| TWI402360B (en) * | 2010-06-24 | 2013-07-21 | Nippon Steel & Sumitomo Metal Corp | And a method for producing the molten Al-plated steel sheet with excellent heat resistance and blackening property |
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| KR100878614B1 (en) | 2009-01-15 |
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