CN107815612A - Hot press-formed steel, hot press-formed technique and formed parts - Google Patents

Hot press-formed steel, hot press-formed technique and formed parts Download PDF

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Publication number
CN107815612A
CN107815612A CN201711063360.6A CN201711063360A CN107815612A CN 107815612 A CN107815612 A CN 107815612A CN 201711063360 A CN201711063360 A CN 201711063360A CN 107815612 A CN107815612 A CN 107815612A
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CN
China
Prior art keywords
hot press
steel
parts
formed parts
technique
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
CN201711063360.6A
Other languages
Chinese (zh)
Inventor
易红亮
熊小川
T.奥皮茨
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Work Easily Shaping Iron And Steel Science And Technology Ltd Is Breathed Out In Chongqing
Volkswagen AG
Original Assignee
Work Easily Shaping Iron And Steel Science And Technology Ltd Is Breathed Out In Chongqing
Volkswagen AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Work Easily Shaping Iron And Steel Science And Technology Ltd Is Breathed Out In Chongqing, Volkswagen AG filed Critical Work Easily Shaping Iron And Steel Science And Technology Ltd Is Breathed Out In Chongqing
Priority to CN201711063360.6A priority Critical patent/CN107815612A/en
Priority to CN202210051980.2A priority patent/CN114369768A/en
Publication of CN107815612A publication Critical patent/CN107815612A/en
Priority to KR1020237012517A priority patent/KR20230054500A/en
Priority to JP2020544088A priority patent/JP7269588B2/en
Priority to US16/760,979 priority patent/US20200263271A1/en
Priority to PCT/CN2018/112367 priority patent/WO2019085855A1/en
Priority to KR1020207015802A priority patent/KR20200072552A/en
Priority to EP18873592.2A priority patent/EP3704282A4/en
Pending legal-status Critical Current

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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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/02—Stamping using rigid devices or tools
    • B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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    • C—CHEMISTRY; METALLURGY
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    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
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    • 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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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
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    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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Abstract

The present invention provides a kind of hot press-formed steel, hot press-formed technique and formed parts, utilize the hot press-formed steel, high-elongation just can be reached by simple hot press-formed technique, the formed parts have excellent yield strength, tensile strength and elongation percentage.The hot press-formed of the present invention includes following component by weight percentage with steel：C:0.1‑0.19%,Mn:5.09‑9.5%,V:0.11‑0.4%,Si+Al:0‑2%；Wherein C and V also meets following alternative one：1）C：0.1 0.17%, V：0.11‑0.4%；2）C：0.171 0.19, V：0.209‑0.4%.

Description

Hot press-formed steel, hot press-formed technique and formed parts
Technical field
The present invention relates to a kind of hot press-formed steel, hot press-formed technique and formed parts.
Background technology
Auto industry, which develops rapidly, brings safety and problem of environmental pollution, and automotive light weight technology can be under the premise that security is guaranteed Energy-saving and emission-reduction are effectively realized, and lift automotive performance.The application of high strength steel can reduce material thickness and meet that security performance will Ask, be the important channel of automotive light weight technology and lifting vehicle safety.
Generally, the forming property of steel is improved and declined with intensity, and hot press-formed is that can be achieved to be shaped then to strengthen Production superhigh intensity auto parts and components a kind of technique, its strengthening mechanism is the gap solution strengthening of martensite.Drop stamping into The advantages of shape part, is that shaping is accurate, can effectively avoid resilience of the high-strength steel in cold forming process from asking with superhigh intensity Topic.In current automobile high-strength steel, only the intensity of drop stamping steel can reach more than 1500MPa.
Automotive safety structural member require material while with higher intensity with more preferable elongation percentage, with existing Loss of weight is further realized on the basis of the hot press-formed steel of 22MnB5.But existing hot press-formed component is in elongation percentage side The space that face is improved.
In addition, hot press-formed steel coated plate is Al-Si coated plates at present, antiseptic property is far below galvanized steel, and Welding difficulty.Galvanized sheet, which is heated to 900 DEG C of drop stamping technique, can occur serious liquefaction, gasification and oxidation, limit galvanized sheet Application in drop stamping.
Chinese patent CN102127675A provides a kind of steel plate warm working part and its production method.Wherein, it is public at it Under the conditions of the steel product ingredient opened, in order to obtain required mechanical property, the production method, which is included in, reduces hot press-formed temperature Under conditions of, heat the material to 730-780 DEG C and punching press is cooled to below Ms 30-150 DEG C（It is typically cooled to 150-280 ℃）Afterwards, 1-5 minutes are incubated after being further heated to 150-450 DEG C, make it from martensite to the austenite partition not changed through carbon For stabilization to end-state, the TRIP effects based on retained austenite improve material ductility.
But this method raises temperature to 150-450 again after component need to be cooled to 150-280 DEG C of a certain specified temp DEG C it is incubated, causes the accuracy of member temperature unmanageable with uniformity, it is necessary to which complicated production process controls Its hardening heat, it is unfavorable for the actual production of hot press-formed component.
The content of the invention
It is an object of the invention to provide a kind of hot press-formed steel, hot press-formed technique and its formed parts, profit With the hot press-formed steel, high-elongation just can be reached by simple hot press-formed technique, the formed parts have Excellent yield strength, tensile strength and elongation percentage.
Technical scheme 1 be related to it is a kind of it is hot press-formed use steel, the hot press-formed use steel are with weight hundred Divide and include following component than meter：C: 0.1-0.19%,Mn: 5.09-9.5%,V: 0.11-0.4%,Si+Al: 0-2%;Wherein C Cooperation with V also meets following alternative one：1）C：0.1-0.17%, V：0.11-0.4%；2） C：0.171-0.19, V： 0.209-0.4%。
According to technical scheme 1, the hot press-formed addition with steel by the stable austenite element such as C, Mn of the invention Reduce the martensite start temperature of material（Ms）With martensitic traoformation end temp（Mf）, so as to can ensure that hardening heat It is set to lower temperature（Such as less than 100 DEG C）And the retained austenite of reasonable content can be retained under quenching state.Therefore can be with Hardening heat is set as room temperature, the accuracy of temperature is easily controllable with uniformity, and technique is simple.
Specifically, quenching-carbon partition is being utilized（Q&P）In the steel of mechanism, it is necessary in initial structure after making quenching " seed " is used as comprising the considerable retained austenite of ratio, to make carbon during carbon partition from martensite to residual austenite Body spreads, so as to increase stability of retained austenite to improve material property.It is in order that considerable comprising ratio in initial structure Retained austenite, hardening heat（QT）Must be in martensite start temperature（Ms）With martensitic traoformation end temp（Mf）It Between.In existing Q＆P steel grades, such as it is set as Ms=500 DEG C, Mf=150 DEG C, needs to need to be set in by QT in this case 200-300 DEG C, this just needs special hardening media to realize quenching, such as salt or oil or special hardening gas.In contrast, In the present invention, it can be ensured that Mf is less than room temperature, therefore even if QT is set as into room temperature or 0-100 DEG C（Medium is water）, The tissue for including abundant residues austenite can be obtained easily, so that it is guaranteed that material property.
Moreover, the present invention's is hot press-formed with adding vanadium (V) element in steel, by technology controlling and process vanadium carbide (VC) or Vanadium（V）With titanium（Ti）, niobium（Nb）Compound carbonitride Deng formation separates out in austenite, one side crystal grain thinning, the opposing party C content in face vanadium carbide (VC) or above-mentioned compound Carbonitride Precipitation consumption matrix, so as to reduce geneva under drop stamping state C content in body, the carbon content in matrix is reduced by crystal grain thinning and vanadium carbide (VC) or above-mentioned compound Carbonitride Precipitation The two mechanism ensure the toughness of material after drop stamping, elongation percentage >=6%, to avoid delayed fracture, meet assemble welding requirement. Work as C：During 0.1-0.17%, more than 0.11% V can ensure that the carbide for separating out enough vanadium reaches above-mentioned target；And work as C： 0.171-0.19, then need to add more vanadium and formed for the carbide of vanadium, meets the target for reducing the carbon content in matrix, V needs to be higher than 0.209%.
The hot press-formed of the present invention can also include at least one of following component with steel：Cr:0-5%, Ti:0- 0.2%, Nb:0-0.2%,Zr:0-0.2%, B:0-0.005%, Ni：0-4%, Cu：0-2%, Mo：0-2%, W：0-2%.
Wherein, it is preferably 5.09 ~ 8% that C content, which ranges preferably from 0.12 ~ 0.17%, Mn content ranges,.Inventor has found, most Pipe carbon content can obtain 1100MPa yield strength substantially when being 0.11, but more than 0.12 carbon content can be further assured that Yield strength is more than 1100MPa.On the other hand, although occurring when carbon content is 0.19 when can avoid hot press-formed substantially crisp Property fracture risk, but less than 0.17 carbon content can be further ensured that material has excellent toughness when hot press-formed.And And in the case where being 0.12-0.17% by C range set, 5.09 ~ 8% Mn can obtain suitable martensitic traoformation just Start temperature, so as to which hardening heat is set as into room temperature, at utmost improve the produceability of parts.
The hot press-formed use steel of the present invention can also have on its surface is selected from Al-Si coating, zinc coat and high temperature Coating among oxide coating.For zinc coat with the peak melting point after ferroalloy at 780 DEG C or so, tradition is hot press-formed to use steel The austenitizing heating-up temperature of use is generally higher than 900 DEG C, during the evaporation of zinc and the thawing of zinc-iron coating can occur, so as to Cause liquid Zn embrittlement, reduce hot press-formed intensity and toughness with steel.In addition, liquid Zn oxidation is serious under high temperature, its Hot press-formed component must use the higher dry ice processing of cost or bead to remove the oxide of top layer zinc, it is ensured that follow-up Coating process.Under preferable case, the hot press-formed full austenite temperature with steel of the invention can be less than 780 DEG C, heat punching Pressure can be carried out below 650 DEG C, can meet the hot press-formed requirement of galvanized sheet.
Preferably, it is hot press-formed to meet following condition with the composition proportion of steel：The hot press-formed steel exist Martensite start temperature after hot press-formed（Ms）Actual measured value be 150-280 DEG C.
Thus, room temperature can be set as by hardening heat by further ensuring that, improve the produceability of parts.
Technical scheme 2 is related to a kind of hot press-formed technique, it is characterised in that the hot press-formed technique Including：Step A：Hot press-formed by technical scheme 1 described hot press-formed is obtained with steel or by preform with steel To prefabricated component be heated to 700-890 DEG C and be incubated, the soaking time 0.1-10000 seconds；Step B：After handling in step It is described it is hot press-formed be transferred to steel or the prefabricated component in mould carry out it is stamping, to obtain formed parts；And Step C：The formed parts are cooled down, average cooling rate is between 0.1-1000 DEG C/s.
In step, if temperature is less than 700 DEG C, austenitizing can be caused insufficient, it is impossible to meet ferrite 0- 10% requirement, on the other hand, temperature can then cause crystal grain to grow up and the carbide dissolution of vanadium and grow up higher than 890 DEG C, performance drop It is low.In addition, the average cooling rate in step C is set between 0.1-1000 DEG C/s, can avoid the formation of ferrite, pearlite, The non-martensite microstructures such as bainite so that material quenching degree is good.
Preferably, the described of technical scheme 1 hot press-formed is heated to steel or the prefabricated component in step 740-850 DEG C and it is incubated, heating-up temperature then can shorten the heat time higher than 740 degree, improve production efficiency, and temperature is less than 850 It DEG C can obtain the Carbide Precipitation of the crystal grain control more optimized and vanadium；Soaking time is preferably the 10-800 seconds, during shorter heating Between may cause to heat uneven unstable, the longer heat time and production efficiency can be caused to reduce.It is further preferred that in step In rapid A by technical scheme 1 it is described it is hot press-formed be heated to 740-780 DEG C with steel or the prefabricated component and be incubated, heat Temperature can more preferably suppress the problem of galvanized sheet liquefies and aoxidized in hot stamping operation less than 780 DEG C.
It is further preferred that in step C, between 1-100 DEG C/s, slower cooldown rate can cause average cooling rate Cool time extends, and reduces production efficiency, and higher cooldown rate enforcement difficulty in hot press-formed technical process is larger.
Technical scheme 3 is related to a kind of formed parts, and it to the hot press-formed of technical scheme 1 by using steel Or the hot press-formed prefabricated component obtained with steel by preform carries out hot press-formed obtain.Preferably, into Shape component is included with undertissue by volume：0.1-5% vanadium carbide or compound carbonitride, 2-15% retained austenite, 0- 10% ferrite, remainder are martensite.
Formed parts elongation percentage >=6% that technique according to the invention scheme 3 obtains, anti-delayed fracture can be met and prevented Only be welded the requirement of cracking.
Preferably, formed parts are handled in the range of 140-220 DEG C by heating and thermal insulation, the time of heating and thermal insulation processing For the 1-100000 seconds.
Preferably, the formed parts are used as automobile component, and the heating and thermal insulation handles the paint during automobile production Carried out in layer baking process, processing time is 5-30 minutes.
Thus, carbon partition can be realized in the baking application step of auto assembly process, without extra addition heat treatment work Sequence, material elongation percentage and toughness are further lifted after coating baking, meet collision performance requirement.
Preferably, the formed parts after heating and thermal insulation processing are included with undertissue by volume：0.1-2%'s Vanadium carbide or compound carbonitride, 5-25% retained austenite, 0-10% ferrite, remainder are martensite.
Formed parts are after the processing of above-mentioned heating and thermal insulation, yield strength >=1100MPa, tensile strength >=1400MPa, extension Rate >=10%, meet collision performance requirement.
The present invention is reduced or avoided and quenched mainly by the carbon content for setting steel product ingredient to reduce in original state martensite Fiery state martensite fragility, so as to ensure the stable performance of component drop stamping state, elongation percentage >=6%, avoid delayed fracture and meet Assemble welding requirement；In addition, through overbaking coating process martensite occurs for the material of drop stamping state into retained austenite Carbon partition, and partial martensite, to the reverse transformation of austenite, finally obtained residual austenite content is more than 5%, and performance It is stable, yield strength >=1100MPa, tensile strength >=1400MPa, elongation percentage >=10%.
Brief description of the drawings
Fig. 1 represents an example of the Technology for Heating Processing of the present invention.
Embodiment
Below, technical scheme is illustrated in conjunction with the embodiments.
The hot press-formed of the present invention includes following component by weight percentage with steel：C: 0.1-0.19%, Mn: 5.09-9.5%, V: 0.11-0.4%, Si+Al: 0-2%.This is hot press-formed to may also include in following component extremely with steel Few one kind：Cr:0-5%, Ti:0-0.2%, Nb:0-0.2%,Zr:0-0.2%, B:0-0.005%, Ni：0-4%, Cu：0-2%, Mo： 0-2%, W：0-2%, the content of these compositions is equally by weight percentage.The hot press-formed composition proportion of steel causes Its martensite start temperature actual measured value after hot press-formed is 150-280 DEG C.
Hot press-formed the reason for being limited as described above with the chemical composition of steel of the present invention, is as described below.
C ：0.1% to 0.19%
Carbon is generally the least expensive intensified element, and the strong intensity for improving steel can be dissolved by gap.And the rise meeting of carbon content It is strong to reduce full austenite temperature（Ac3）, the energy is saved so as to reduce heating-up temperature.Although carbon can reduce martensitic phase strongly The tissue of martensite start temperature≤280 DEG C and steel will when becoming start temperature, but having to meet alloy design Ask, and carbon is most important gap solution strengthening element, therefore the lower limit of carbon content is 0.1%.But too high carbon content pair The mechanical property performance impact of steel is very big, timber intensity can be caused too high and toughness decline.0.19% is set to for the upper limit of this carbon, Carbon content can cause brittle fracture under the hot press-formed state of steel higher than the numerical value.It is further preferred that C content range is 0.12~0.17%。
Mn ：5.09% to 9.5%
Manganese is the important element in the present invention.Manganese is good deoxidier and desulfurizing agent.Manganese is among the austenite stabilizing elements, can be expanded Austenite region, reduce Ac3 temperature.Manganese has the quenching degree that excellent suppression austenite improves steel to ferritic transformation Effect.Heating-up temperature during in order to reduce heat treatment, being defined to 5.09% under manganese, to ensure martensite start temperature ≤ 280 DEG C, while ensure that the Ac3 of material is hot press-formed to facilitate its galvanized sheet to carry out less than 780 DEG C.Too high manganese adds Add, material can be caused to form brittle ξ martensites after quenching, therefore the upper limit of manganese is set to 9.5%.It is further preferred that Mn's contains Amount scope is 5.09-8%.
V：0.11-0.4%
Vanadium separates out as strong carbide, and the carbide by separating out vanadium can play crystal grain thinning, lift the effect of intensity.Vanadium leads to Cross and separate out vanadium carbide in austenitization stage and drop stamping stage, on the one hand refine original austenite grains, on the other hand drop Carbon content in low matrix, so as to ensure that the carbon content after hot forming in martensite is relatively low, the present invention is by adding v element And the carbide of vanadium is separated out to realize the control to the carbon content in martensite after hot forming, so as to ensure hot forming state material Elongation percentage and specific elongation steadily.Less than 0.11% V DeGrains, the design of material demand of the present invention is not reached.It is but big The addition of amount v element can cause VC sizes to increase, and can bring the lifting of steel product cost, to ensure initial state after hot forming The stability of steel elongation percentage, V content should be less than being equal to 0.4%.
Si+Al：0-2%
Silicon and aluminium can suppress the formation of carbide, when being incubated after steel is quenched to room temperature less than Ac1 temperature ranges, silicon and Aluminium can suppress the precipitation of carbide in martensite, and make carbon with assigning in retained austenite, improve stabilization of austenite, improve The strength and ductility product of steel.During industrial production, excessive Al can in continuous casting stopped nozzles, increase the difficulty of continuous casting, and Al can be improved Material martensite start temperature and full austenite temperature, the organizational controls temperature requirement of steel in the present invention is not met.Silicon Content height can cause the impurity in steel more.The present invention uses 140-220 DEG C of cryogenic carbon partition, in this low-temperature range cementite Formation is suppressed, it is only possible to can form a part of transiens carbide, but the formation of this partially carbonized thing is not significantly affected by The toughness of material, and Si and Al a large amount of additions can not also suppress the generation of transiens carbide, thus the present invention independent of Si+Al is less than or equal to 2% in Si+Al addition, the present invention.
Cr：0-5%
Chromium is also to improve material quenching degree element, and can also reduce martensite start temperature, therefore is designed according to alloy The carbon content in requirement and steel on martensite start temperature, determines the percentage composition of manganese and chromium in steel.Manganese and chromium The one of which of both elements or compound addition.Cr can not preferably add because cost is higher.
Ti、Nb、Zr：It is 0-0.2%
Ti, Nb, Zr raise the crystal grain refinement of steel, intensity and obtain good heat treatment characteristic.Ti, Nb, Zr concentration mistake It is low, effect is not had, and can increase unnecessary cost more than 0.2%.Because of steel of the present invention setting because of rational C and Mn Meter, the intensity more than 1600MPa and preferable ductility can be obtained, to reduce cost, may not necessarily preferably add in addition Ti, Nb, Zr。
B：0-0.005%
B is segregated in austenite grain boundary, is prevented ferritic forming core, can be improved the quenching degree of steel strongly, can be notable after heat treatment Improve the intensity of steel.B contents can not significantly improve its effect higher than 0.005%.Because the high Mn of steel of the present invention is designed, Possess higher quenching degree, to reduce cost, may not necessarily preferably add B in addition.
Ni：0-4% ；Cu：0-2%
Ni can improve the intensity of steel, and keep good plasticity and toughness.Ni concentration is more than 4.0%, then can be added to This.Cu can improve intensity and toughness, particularly atmospheric corrosion performance.Cu content is more than 2.0%, then processability may deteriorate, heat The process of rolling, which can form liquid phase, to be caused to ftracture, and high Cu contents cause unnecessary cost to increase.Because steel of the present invention is because rationally C and Mn design, the intensity more than 1600MPa and preferable ductility can be obtained, to reduce cost, preferably may not be used Ni, Cu must be added in addition.
Mo、W：It is 0-2%
The quenching degree of Mo, W raising steel can effectively improve the intensity of steel.In addition, even in due to during hot forming with mould Have it is unstable contact and make steel cooling it is insufficient in the case of, due to the quenching degree of Mo and the W raising brought, steel still may be used There is suitable intensity.In the case of 2.0%, extra effect can not be obtained, cost can be increased on the contrary.Because of the present invention The high Mn designs of steel, have possessed higher quenching degree, to reduce cost, may not necessarily preferably add Mo, W in addition.
P, the impurity that S, N etc. are difficult to avoid that
In general, phosphorus is the harmful element in steel, can increase the cold brittleness of steel, weldability is degenerated, and reduces plasticity, makes Cold-bending property degenerates.Sulphur is also harmful element under normal circumstances.Steel is produced red brittleness, reduce the ductility and welding performance of steel. Nitrogen is a kind of element being inevitably present in steel.Nitrogen is similar with the effect of carbon, and helps to bakee and harden.
To the present invention it is hot press-formed carried out with steel or prefabricated component it is hot press-formed.
In one embodiment, by it is above-mentioned it is hot press-formed be heated to 700-890 DEG C with steel or prefabricated component and be incubated, protect The warm time 0.1-10000 seconds（Step A）.The technique used in experiment is incubated 5 minutes at 750-840 DEG C.As shown in figure 1, heating Temperature can be 780 DEG C, be incubated 5 minutes.Then, be transferred in mould carry out it is hot press-formed（Step B）, and by formed parts Less than 100 DEG C are cooled to air cooling or other manner, average cooling rate is between 0.1-1000 DEG C/s（Step C）.One section After time, then the component after processing is passed through into heating and thermal insulation at 140-220 DEG C and handled, the time is the 1-100000 seconds, to carry out carbon Partition processing, is cooled to room temperature afterwards, and cooling medium can be and be not limited to sky gas and water, oil, die surface.Adopted in experiment Technique is to carry out heating and thermal insulation processing at 150-210 DEG C, and the time is 5-30 minutes.As shown in figure 1, the heating and thermal insulation is handled It can be carried out during the paint baking during automobile production.
Table 1 is steel product ingredient used by embodiment, and steel can be prepared through following technique turns into sheet material.That is, casting base exists Forging turns into slab after 1200 degree of insulation 3h, and slab is incubated 10h to carry out grinding off skin decarburization after homogenization at 1200 DEG C Layer, hot rolling is carried out between 800 DEG C ~ 1200 DEG C to form hot rolled plate after being heated to 1200 DEG C of insulation 1h afterwards.By hot rolling acid-cleaning Plate is incubated 10h simulation bell-type annealings at 600 DEG C and is advantageous to cold rolling to reduce the intensity of hot rolled plate, and then hot rolling acid-cleaning is annealed Plate is cold-rolled to such as 1.5mm thickness, then cold-reduced sheet is made annealing treatment to simulate industrial cold rolled sheet continuous annealing or coated plate Production procedure, acquisition is hot press-formed to use steel plate.
Wherein, BT series is the steel of the present invention, and CT series is comparative steel, and the composition of CT series steel is beyond the present invention Scope.
Table 2 is used technique, and table 3 is the property for the formed parts that the steel of table 1 obtain after the PROCESS FOR TREATMENT of table 2 Energy.
The main chemical compositions of the steel of table 1
C Mn Si V
BT1 0.15 7.5 0.2 0.15
BT2 0.15 7.5 0.2 0.25
BT3 0.17 6.4 0.19 0.34
BT4 0.12 7.43 0.21 0.18
CT1 0.22 8 1.26 -
CT2 0.24 7.3 1.21 0.25
CT3 0.17 7.2 0.2 -
The Technology for Heating Processing of the steel of table 2
The mechanical property of the formed parts of table 3
Handled without foregoing heating and thermal insulation（Baking is handled）Formed parts by volume include with undertissue：0.1-5% Carbide containing V or compound carbonitride, 2-15% retained austenite, 0-10% ferrite, remainder be martensite.From 1-1,1-2,1-3,1-4,1-5,2-1,2-2,2-3,2-4,3-1,4-1 in table 3 understand that the elongation percentage of these formed parts is Reach more than 6%.
Formed parts after the processing of foregoing heating and thermal insulation are included with undertissue by volume：0.1-2%'s is carbonized containing V Thing or compound carbonitride, 5-25% retained austenite, 0-10% ferrite, remainder are martensite.1- from table 3 Knowable to 1-200,1-2-200,1-5-170,2-4-180,2-4-200,3-1-200,4-1-200, the surrender of these formed parts Intensity reaches more than 1100MPa, and tensile strength reaches more than 1400MPa, and elongation percentage reaches more than 10%.
In contrast, which kind of Technology for Heating Processing no matter steel CT1, CT2, CT3 of comparative example use, and can not meet simultaneously Four performance indications of steel of the present invention：Drop stamping state（Before implementing carbon partition）Elongation percentage >=6%；Carbon partition（Such as application is dried It is roasting）Yield strength >=1100MPa, tensile strength >=1400MPa, elongation percentage >=10% afterwards.Especially from CT1-1, CT1-2, CT2- 1st, CT2-2, CT3-1, CT3-2 understand that the possibility of brittle failure occurs before carbon partition is implemented for steel CT1, CT2, CT3 of comparative example It is high, and the steel of the present invention can also reach more than 6% elongation percentage before carbon partition is implemented, and avoid the generation of brittle failure, energy Fully meet assemble welding requirement.
The formed parts of the present invention can be used for land automotive high intensity component, including but not limited to B posts reinforcement, insurance Thick stick, door anti-collision joist and wheel spoke etc..
Above example and experimental data are intended to exemplarily illustrate the present invention, it will be apparent to those skilled in the art It is that the present invention is not limited only to these embodiments, without departing from the scope of the invention, various changes can be carried out.

Claims (16)

1. hot press-formed steel are used a kind of, it is characterised in that described hot press-formed to be included by weight percentage with steel Following component：C: 0.1-0.19%,Mn: 5.09-9.5%,V: 0.11-0.4%,Si+Al:0-2%；Wherein C and V cooperation is also Meet following alternative one：1）C：0.1-0.17%, V：0.11-0.4%；2） C：0.171-0.19, V：0.209-0.4%.
2. hot press-formed steel are used as claimed in claim 1, it is characterised in that described hot press-formed also to be wrapped with steel Containing at least one of following component：Cr:0-5%, Ti:0-0.2%, Nb:0-0.2%,Zr:0-0.2%, B:0-0.005%, Ni： 0-4%, Cu：0-2%, Mo：0-2%, W：0-2%.
3. hot press-formed as claimed in claim 1 or 2 use steel, it is characterised in that C content scope is 0.12- 0.17%, Mn content range are 5.09-8%.
4. hot press-formed steel are used as claimed in claim 1 or 2, it is characterised in that described hot press-formed to use steel There is the coating among being selected from Al-Si coating, zinc coat and high-temperature oxydation coating on its surface.
5. hot press-formed steel are used as claimed in claim 1 or 2, it is characterised in that described hot press-formed to use steel Composition proportion meet following condition：The hot press-formed martensite start temperature with steel after hot press-formed Actual measured value is 150-280 DEG C.
6. a kind of hot press-formed technique, it is characterised in that the hot press-formed technique includes：
Step A：Hot press-formed any one of claim 1 to 5 with steel or described hot press-formed is used into steel The prefabricated component obtained by preform is heated to 700-890 DEG C and is incubated, the soaking time 0.1-10000 seconds；
Step B：Hot press-formed be transferred to steel or the prefabricated component in mould after handling in step is carried out It is stamping, to obtain formed parts；And
Step C：The formed parts are cooled down, average cooling rate is between 0.1-1000 DEG C/s.
7. hot press-formed technique as claimed in claim 6, it is characterised in that in step, heating-up temperature 740-850 ℃。
8. hot press-formed technique as claimed in claim 7, it is characterised in that in step, heating-up temperature 740-780 ℃。
9. hot press-formed technique as claimed in claim 7, it is characterised in that in step C, average cooling rate is in 1- Between 100 DEG C/s.
10. a kind of formed parts, it is characterised in that the formed parts pass through to the heat any one of claim 1 to 5 It is stamping with steel or the hot press-formed prefabricated component obtained with steel by preform carry out it is hot press-formed come Obtain.
11. formed parts as claimed in claim 10, it is characterised in that the formed parts are included with the following group by volume Knit：0.1-5% vanadium carbide or compound carbonitride, 2-15% retained austenite, 0-10% ferrite, remainder are horse Family name's body.
12. formed parts as claimed in claim 10, it is characterised in that the formed parts have more than 6% elongation percentage.
13. the formed parts as any one of claim 10 to 12, it is characterised in that the formed parts are in 140- Handled in the range of 220 DEG C by heating and thermal insulation, the time of heating and thermal insulation processing is the 1-100000 seconds.
14. formed parts as claimed in claim 13, it is characterised in that the formed parts are used as automobile component, described to add Hot isothermal holding is carried out during the paint baking during automobile production, and processing time is 5-30 minutes.
15. formed parts as claimed in claim 13, it is characterised in that the formed parts are included with the following group by volume Knit：0.1-2% vanadium carbide or compound carbonitride, 5-25% retained austenite, 0-10% ferrite, remainder are horse Family name's body.
16. formed parts as claimed in claim 13, it is characterised in that the formed parts have bending for more than 1100MPa Take intensity, more than 1400MPa tensile strength and more than 10% elongation percentage.
CN201711063360.6A 2017-11-02 2017-11-02 Hot press-formed steel, hot press-formed technique and formed parts Pending CN107815612A (en)

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KR1020237012517A KR20230054500A (en) 2017-11-02 2018-10-29 Steel used for hot stamping, hot stamping process and formed component
JP2020544088A JP7269588B2 (en) 2017-11-02 2018-10-29 Steels used for hot stamping, hot stamping methods and formed components
US16/760,979 US20200263271A1 (en) 2017-11-02 2018-10-29 Steel used for hot stamping, hot stamping process and formed component
PCT/CN2018/112367 WO2019085855A1 (en) 2017-11-02 2018-10-29 Steel used for hot stamping, hot stamping process and formed component
KR1020207015802A KR20200072552A (en) 2017-11-02 2018-10-29 Steel for hot stamping, hot stamping process and molded components
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