CN108474081A - For stamping steel and its formed parts and heat treatment method - Google Patents

For stamping steel and its formed parts and heat treatment method Download PDF

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CN108474081A
CN108474081A CN201580085081.2A CN201580085081A CN108474081A CN 108474081 A CN108474081 A CN 108474081A CN 201580085081 A CN201580085081 A CN 201580085081A CN 108474081 A CN108474081 A CN 108474081A
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steel
steel plate
austenite
formed parts
stamping
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CN108474081B (en
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易红亮
杜鹏举
杨达朋
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Easyforming Steel Technology Co ltd
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Easyforming Steel Technology Co ltd
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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
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/0294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a localised treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • 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
    • C21D2221/00—Treating localised areas of an article
    • C21D2221/10—Differential treatment of inner with respect to outer regions, e.g. core and periphery, respectively

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

It being used for stamping steel the present invention relates to a kind of, it is characterized in that, the steel include 0.22 ~ 0.48% C, 5 ~ 9.5% Mn, 0.5 ~ 3.0% Si+Al and the Fe of surplus and inevitable impurity by weight percentage, the wherein described steel are hot rolling, hot rolling acid-cleaning, hot rolling acid-cleaning coating coil of strip or steel plate or cold rolled annealed, cold rolling coating coil of strip or steel plate.The invention further relates to based on above-mentioned steel process for stamping and forming and stamping component, be mainly used for but be not exclusively for automobile structure.The coil of strip or steel plate or formed parts are heated to 650 ~ 780 DEG C of heat preservations 0.5 ~ 60 minute and obtain, containing having more than 30%（With volume fraction）Retained austenite.Its mechanical property reaches：0.5 ~ 1.2GPa of yield strength, 1.0 ~ 1.5GPa of tensile strength, strength and ductility product（Tensile strength × elongation percentage）25GPa% or more.The invention further relates to the formed parts of the steel and heat treatment methods.

Description

For stamping steel and its formed parts and heat treatment method Technical field
The present invention relates to a kind of for stamping steel, and stamping component and heat treatment method based on above-mentioned steel.
Background technique
Energy-saving and emission-reduction have become the important indicator of automobile, realize that the important means of these targets is the lightweight of automobile.Reducing car weight can be improved fuel utilization ratio and reduces exhaust gas discharge.It guarantees safety while loss of weight, the use of high strength steel just becomes inexorable trend.At present, for example the advanced high-strength steel of the first generation such as two-phase (DP) steel, multiphase (CP) steel, phase change induction plasticity (TRIP) steel, martensite steel (its strength and ductility product, that is, tensile strength × breaking elongation is 15~20GPa%) has been widely applied in automotive field, and plays important function to automotive light weight technology.However, the processability and intensity of the advanced high-strength steel of the first generation are still to be improved, to meet the Automobile Design demand increasingly promoted.With the strength and ductility product for the advanced high-strength steel of the second generation that twinning induced plasticity (TWIP) is representative up to 60GPa%, and have been realized in industrialization, but due to a large amount of additions of alloying element, cause its manufacturing cost high, production difficulty is big, and the alloying element largely added is degrading the welding performance of steel, to not be widely used.The main purpose for developing the advanced high-strength steel of the third generation is exactly to obtain balance between the cost of material and the performance of material, and strength and ductility product is generally in 25GPa% or more.
It is in progress in the light of recent researches, manganese content would be possible to become the advanced automobile steel that next-generation intensity is more than 1GPa or more with its outstanding mechanical property in the advanced high-strength steel of 5wt% to 30wt%.The Plastic Deformation Mechanism of the height of manganese content and steel in steel, manganese steel is divided into three classes: Mn content is in 4~8wt%, general phosphorus content is lower, it organizes to be retained austenite and ferritic duplex structure, its strengthening mechanism is generally TRIP effect, retained austenite undergoes phase transition in deformation process, cause high work hardening rate and generally 30% or so elongation percentage；Mn content is in 12~22wt%, and the initial tissu of such steel is austenite structure, and stacking fault energy is generally 20mJ/m2, since its strengthening mechanism is TWIP (twinning induced plasticity), such steel has the elongation percentage of outstanding work hardening rate and general 60% or so；For Mn content in 22~30wt%, strengthening mechanism is MBIP (Microband-induced plasticity, micro-strip induced plastic), and such steel carbon content with higher and aluminium content, stacking fault energy is in 80mJ/m2.Ultra small scale manufacture band is formed in deformation process leads to the elongation percentage of high work hardening rate and general 60%.
The requirement of comprehensive current energy-saving and emission-reduction and the advanced high-strength steel of the third generation, manganese content are widely noticed in 3~10% medium managese steel.The rolled tissue of medium managese steel is generally martensitic structure, then select suitable annealing temperature, time enough is kept the temperature in two-phase section, obtain austenite and ferritic duplex structure, and the process that carbon and manganese are spread into austenite is completed in the process, stablize austenite to room temperature, obtains more austenite structure.Deformation and obstruction crack propagation using retained austenite, obtain higher intensity and elongation percentage.Higher aluminium generally can be added in order to expand the temperature range of two-phase section, the addition of more aluminium can cause annealing temperature to increase, and coarse grains cause yield strength to reduce.The design of manganese TRIP steel in general, carbon content is lower, and generally 0.2% hereinafter, its tensile strength is generally in 1000MPa or so, yield strength is in 600MPa hereinafter, elongation percentage is below 30%.
The control of retained austenite has a major impact the strong plasticity of steel.There are many factor for influencing retained austenite Plastic Deformation Mechanism, including the stacking fault energy of mechanical stability and austenite.Wherein carbon is cheap solution strengthening element and among the austenite stabilizing elements, and carbon has an impact on stacking fault energy and the crystallite dimension by influencing heat treatment process change steel.
Stacking fault energy is that the deformation mechanism of austenite has a major impact.With the reduction of stacking fault energy, Plastic Deformation Mechanism is followed successively by dislocation movement by slip mechanism, deformation twin and martensitic traoformation occurs.The factor for influencing stacking fault energy is mainly the ingredient and grain size of austenite.Carbon, manganese and aluminium will improve the stacking fault energy of austenite, and a small amount of silicon can improve the stacking fault energy of austenite and can play the role of solution strengthening and improve the yield strength and tensile strength of steel, and chromium reduces the stacking fault energy of austenite.The crystal grain of austenite, which becomes larger, can provide nucleation site and the reciprocation of shear band of more faults, but can cause the reduction of the elastic strain energy and shear-deformable strain energy of lattice trimming simultaneously and cause martensitic traoformation.The crystal grain or slat dimension of austenite are tiny to improve its stacking fault energy, and influences its Plastic Deformation Mechanism.
Summary of the invention
It is an object of the present invention to provide a kind of high-strength tenacities and the stamping of high energy absorption capacity to use steel, and stamping component and heat treatment method based on this steel.Steel heat treatment of the invention is in two-phase section isothermal holding, and conducive to the accurate control for realizing temperature, carbon manganese content is high, and harden ability is good, is required cooling velocity low.By the steel plate after heat treatment, mechanical mechanics property reaches: 0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, strength and ductility product (tensile strength × elongation percentage) 25GPa% or more.Through on mold it is stamping be component, be mainly used for but be not limited to automobile structure.
According to the first aspect of invention, it provides a kind of for stamping steel, the steel include 0.22~0.48% C by weight percentage, 5~9.5% Mn, 0.5~3.0% Si+Al and Fe of surplus and inevitable impurity, wherein the steel are hot rolled coil (plate), hot rolling acid-cleaning rolls up (plate), cold rolled annealed volume (plate), cold rolling coating rolls up one of (plate), it is heated to 650~780 DEG C of heat preservations before stamping (wherein may be selected 680, 700, 720, the temperature such as 750 DEG C) 0.5~60 minute (it wherein may be selected 5, 10, 20, 30, 40, 50 equal times) heat treatment and obtain.Go out the variation of manganese, carbon and other alloying elements in austenite when two-phase section annealing balances using thermodynamics soft com-puting.Then according to the ratio of balance Shi Gangzhong austenite and based on martensitic traoformation K-M formula, fM=1-exp (- 0.011 (Ms-QT) (wherein QT=room temperature, Ms is found out according to the variation of element in austenite), it calculates to obtain the corresponding annealing temperature of maximum retained austenite, according to different-alloy ingredient and manufacturing process, at this temperature 0.5 minute~1 hour.The selection of binding constituents design and processes, obtains the volume fraction of retained austenite 30%~60%, martensite (ferrite) tissue of volume fraction 40%~70% and 0~3% carbide.Due to carbon and manganese element in austenite diffusion velocity than several orders of magnitude slow in martensite, the regional area that once will cause austenite is enriched with more carbon and manganese element, carbon content in final actual measurement retained austenite is 0.5% or more, manganese content is greater than 7%, and the crystal grain of austenite is less than 1 μm.Steel plate generates martensitic traoformation and deformation twin in deformation process inside austenite, is conducive to the energy absorption capacity and elongation percentage that improve steel plate.
The ingredient design of steel of the invention based on manganese in high-carbon, carbon content is between 0.22~0.48%, and preferably 0.25~0.45%, manganese content is between 5~9.5%, and preferably 6~8%.Carbon and manganese are all among the austenite stabilizing elements, the austenitizing temperature and martensite of reduction steel that can be strong start phase transition temperature, during annealing heat-treatment, form austenite/ferritic lath alternating structure, and carbon and manganese partition are into austenite, make austenite stablize to room temperature hereinafter, in deformation process occur TRIP effect gradually mutually become martensite, improve the intensity and ductility of steel；Particularly, the steel of the ingredient design and annealing process that optimize in steel of the present invention, retained austenite carbon with higher and manganese, the stacking fault energy of partial austenitic are higher, deformation twin is formed in deformation process, can further improve work hardening rate and improves the strength of materials and ductility simultaneously.It when carbon and lower manganese content, to obtain more austenite, needs to improve with its preferred annealing temperature, causes the crystal grain of austenite coarseer, and cause stabilization of austenite poor, the obdurability of steel reduces in deformation process.When carbon content is higher, hypereutectoid tissue may be will form, and form more coarse carbide and deteriorate the mechanical property of steel.It is found by the applicant that carbon content control can obtain preferable strong plasticity between 0.22~0.48% the control of Mn content 5~9.5%.
According to a preferred embodiment of the present invention, the steel further include at least one of following component: Cr:0.001%~5%；Mo:0.001%~2.0%；W:0.001%~2.0%；Ti:0.0001%~0.4%；Nb:0.0001%~0.4%；Zr:0.0001%~0.4%；V:0.0001%~0.4%；Cu:0.0005%~2%；Ni:0.0005%~3.0%；B:0.0001%~0.005%.Pass through the combination of at least one of these ingredients and above-mentioned basis, it can further ensure that the ultra-high strength and toughness matching of punching component, so that its mechanical mechanics property reaches: 0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, strength and ductility product (tensile strength × elongation percentage) 25GPa% or more.
According to a preferred embodiment of the present invention, the steel include hot rolled steel plate, cold-rolled steel sheet or the steel plate with coated layer.The steel plate with coated layer can be zinc coating steel plate, it is the hot rolled steel plate or cold-rolled steel sheet for being formed on metal zinc layers.The zinc coating steel plate includes plating one of (GE) selected from galvanizing by dipping (GI), zinc-plated annealing (GA), zinc plating or zinc-ferroelectricity.The steel plate with coated layer is to be formed on the hot rolled steel plate of al-si layer or the steel plate of cold-rolled steel sheet or organic coating or the steel plate with other galvanneal coatings.
According to an aspect of the invention, there is provided a kind of process for stamping and forming comprising the steel with mentioned component are provided, it is stamping by being carried out after the heat treatment process processing for being heated to 650~780 DEG C of heat preservations 0.5~60 minute.Alternatively, the steel directly carry out cold stamping or it is hot press-formed after, be heated to 650~780 DEG C heat preservation 0.5~60 minute heat treatment process processing after obtain required stamping parts.With the raising of carbon and manganese element content, the harden ability of steel can be greatly improved, so that can obtain full martensitic structure, therefore intensity with higher under the conditions of air-cooled after hot rolling, and cause cold rolling difficult.To solve the problems, such as cold rolling difficulty, applicant combines production technology, proposes solution.It is generated between 630~750 DEG C of temperature in the carbide of steel, it is consistent with the softening annealing process that industrial bell furnace routinely uses, make the austenite of carbide precipitate and generation reverse transformation in steel, that is, reduce the intensity of steel, and improves the elongation percentage of steel convenient for cold rolling.
According to another aspect of the present invention, a kind of stamping component is provided, the stamping component stamping is prepared with steel by process for stamping and forming of the invention by of the invention.
Steel of the invention or its microstructure of stamping component by volume include: 30% or more retained austenite, 70% martensite (ferrite) tissue below, or including 3% carbide below, reach to obtain mechanical property: 0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, strength and ductility product (tensile strength × elongation percentage) 25GPa% or more.Preferably, originally The steel of invention or its stamping component are after the heat treatment process by being heated to 650~780 DEG C of heat preservations 0.5~60 minute, it include: 30% to 60% retained austenite with areametric microstructure, the martensite or ferrite of 40% to 70% body-centered cubic crystal structure, the carbide lower than 3%.Preferably, the retained austenite and martensite or ferrite can distribute alternately in lath-shaped or, its lath thickness is between 10~300nm.It preferably, by weight percentage may include the Mn more than or equal to the 7% and C more than or equal to 0.5% in austenite.Preferably, steel of the invention or its stamping component are during stress deformation, retained austenite passes through phase-change induced plastic, or twinning induced plasticity effect is assisted simultaneously, improve the matching of its intensity and ductility, so that mechanical property reaches: 0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, strength and ductility product >=25GPa%.
According to a preferred embodiment of the present invention, the stamping component can be used at least one of automotive safety structural member, enhancing structure part and high tough automobile structure.More specifically, the formed parts can be used at least one of B column reinforcement, bumper and door anti-collision joist, wheel spoke.Certainly, the formed parts can be used for the occasion for the component for requiring the high intensity of lightweight to increase ductility in other all terrestrial vehicles.
According to the technique and scheme of the present invention, it can achieve the advantages that
1. being made by the control for improving carbon content and reasonable manganese content there are the retained austenite of a large amount of high stability in steel, TRIP effect occurs in deformation process, improves the strong plasticity of steel 30% or more for austenite content volume fraction；
2. auxiliary deformation is more advantageous to the strong plasticity for improving steel in situations where it is preferred, TWIP effect occurs in deformation process for partially stabilized austenite；
3. yield strength significantly improves compared with middle Mn-TRIP steel, the matching of tensile strength and elongation percentage is also significantly improved；
4. simple production process, lower to cooling rate requirement, conducive to the control for the microstructure for realizing steel and the stability of guarantee mechanical property.
In particular, it is compared with patent document CN102021472B (its artwork can refer to Fig. 7), the present invention improves materials A c because higher Si and Al is added1Temperature, it improves for the softening annealing temperature that cold rolling is prepared to 630-750 DEG C (different from 450~630 DEG C of its claim of softening annealing temperature), it increases in its elongation percentage and rolling deformation ability relatively comparison patent, it is consistent with the softening annealing process that industrial bell furnace routinely uses, be conducive to organization of production.And the present invention, which can be used after hot rolled plate directly carries out annealing heat preservation 0.5-60min at 650-780 DEG C, can obtain ideal performance.And the present invention passes through C the and Mn alloy design of optimization, and optimization Heat treatment design makes it have the reasonable high-volume fractional retained austenite (30%~60%) of stability, therefore the tensile strength with 1000MPa or more, and strength and ductility product 25GPa% or more.For ideal performance can also be obtained after 650-780 DEG C of heat preservation 0.5-60min by directly stamping or hot press-formed component.
It is compared with patent document CN101638749B, the design that the present invention optimizes, makes its finally only once Ac1The 650-780 DEG C of above annealing can be obtained required structure property for 0.5~60 minute, and (subsequent with its processing route need to further Ac1100 DEG C to Ac below1At a temperature of heat preservation in 1~10 hour complicated technology it is different), steel of the invention can directly obtain required tissue and performance after the heat treatment of industrial continuous annealing furnace.The process ration figure of the present invention and comparison patent can refer to Fig. 8.
The reverse transformation of austenite is in Ac in CN101638749B1100 DEG C to Ac below1At a temperature of 1-10 hours.The alloying element partition processing of hot rolled plate is identical as austenite reverse transformation treatment process.
It is compared with patent document CN104846274A, its steel is handled merely through a step in the present invention, i.e. 650-780 DEG C is annealed 0.5~60 minute, the austenite content of formation is much higher than the comparison patented technology, reach 30%~60% retained austenite, therefore its matching with better intensity and ductility, strength and ductility product reach 25GPa% or more；Its stamping component is annealed 0.5~60 minute through 650-780 DEG C and is handled, and heat treatment process and microstructure are different from comparing patented technology, and have higher ductility, and elongation percentage is above 18%, and strength and ductility product reaches 25GPa% or more.
The initial hot rolling microstructure of steel of the present invention is the martensitic structure of lath-shaped, utilizes the thinner feature of martensite lath.It anneals in two-phase section, complete the partition of carbon and manganese, the austenite of the reverse transformation made saves the form of martensite lath, and wherein there are enough carbon contents and manganese content, enable to be stabilized at room temperature, the elongation percentage of steel is improved using the compatible deformation of retained austenite and annealing martensite.
The enrichment of a large amount of carbon contents in the crystal grain or slat dimension that reverse transformation obtains tiny austenite and austenite; cause the stacking fault energy of austenite to increase, make austenite that TWIP/TRIP effect occur in deformation process, improves the work hardening rate of steel; inhibit yield point elongation, improves the strong plasticity of steel.
For the present invention by improving the carbon content in steel and controlling the content of manganese, obtained hot rolling microstructure is martensitic structure.Then it is kept the temperature in two-phase section, obtains austenite and ferritic duplex structure, and make on the carbon and rich manganese to austenite in steel during this period, the design based on appropriate carbon and manganese obtains the retained austenite of higher carbon content and manganese content at room temperature.
Detailed description of the invention
Fig. 1 is the heat treatment process figure of the embodiment of the present invention, and HR indicates hot rolling；CR indicates cold rolling；
Fig. 2 is the engineering stress strain curve after No. 1 steel of the embodiment of the present invention keeps the temperature 10h at 650 DEG C of soft annealing；
Fig. 3 is that No. 1 steel of the embodiment of the present invention keeps the temperature the microstructure of parallel-segment after 10h post-tensioning deformation at 650 DEG C of soft annealing；
Fig. 4 is the engineering stress strain curve of No. 5 steel cold rolling plate mark C treatment process at normal temperature；
Fig. 5 is the microstructure of No. 5 steel cold rolling plate mark C treatment process；
Fig. 6 is before deforming after No. 5 steel cold rolling plate mark C treatment process and deformed X ray diffracting spectrum；
Fig. 7 is the heat treatment process figure of comparison patent document CN102021472B；
Fig. 8 is the process ration figure of the present invention with comparison patent CN102021472B.
Specific embodiment
Below with reference to embodiment, the present invention will be described in more detail.Embodiment is intended to explain illustrative embodiment of the invention, and the present invention is not limited to these Examples.
The reason of chemical component (by weight percentage) of steel of the invention limits is as follows:
C:0.22 to 0.48%
Carbon is generally the least expensive intensified element, and the strong intensity for improving steel can be dissolved by gap.In addition, the raising of carbon content can reduce Ac strongly3, so that it is energy saving to reduce heating temperature.But the welding performance that excessively high carbon content will lead to steel is bad, and may lead that timber intensity is excessively high, and the mold damage in heat forming processes reduces the service life of mold.The upper limit of carbon is set as 0.48% thus.To guarantee to be enriched with enough carbon in austenite, the lower limit of carbon content is 0.2%, preferably 0.25~0.45%.
Mn:5% to 9.5%
Manganese is the important element for improving stabilization of austenite.Manganese can expand austenite region, reduce Ac3Temperature.Manganese has the function of that excellent inhibition austenite improves the harden ability of steel to ferritic transformation.In order to guarantee that enough austenites exist in ambient-temp-stable, being limited to 5% under manganese.Manganese increases the resistance to corrosion that can weaken steel and reduces welding performance, and is easy to cool down in quenching Will form twin crystal martensite in the process reduces the strong plasticity of material.So the upper limit of manganese is set as 9.5%.
Si+Al:0.5% to 3.0%
Silicon and aluminium can inhibit the formation of carbide, and silicon and aluminium can improve Ac1Temperature improves the temperature of cold rolling front spring sofening treatment, consistent with the softening annealing process that industrial bell furnace routinely uses, and is able to suppress larger-size cementite and generates.During steel is cooled to room temperature, silicon and aluminium are able to suppress the precipitation of cementite.And silicon can play the role of solution strengthening, improve the yield strength of steel, and aluminium can obviously expand the temperature range of two-phase section, expand process window, so the lower limit of Si+Al is 0.5%.When industrial production, excessive Al can in continuous casting stopped nozzles, increase the difficulty of continuous casting.It is more that silicone content height will cause the impurity in steel.Therefore the upper limit of Si+Al is set as 3.0%.
Cr, Mo, W:0.001% are to 2.0%
Cr, Mo, W improve the harden ability of steel, can effectively improve the intensity of steel.Cr can make even tissue, increase temper resistance, and the alloyed cementite that Cr and C are formed can hinder Austenite Grain Growth, improve the toughness of steel.In addition, Mo can prevent temper brittleness, increase remanent magnetism and coercivity and the corrosion stability in certain media.Mo can reduce the tendency that carbide is distributed in crystal boundary.W play the role of with Mo it is similar, W can reduce steel superheated susceptivity, increase harden ability and improve hardness.When concentration is lower than 0.001%, then enough harden ability cannot be obtained, even if can not obtain additional effect in the case where being greater than 2.0%, will increase cost instead.
Ti, Nb, Zr, V:0.0001% are to 0.4%
Ti, Nb, Zr and V make the crystal grain refinement of steel, intensity increase and obtain good heat treatment characteristic.The concentration of Ti, Nb, Zr and V are too low, do not have effect, and are greater than 0.4% and will increase unnecessary cost.
Cu, Ni:0.0005% are to 2.0%
Cu can improve intensity and toughness, especially atmospheric corrosion performance.The content of Cu is greater than 2.0%, then processability may deteriorate.Ni can improve the intensity of steel, and keep good plasticity and toughness.The content of Ni cannot get due effect lower than 0.0005%, and the concentration of Ni is greater than 2.0%, then will increase cost.
B:0.0001% to 0.005%
B is segregated in austenite grain boundary, is prevented ferritic forming core, can be improved the harden ability of steel strongly, the intensity of steel is remarkably improved after heat treatment.The content of B is lower than 0.0001%, then does not have effect.B content can not be significantly improved higher than 0.005% and be worked.
One object of the present invention produces 500~1200MPa of yield strength, tensile strength 980~1480MPa, the steel plate of strength and ductility product (tensile strength × elongation percentage) >=25GPa%.The steel plate includes hot rolled steel plate, cold-rolled steel sheet and galvanized steel plain sheet or other clad steel sheets.Microstructure after its heat treatment by volume includes: 30% to 70% retained austenite, the tissue (martensite or ferrite) of 30% to 70% body-centered cubic structure.Mn >=7% in its austenite by weight percentage, C >=0.5%.
It is described below with the experiment of steel plate progress of the invention.To the steel of the ingredient as determined by table 1 in 1200~1500 DEG C of heat preservation 5~20h homogenizations, hot rolling is carried out to form hot rolled plate after 0.5~2h is then kept the temperature between 1000 DEG C~1200 DEG C.With reference to Fig. 1, hot rolled plate treatment process is that hot rolled plate is being heated to annealing temperature heat preservation 0.5~60 minute.Hot rolled plate is subjected to soft annealing processing to be easy to cold rolling before cold rolling, the hot rolled plate after annealing is cold-rolled to 1.5mm after pickling, and keep the temperature 0.5~60min in annealing temperature.Wherein the hot rolled plate of No. 1 steel and cold-reduced sheet are carrying out a step annealing processing first after carrying out plate stamping pressing formation after 780 DEG C of austenitizings are handled in table 1.
The manufacturing method of formed parts is described below.The steel plate under hot rolled plate or cold-reduced sheet or other plating layer states is heated to 650~780 DEG C of heat preservations before the punching.Its type of cooling can be air-cooled or is cooled to room temperature with other types of cooling.Steel plate is transferred in mold after cooling carry out it is stamping, with the formed parts of shape needed for obtaining.Or gained steel plate is directly carried out to cold stamping or hot press-formed, it is kept the temperature later at 650~780 DEG C, is cooled to room temperature with air-cooled or other types of cooling.In above-mentioned manufacturing method, steel plate is heated to 650~780 DEG C of heat preservations, can get the tissue of face-centred cubic structure and body-centered cubic structure, and carbon and manganese in martensite (ferrite) is made to be diffused into austenite, stabilization of austenite is improved, is allowed to save to room temperature.In formed parts deformation process, sufficiently stable austenite can undergo phase transition induced plastic, and (TRIP, particularly, twinning induced plasticity (TWIP) can occur for partial austenitic in the preferred case, to improve the plasticity and energy absorption capacity of material.The microstructure of stamping component of the invention by volume includes: 30% to 60% retained austenite, the martensite or ferrite of 40% to 70% body-centered cubic crystal structure.Wherein Mn >=7% in austenite by weight percentage, C >=0.5%.
The chemical component of 1 steel of table
  C Mn P S It is other
1 0.3 6.66 0.012 0.008 1.05Si 0.04Ti 0.005B
2 0.28 5.75 0.009 0.002 1.05Si
3 0.4 4 0.006 0.008 1Al 1.5Si 0.5Mo
4 0.2 9.5 0.009 0.002 2Al 1Si
5 0.28 6.3 0.009 0.008 1.5Si
The heating of steel plate and heat treatment experiment
Hot rolled plate or cold-reduced sheet are completed into heating and heat insulation experiment in the resistance-type batch-type furnace with nitrogen protection.Specific experimental technique is shown in Table 2.
The different heat treatment process of table 2
The mechanical property for the steel plate that different heat treatment technique obtains is as shown in table 3.
The tensile mechanical properties of 3 steel plate of table
Note:
YS indicates yield strength, and taking the stress value of 0.2% residual deformation is its yield limit；TS indicates tensile strength；TE indicates breaking elongation.
Tensile sample is the ASTM standard sample of gauge length 50mm in table 3；The strain rate of stretching mechanical property testing is 6.67 × 10-4s-1。
It can be seen that the steel plate with present component by the mechanical performance data of table 3, heat treatment process through the invention can obtain intensity and the especially excellent formed parts of elongation percentage comprehensive performance.Specifically, it is able to achieve 500~1200MPa of yield strength, and 980~1480MPa of tensile strength, the steel plate of strength and ductility product (tensile strength × elongation percentage) >=30GPa%.
Softing treated the stress strain curve of the present invention and microstructure are as shown in Figures 2 and 3.Analysis on Microstructure is carried out to invention steel homogeneous deformation area, there are a small amount of carbide in steel, tissue is in zonal distribution, its austenite lath is in 200nm or so, and there are streaky structures in austenite, this tissue may be ε-martensite or Observations of Austenite Twins, and mechanical twin has occurred in deformation process by diffraction spot calibration austenite.
Fig. 4 gives No. 5 steel cold-reduced sheets and keeps the temperature 10 minutes stress strain curves at 670 DEG C, and yield strength, tensile strength and elongation percentage meet invention and require, and steel of the present invention unanimously keep compared with Yield point elongation and luders band is not present in high work hardening rate.It can be seen that according to the microstructure of Fig. 5 characterization, the still basic holding plate bar state distribution of tissue after cold rolled annealed, its crystallite dimension is at 1 micron or less, not only increase the yield strength of steel, and improve the stacking fault energy of austenite, be conducive to it and mechanical twin occurs in deformation process, to improve the elongation percentage and work hardening rate of steel.Fig. 6 is the X ray diffracting spectrum of deformation front and back under this technique, and the volume fraction being computed before and after austenite deformation is respectively 40% and 6%.In deformation process, TWIP TRIP effect is had occurred in retained austenite, to ensure that the required intensity and plasticity of steel of the present invention.

Claims (14)

  1. It is a kind of for stamping steel, which is characterized in that the steel include 0.22~0.48% C, 5~9.5% Mn, 0.5~3.0% Si+Al and the Fe of surplus and inevitable impurity by weight percentage.
  2. Steel as described in claim 1, which is characterized in that may also include at least one of following component:
    Cr:0.001% to 2%；
    Mo:0.001% to 2.0%；
    W:0.001% to 2.0%；
    Ti:0.0001% to 0.4%；
    Nb:0.0001% to 0.4%；
    Zr:0.0001% to 0.4%；
    V:0.0001% to 0.4%；
    Cu:0.0005% to 2%；
    Ni:0.0005% to 3.0%；
    B:0.0001% to 0.005%.
  3. Steel as described in claim 1, it is characterized in that, the steel are hot rolling, hot rolling acid-cleaning, hot rolling acid-cleaning coating coil of strip or steel plate or cold rolled annealed, cold rolling coating coil of strip or steel plate, and wherein coating coil of strip or steel plate include the coil of strip or steel plate of zinc coating coil of strip or steel plate or other coatings.
  4. Steel as claimed in claim 3, which is characterized in that the zinc coating steel plate is the hot rolled steel plate or cold-rolled steel sheet for being formed on metal zinc layers.
  5. Steel as claimed in claim 4, which is characterized in that the zinc coating steel plate includes selected from one of galvanizing by dipping, zinc-plated annealing, zinc plating or zinc-iron electroplating steel plate.
  6. Steel as claimed in claim 3, which is characterized in that the steel plate of other coatings is the hot rolled steel plate or cold-rolled steel sheet for being formed on al-si layer, or to be formed on the steel plate of other galvanneal coatings, organic coating.
  7. Such as steel according to any one of claims 1 to 6, the steel are heated to 650~780 DEG C the heat treatment for keeping the temperature 0.5~60 minute.
  8. Steel as claimed in claim 7, which is characterized in that after the heat treatment, the steel include: 30% to 60% retained austenite with areametric microstructure, 40% to The martensite or ferrite of 70% body-centered cubic crystal structure, the carbide lower than 3%.
  9. Steel as claimed in claim 8, which is characterized in that by weight percentage include the Mn more than or equal to the 7% and C more than or equal to 0.5% in the retained austenite.
  10. Steel as claimed in claim 9, it is characterized in that, during stress deformation, the retained austenite passes through phase-change induced plastic, or twinning induced plasticity effect is assisted simultaneously, the matching of its intensity and ductility is improved, so that mechanical property reaches: 0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, strength and ductility product >=25GPa%.
  11. A kind of formed parts, which is characterized in that formed parts steel as described in any one of claim 7-10 are formed by process for stamping and forming, and the formed parts include automobile structure.
  12. A kind of formed parts, which is characterized in that the formed parts are formed by steel of any of claims 1-6 through direct process for stamping and forming or hot press-formed technique, and the formed parts include automobile structure.
  13. Formed parts as claimed in claim 12, it is characterized in that, the formed parts are heated to 650~780 DEG C and keep the temperature 0.5~60 minute, the component includes: 30% to 60% retained austenite with areametric microstructure, the martensite or ferrite of 40% to 70% body-centered cubic crystal structure, carbide lower than 3%, it by weight percentage include the Mn more than or equal to the 7% and C more than or equal to 0.5% in the retained austenite, during stress deformation, the austenite passes through phase-change induced plastic, and twinning induced plasticity effect can be assisted, improve the matching of its intensity and ductility, so that mechanical property reaches: 0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, strength and ductility product >=25GPa%.
  14. A kind of heat treatment method, which comprises the following steps:
    (A) formed parts for providing such as steel according to any one of claims 1 to 6 or being formed by the steel by direct punching press or drop stamping；
    (B) steel or the formed parts are heated to 650~780 DEG C and keep the temperature 0.5~60 minute.
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