CN106011418A - Treatment process for obtaining and member with gradient performance - Google Patents
Treatment process for obtaining and member with gradient performance Download PDFInfo
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- CN106011418A CN106011418A CN201610440901.1A CN201610440901A CN106011418A CN 106011418 A CN106011418 A CN 106011418A CN 201610440901 A CN201610440901 A CN 201610440901A CN 106011418 A CN106011418 A CN 106011418A
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
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- 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
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- 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
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- 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
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- 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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Abstract
The invention relates to a treatment process for obtaining gradient performance. The treatment process comprises the following steps: A, preparing a blank, and dividing the blank into an area for a hard area to be formed and an area for a soft area to be formed; B, heating the area for the hard area to be formed to be 720DEG C or higher, and enabling a microstructure of the area to be changed into austenite; C, stamping and forming an overall blank, and cooling the overall blank in an any cooling mode after stamping and forming; D, performing carbon distribution treatment on the hard area of a member obtained by stamping and forming, and enabling carbon to be diffused from martensite to the austenite; and meanwhile, keeping the temperature of the area for the soft area to be formed being lower than 720DEG C in the step B or adding a step E after the step D, and heating the area for the soft area to be formed to be 600 to 720DEG C and insulating for 0.5 to 60 minutes. The invention also relates to a forming member produced by the treatment process. According to the treatment process disclosed by the invention, a die is simple, and the reliability of the process is good; in addition, the tensile strength of the soft area can reach 900 to 1500MPa, and the elongation percentage is greater than 15 percent, which are far superior to the levels in the prior art.
Description
Technical field
The present invention relates to a kind of process technique for obtaining gradient distribution performance.Specifically, the present invention relates to a kind of technique realizing gradient distribution performance on Same Part, the process for stamping and forming in its hard area, heat treatment method and mechanical performance are different with the process for stamping and forming of its soft zone and heat treatment method.The invention still further relates to the component made via this process technique, it has the different hard area of mechanical performance and soft zone simultaneously.
Background technology
Energy-saving and emission-reduction are the problems that automotive field is in the urgent need to address, and automotive light weight technology is one of effective means and approach of realizing energy-saving and emission-reduction.The lightweight of automobile can be realized by reasonably design and advanced manufacturing process.The use of high strength steel can ensure the safety of automobile while automobile lightweight.But there is relatively low stretch flangeability and low hole expansibility in high strength steel, so easily ftractureing when there is punching press and the problem such as stamping rear part resilience increase.
In order to solve the Problems in forming of high strength steel, a kind of it is referred to as hot press-formed or hot forming, has been commercially used for manufacturing the manufacturing process of the vehicle part with 1000MPa or higher intensity.Although but the part intensity after hot forming is the highest, but elongation percentage is the lowest.In actual automobile collision procedure, not requiring nothing more than safety member has higher intensity effectively to keep out collision object intrusion, and often wholly or partially has the requirement of ductility and toughness to part, to ensure high collision energy-absorbing.Traditional hot forming steel 22MnB5 is difficult to have high intensity and high ductility under the most hot formed technique concurrently simultaneously, so in order to solve this problem, industrial quarters develops splicing performance technologies (Tailored
Properties), making single part by high intensity together with the areas combine of two different performances of high-elongation, such as one B post, has high intensity in upper end and good preventing invades performance, and lower end has relatively low-intensity and preferable elongation percentage, thus reach the purpose of energy absorption.Splicing performance technologies is divided into the most again tailor welded (Tailor welded Blank) technology and realizes segmentation/gradient reinforcement technique two kinds by technique.
The common practices of tailor welded is exactly the method using laser welding at some position, by two pieces of heterogeneities together with the Plate Welding of different-thickness, obtains different performances after treatment.The welding of foreign material and different-thickness is relatively difficult, and adds production process and there is potential weld seam reduction or destroy risk.
Realize segmentation/gradient reinforcement technique by technique and be usually control part rate of cooling in hot stamping operation, obtain different tissues and obtain different performances.Mainly there is the heat conduction controlling mould, including active cooling (CN 102212742 A), passive cooling (CN104831020A, CN103521581A, CN103409613A).CN102212742A realizes different rate of cooling by the hot stamping forming die of the flexible controlled big band cooling pipe of design, the different water velocity of zones of different design of part.CN104831020A by the water channel design in mould, the distance stayed in a mold along with cooling water and cause temperature different, form uneven temperature field in a mold and the gradient that realizes in punching course controls.CN103521581A and CN103409613A is all to change the cooling rate of part by thermal barrier coatings in a mold and realize performance gradient distribution.
WO2006/038868
A1 describes a kind of gradient distribution method, and it forms the air gap by controlling the groove between mould and part to be punched, carrys out rate of cooling.US2013/0048160A1 by steel plate austenitizing and hot press-formed between to needing the part zone softened to carry out pre-cooling and obtain soft phase constitution, with after after drop stamping, realize the gradient distribution of part.
CN101861265A describes a kind of B post for vehicle and manufacture method thereof.Its objective is to design a kind of B post with gradient performance, there is the soft zone of at least 30mm near B post lower end fixed part, its manufacture method is the rate of cooling controlling soft zone.
CN103878237A discloses the method for a kind of high-strength steel hot press-formed part processing, and it carries out the annealing of local to the homogeneous component after hot forming, it is achieved the gradient distribution of part.The method needs to design special load coil, and annealing temperature is higher, is 600～1000 DEG C, and its preferable temperature is 800 DEG C, and after annealing, air cooling is processed to 100～500 DEG C.
The method in various contrast patents in sum, it is mainly characterized by after steel plate austenitizing and hot forming, its structure property is obtained by controlling soft zone phase transformation in cooling procedure, obtain different intensity by controlling the cooldown rate of different parts, or the design that cooled down by mould or groove or precooling treatment obtain soft zone.Significantly shortcoming is to need to change original Design of Dies, and technology stability is poor, and die life is short, and the soft zone on the material foundation of 22MnB5 is difficult to break through the elongation percentage of 15%.
Summary of the invention
The present invention relates to a kind of technique realizing gradient distribution performance on Same Part, the process for stamping and forming in its hard area, heat treatment method and mechanical performance are different with the process for stamping and forming of its soft zone and heat treatment method.The invention still further relates to the component with hard area and soft zone, its hard area can ensure little collision deformation because of high intensity, and its soft zone can ensure collision energy-absorbing because of high elongation percentage.
According to a preferred embodiment of the present invention, it is provided that a kind of process technique for obtaining gradient distribution performance, it is characterised in that comprise the following steps: A, preparation base material, base material is divided into region and the region of soft zone to be formed in hard area to be formed；B, the region in hard area to be formed is heated to more than 720 DEG C so that it is microstructure is changed into austenite, keeps the temperature in region of soft zone to be formed less than 720 DEG C simultaneously；C, base material entirety is carried out stamping, and cool down with any type of cooling after stamping；D, hard area to the component obtained after stamping carry out carbon partition process, make carbon spread to austenite from martensite.
According to another preferred embodiment of the invention, it is provided that a kind of process technique for obtaining gradient distribution performance, it is characterised in that comprise the following steps: A, preparation base material, base material is divided into region and the region of soft zone to be formed in hard area to be formed；B, the region in hard area to be formed is heated to more than 720 DEG C so that it is microstructure is changed into austenite, keeps the temperature in region of soft zone to be formed less than 720 DEG C simultaneously；C, base material entirety is carried out stamping, and cool down with any type of cooling after stamping；D, hard area to the component obtained after stamping carry out carbon partition process, make carbon spread to austenite from martensite.
Further embodiment according to the present invention, it is provided that a kind of component with gradient distribution performance, it is characterised in that described component is made by the process technique of above preferred embodiment.
In a scheme of the present invention, hard area different with the heating technique of soft zone (heating of soft zone non-full austenite), process for stamping and forming soft zone is consistent with hard area, therefore need not mould amendment, and reliability of technology is good.The another kind of scheme of the present invention is then to first pass through process for stamping and forming to form formed parts, then soft zone individually carries out heat treatment, diel and technique are not had any impact.It is emphasized that the soft zone elongation percentage that the two schemes of the present invention is obtained can ensure that more than 15%, preferably 25～35%, it is much better than the level of prior art.
It should be noted that in this manual, capability gradient part includes but not limited to the B post of automobile, A post, front longitudinal etc.." hard area " refers to the hardened area that on part, intensity is high, and " soft zone " refers to the region that on part, intensity is low and elongation percentage is high.As a example by automobile B-column, hard area is the region that upper end needs to prevent collision from invading, and soft zone is the region that lower end needs to absorb collision energy.
The microstructure of soft zone includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%.The mechanical property of soft zone is: tensile strength 900～1500MPa, and elongation percentage is more than 15%.
The microstructure in hard area is counted with area and is included: the retained austenite of 3% to 23%, the carbide less than 2%, remaining is as martensite.The mechanical property in hard area is: yield strength is more than 1200MPa, and tensile strength is more than 1600MPa, and elongation percentage is more than 10%.
Accompanying drawing explanation
The preferred embodiments of the present invention are described below with reference to the accompanying drawings, in accompanying drawing:
Fig. 1 is process route chart according to a first embodiment of the present invention；
Fig. 2 is process route chart according to a second embodiment of the present invention；
Fig. 3 is process route chart according to a third embodiment of the present invention；
Fig. 4 is process route chart according to a fourth embodiment of the present invention；
Fig. 5 is containing hard area and the schematic diagram of the automobile B-column of soft zone.
It is pointed out that in diagram, solid line represents the processing route being subjected to, and dotted line represents nonessential optional processing route.
Detailed description of the invention
The process route of the present invention it is more fully described below with reference to exemplary embodiment.Following example are intended to explain the exemplary process route of the present invention, and it will be apparent to those skilled in the art is to the invention is not restricted to these embodiments.
According to the present invention, first can provide a kind of for stamping steel, described steel include 0.22～the Si+Al of the Mn of the C of 0.48%, 5～9.5%, 0.2～3.0% and the Fe of surplus and inevitable impurity by weight percentage, and wherein said steel are one of hot rolled coil (plate), hot rolling acid-cleaning volume (plate), cold rolled annealed volume (plate), cold rolling coating volume (plate).Its soft zone part (scheme one before stamping, in the austenitizing heating process of hard area, soft zone temperature controls) or drop stamping after (scheme two, soft zone individually heats) be heated to the heat treatment of 600～780 DEG C of insulations (wherein may select 680,700,720,750 DEG C of equitemperatures) 0.5～60 minute (wherein may select 1,3,5,10,20,30,40,50 etc. time) and obtain.Manganese, carbon and the change of other alloying element in austenite when utilizing thermodynamics soft com-puting to go out two-phase section annealing balance.Binding constituents design and processes selects, and soft zone obtains the volume fraction of retained austenite 30%～60%, martensite (ferrite) tissue of volume fraction 40%～70%, and is less than the carbide of 3%.Owing to carbon and manganese element spread in austenite and are enriched with in the heating process of soft zone, and design carbon content and Fe content have reached 0.22% and more than 5% the most in alloy, therefore the medium managese steel with prior art contrasts, need not reach or stable retained austenite can be formed close to the carbon in austenite during thermodynamical equilibrium and Fe content, under above-mentioned heating technique, the carbon content in final actual measurement retained austenite is more than 0.5%, Fe content is more than 7%, and the crystal grain of austenite is less than 1 μm less than 2 μm or austenite lath thickness.Steel plate is in deformation process, and retained austenite itself has high deformability and toughness, and produces martensitic phase transformation and/or the energy absorption capacity of deformation twin beneficially raising steel plate and elongation percentage inside retained austenite.
The steel of the present invention based in high-carbon manganese composition design, carbon content between 0.22～0.48%, preferably 0.25～0.45%, Fe content between 5～9.5%, preferably 6～8%.Carbon and manganese are all among the austenite stabilizing elements, the austenitizing temperature reducing steel and martensite that all can be strong start phase transition temperature, in annealing heat treatment process, form austenite/ferritic lath alternating structure, and carbon and manganese partition are in austenite, make austenite stable to room temperature, retained austenite itself has high deformability and toughness, deformation process also can occur TRIP effect become martensite mutually, improve intensity and the ductility of steel.Especially, the composition design optimized in the steel of the present invention and the steel of annealing process, its retained austenite has higher carbon and manganese, and the stacking fault energy of partial austenitic is higher, deformation process is formed deformation twin, can further improve work hardening rate and improve the strength of materials and ductility simultaneously.When carbon and Fe content are relatively low, for obtaining more austenite, needing to improve with its preferred annealing temperature, cause carbon and Fe content in austenite to reduce thicker with crystal grain, and cause stabilization of austenite poor, in deformation process, the obdurability of steel reduces.When carbon content is higher, hypereutectoid tissue may be formed, in above-mentioned heating process, easily form more coarse carbide and deteriorate the mechanical property of steel, and the further raising of carbon content can deteriorate the toughness in hard area.It is found by the applicant that Mn content is controlled 5～9.5%, carbon content control, between 0.22～0.48%, can obtain the strongest plasticity.
According to a preferred embodiment of the present invention, described steel comprise at least one in following component: Cr:0.001%～5% further；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%.By at least one combination with above-mentioned basis in these compositions, the ultra-high strength and toughness coupling of punching component can be further ensured that, its mechanical mechanics property is reached: yield strength 0.5～1.2GPa, tensile strength 1.0～1.5GPa, strength and ductility product (tensile strength × elongation percentage) more than 25GPa %.
According to a preferred embodiment of the present invention, described steel include hot rolled steel plate, cold-rolled steel sheet or the steel plate with coated layer.The described steel plate with coated layer can be zinc coating steel plate, and it is hot rolled steel plate or the cold-rolled steel sheet being formed on metal zinc layers.Described zinc coating steel plate includes the one in galvanizing by dipping (GI), zinc-plated annealing (GA), zinc plating or zinc-ferroelectricity plating (GE).The described steel plate with coated layer also can be hot rolled steel plate or the cold-rolled steel sheet being formed on al-si layer, or the steel plate of organic coating or the steel plate with other galvanneal coating.
Several selection process routes of the gradient distribution property treatment technique of of the present invention steel are described more fully below, and it can realize the performance of gradient distribution on Same Part.Certainly, it should be appreciated by those skilled in the art, the process route of the present invention is not limited to concrete technology route described below.
Process route 1:
First, the plate after base material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Base material can be such as the base material of composition and the performance with above-mentioned steel.
Then, as it is shown in figure 1, make annealing treatment base material entirety, its light plate and coil of strip etc. can carry out heat treatment at steel plant's continuous annealing production line or continuous annealing coating production line.Such as, base material entirety can be heated to 600～720 DEG C, be incubated 0.5～60 minute, then with any type of cooling (such as in air-cooled, the air cooling of continuous annealing production line, or cooling or air cooling in the mould of drop stamping), it is cooled to a certain temperature of more than-100 DEG C, is preferably cooled to room temperature.After this annealing, the microstructure of base material comprises the steps that the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3% in terms of area, wherein, described retained austenite includes the Mn more than or equal to 7% and the carbon more than or equal to 0.5% by weight percentage.After annealed process, the tensile strength of base material is 900～1500MPa, and elongation percentage reaches more than 15%, and therefore this base material the most i.e. has favorable forming property.
Then, the region in hard area to be formed is heated to 720～850 DEG C, its microstructure is made to be changed into austenite, ensure the region of soft zone to be formed temperature in the process less than 720 DEG C (such as simultaneously, the region of soft zone to be formed is not heated and hold it in room temperature, or be heated to 650 DEG C).In the process, such as, first hard area sensing can be heated to such as 650 DEG C, soft zone does not heats (be maintained at room temperature or rise to a relatively low temperature due to conduction of heat when hard area is heated), heats in then blank entirety inserted the stove that furnace temperature is such as 780 DEG C.For hard area, from 650 DEG C be heated to 780 DEG C needed for heat time heating time shorter, such as 40 seconds, followed by and be incubated such as 20 seconds to realize the homogenization of austenite structure, then the blank overall time in the stove of 780 DEG C is such as 1 minute.In this is 1 minute, soft zone is low due to charging temperature, can not be heated to 780 DEG C in the stove of 780 DEG C, as long as controlling in reality below 720 DEG C.It is pointed out that the homogenization that traditional hot forming Steel material (such as 22MnB5) cannot realize austenite structure because of austenitizing temperature far above the material related in the present invention within the heat time heating time of 1 minute.
Then, base material entirety is carried out stamping.Hard area, after full austenite district is stamping, can be cooled to its martensite start temperature point (Ms) 150～260 DEG C below via any type of cooling (cooling or air cooling in such as mould).Soft zone, after stamping, can cool down via the type of cooling consistent with hard area, such as cooling or air cooling in mould.The microstructure of soft zone comprises the steps that the austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite and the carbide less than 3% in terms of area.
Then, the hard area of the component (i.e. formed parts) obtained after stamping is carried out carbon partition process, such as hard area is heated to 160～450 DEG C, is incubated 1～10000 second, it is allowed to occur carbon to spread to austenite from oversaturated martensite, cause rich carbon in austenite, thus it being greatly improved the stability of austenite so that it is residual quantity at room temperature increases.Preferably, there is the martensite phase transformation to austenite, thus increase retained austeniteization content, improve its mechanical performance.Additionally, for soft zone is come, consistent carbon partition can be carried out with hard area and processes, or it not carried out carbon partition process (it is to say, hard area individually carries out carbon partition process).Whether carrying out carbon partition process, the mechanical property of the soft zone of formed parts all can reach tensile strength 900～1500MPa, and elongation percentage more than 15%.But in order to simple to operate, preferably formed parts entirety can be carried out carbon partition process.
Process route 2:
First, the plate after base material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Base material can be such as the base material of composition and the performance with above-mentioned steel.
Then, as shown in Figure 2, the soft zone to be formed of base material and the region in hard area are heated simultaneously and be incubated 0.5～60 minute, wherein, the region heating and thermal insulation temperature of soft zone to be formed is 600～720 DEG C, the region heating and thermal insulation temperature in hard area to be formed is 720～850 DEG C so that it is microstructure is changed into austenite.During heating and thermal insulation, the microstructure of soft zone includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%, its retained austenite includes the Mn more than or equal to 7% and the carbon more than or equal to 0.5% by weight percentage, and hard area comprises fully austenitic structure, and the carbide less than 3%.In the process, such as, first hard area sensing can be heated to such as 650 DEG C, soft zone is heated to such as 500 DEG C by sensing, heats in then blank entirety inserted the stove that furnace temperature is such as 780 DEG C.For hard area, from 650 DEG C be heated to 780 DEG C needed for heat time heating time shorter, such as 40 seconds, followed by and be incubated such as 20 seconds to realize the homogenization of austenite structure, then the blank overall time in the stove of 780 DEG C is such as 1 minute.In this is 1 minute, soft zone is low due to charging temperature, can not be heated to 780 DEG C in the stove of 780 DEG C, as long as controlling in reality below 720 DEG C.
Then, base material entirety is carried out stamping, with any type of cooling (cooling or air cooling in mould) cooling after punching press.Hard area is cooled to below its martensite start temperature point 150～260 DEG C, and soft zone is cooled to the arbitrary temp of more than-50 DEG C.Preferably, punching press and the enforcement of cooling technique for convenience, the overall type of cooling according to hard area of formed parts cools down, and soft zone structure property also can meet requirement.
Then, the hard area of formed parts is carried out carbon partition process, such as hard area is heated to 160～450 DEG C, is incubated 1～10000 second, it is allowed to occur carbon to spread to austenite from oversaturated martensite, cause rich carbon in austenite, thus it being greatly improved the stability of austenite so that it is residual quantity at room temperature increases.Preferably, there is the martensite phase transformation to austenite, thus increase retained austeniteization content, improve its mechanical performance.Additionally, for soft zone is come, consistent carbon partition can be carried out with hard area and processes, or it not carried out carbon partition process (it is to say, hard area individually carries out carbon partition process).Whether carrying out carbon partition process, the mechanical property of the soft zone of formed parts all can reach tensile strength 900～1500MPa, and elongation percentage more than 15%.But in order to simple to operate, preferably formed parts entirety can be carried out carbon partition process.
Process route 3:
First, the plate after base material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Base material can be such as the base material of composition and the performance with above-mentioned steel.
Then, as it is shown on figure 3, base material entirety is heated to 720～850 DEG C, it is incubated 0.5～60min so that it is be organized as fully austenitic structure, and the carbide less than 3%.
Then, base material entirety is carried out stamping, stamping after through any type of cooling (in mould cooling or air cooling) cooling.In cooling procedure, the region in hard area to be formed is cooled to below its martensite start temperature point 150～260 DEG C, and soft zone is cooled to the arbitrary temp of more than-100 DEG C less than 600 DEG C.Preferably, punching press and the process implementing of cooling for convenience, overall for the formed parts type of cooling according to hard area is cooled down, soft zone structure property also can meet requirement.
Then, the region in the hard area to be formed of the formed parts after stamping is carried out carbon partition process, such as hard area is heated to 160～450 DEG C, is incubated 1～10000 second, it is allowed to occur carbon to spread to austenite from oversaturated martensite, cause rich carbon in austenite, thus it being greatly improved the stability of austenite so that it is residual quantity at room temperature increases.Preferably, there is the martensite phase transformation to austenite, thus increase retained austeniteization content, improve its mechanical performance.Additionally, for soft zone is come, consistent carbon partition can be carried out with hard area and processes, or it not carried out carbon partition process (it is to say, hard area individually carries out carbon partition process).Whether carrying out carbon partition process, the mechanical property of the soft zone of formed parts all can reach tensile strength 900～1500MPa, and elongation percentage more than 15%.But in order to simple to operate, preferably formed parts entirety can be carried out carbon partition process.
Then, as it is shown on figure 3, soft zone carries out heat treatment the most again, being heated to 600～720 DEG C, be incubated 0.5～60 minute, (such as air cooling) is cooled to room temperature the most in any way.After this heat treatment, the microstructure of described steel includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%, its retained austenite includes the Mn more than or equal to 7% and the carbon more than or equal to 0.5% by weight percentage, its mechanical property reaches tensile strength 900～1500MPa, elongation percentage more than 15%.
Process route 4:
First, the plate after base material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Base material can be such as the base material of composition and the performance with above-mentioned steel.
Then, as shown in Figure 4, base material entirety is heated to 720～800 DEG C, is incubated 0.5～60min so that it is be organized as fully austenitic structure, and the carbide less than 3%.
Then, base material entirety is carried out stamping, stamping after through any type of cooling (in mould cooling or air cooling) cooling.In cooling procedure, the region in hard area to be formed is cooled to below its martensite start temperature point 150～260 DEG C, and soft zone is cooled to more than-100 DEG C above arbitrary temps.Preferably, punching press and the process implementing of cooling for convenience, overall for the formed parts type of cooling according to hard area is cooled down, soft zone structure property also can meet requirement.
Then, as shown in Figure 4, soft zone carrying out heat treatment the most again, such as, is heated to 600～720 DEG C, be incubated 0.5～60 minute, (such as air cooling) is cooled to room temperature the most in any way.After this heat treatment, the microstructure of described steel includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%, its retained austenite includes the Mn more than or equal to 7% and the carbon more than or equal to 0.5% by weight percentage, its mechanical property reaches tensile strength 900～1500MPa, elongation percentage more than 15%.
Then, the region in the hard area to be formed of the formed parts after stamping is carried out carbon partition process, such as hard area is heated to 160～450 DEG C, is incubated 1～10000 second, it is allowed to occur carbon to spread to austenite from oversaturated martensite, cause rich carbon in austenite, thus it being greatly improved the stability of austenite so that it is residual quantity at room temperature increases.Preferably, there is the martensite phase transformation to austenite, thus increase retained austeniteization content, improve its mechanical performance.Additionally, for soft zone is come, consistent carbon partition can be carried out with hard area and processes, or it not carried out carbon partition process (it is to say, hard area individually carries out carbon partition process).Whether carrying out carbon partition process, the mechanical property of the soft zone of formed parts all can reach tensile strength 900～1500MPa, and elongation percentage more than 15%.But in order to simple to operate, preferably formed parts entirety can be carried out carbon partition process.
It is to be noted, in this single heat treatment process of soft zone, such as, soft zone can use the mode such as such as flame heating, sensing heating, LASER HEATING to heat, or the overall heating furnace that enters uses the method that soft or hard district heating-up temperature is different to process, the baffle plate of thermal radiation resistant is placed in such as hard area up and down, and hard area is wrapped up coating heat insulating coat on heat-barrier material and hard area.
According to embodiments of the invention, by hard area and soft zone carry out different heating technique (heating of soft zone non-full austenite), but soft zone keeps consistent with the process for stamping and forming in hard area, therefore need not mould amendment, and reliability of technology is good.
The above-mentioned process route of the present invention may be used for manufacturing any parts needing gradient distribution performance, and it includes but not limited to the B post of automobile, A post, front longitudinal etc..Fig. 5 shows the schematic diagram of the automobile B-column comprising hard area and soft zone that a kind of above-mentioned process technique by the present invention makes, and its hard area is the region that upper end needs to prevent collision from invading, and soft zone is the region that lower end needs to absorb collision energy.
According to embodiments of the invention, the microstructure of the soft zone of made formed parts includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%.The mechanical property of soft zone is: tensile strength 900～1500MPa, and elongation percentage is more than 15%.The microstructure in hard area is counted with area and is included: the carbide of retained austenite, 0～2% of 3% to 23%, remaining is as martensite.The mechanical property in hard area is: yield strength is more than 1200MPa, and tensile strength is more than 1600MPa, and elongation percentage is more than 10%.
The foregoing describe the preferred embodiments of the present invention, but those skilled in the art is it is to be understood that any possible change that carries out without departing from the inventive concept of the premise or replacement, belongs to protection scope of the present invention.
Claims (15)
1. the process technique being used for obtaining gradient distribution performance, it is characterised in that comprise the following steps:
A, preparation base material, be divided into region and the region of soft zone to be formed in hard area to be formed by base material；
B, the region in hard area to be formed is heated to more than 720 DEG C so that it is microstructure is changed into austenite, keeps the temperature in region of soft zone to be formed less than 720 DEG C simultaneously；
C, base material entirety is carried out stamping, and cool down with any type of cooling after stamping；
D, hard area to the component obtained after stamping carry out carbon partition process, make carbon spread to austenite from martensite.
2. the process technique for obtaining gradient distribution performance as claimed in claim 1, it is characterized in that, after step and further comprising the steps of before step B: base material entirety is made annealing treatment, base material entirety will be heated to 600～720 DEG C, it is incubated 0.5～60 minute, is then cooled to room temperature with any type of cooling.
3. the process technique for obtaining gradient distribution performance as claimed in claim 2, it is characterised in that make the temperature in the region of soft zone to be formed remain less than 720 DEG C in stepb.
4. the process technique for obtaining gradient distribution performance as claimed in claim 1, it is characterized in that, in stepb the soft zone to be formed of base material and the region in hard area are heated simultaneously and be incubated 0.5～60 minute, wherein, the region heating and thermal insulation temperature of soft zone to be formed is 600～720 DEG C, and the region heating and thermal insulation temperature in hard area to be formed is 720～850 DEG C.
5. the process technique for obtaining gradient distribution performance as described in claim 1-4, it is characterised in that in step C, hard area being cooled to below its martensite start temperature point 150～260 DEG C, soft zone is cooled to the arbitrary temp of more than-100 DEG C.
6. the process technique for obtaining gradient distribution performance as according to any one of claim 1-4, it is characterised in that in step D hard area is heated to 160～450 DEG C, is incubated 1～10000 second.
7. the process technique for obtaining gradient distribution performance as according to any one of claim 1-4, it is characterised in that in step D, is also carried out carrying out consistent carbon partition with hard area and processes, or do not carry out carbon partition process soft zone.
8. the process technique for obtaining gradient distribution performance as according to any one of claim 1-4, it is characterized in that, the microstructure of the soft zone of the component obtained after stamping includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%, the mechanical property of soft zone is: tensile strength 900～1500MPa, and elongation percentage is more than 15%；The microstructure in hard area is counted with area and is included: the carbide of retained austenite, 0～2% of 3% to 23%, remaining as martensite, the mechanical property in hard area is: yield strength is more than 1200MPa, and tensile strength is more than 1600MPa, and elongation percentage is more than 10%.
9. the process technique being used for obtaining gradient distribution performance, it is characterised in that comprise the following steps:
A, preparation base material, be divided into region and the region of soft zone to be formed in hard area to be formed by base material；
B, base material entirety is heated to 720～800 DEG C, is incubated 0.5～60min so that it is structural transformation is austenite；
C, base material entirety is carried out stamping, stamping after cool down through any type of cooling；
D, hard area to the component obtained after stamping carry out carbon partition process, make carbon spread to austenite from martensite.
10. the process technique for obtaining gradient distribution performance as claimed in claim 9, it is characterized in that, in step C, the region in hard area to be formed is cooled to below its martensite start temperature point 150～260 DEG C, and soft zone is cooled to the arbitrary temp of more than-100 DEG C.
The 11. process techniques for obtaining gradient distribution performance as according to any one of claim 9-10, it is characterized in that, before or after step D, soft zone is individually carried out heat treatment, is i.e. heated to 600～720 DEG C, it is incubated 0.5～60 minute, is cooled to room temperature the most in any way.
12. as claimed in claim 11 for obtaining the process technique of gradient distribution performance, it is characterized in that, after soft zone is individually carried out heat treatment, the microstructure of base material or stamping component includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%, its retained austenite includes the Mn more than or equal to 7% and the carbon more than or equal to 0.5% by weight percentage, its mechanical property reaches tensile strength 900～1500MPa, elongation percentage more than 15%.
13. 1 kinds of components with gradient distribution performance, it is characterised in that described component is made by the process technique according to any one of claim 1-12.
14. components as claimed in claim 13, it is characterised in that described component includes the B post of automobile, A post, front longitudinal.
15. components as according to any one of claim 13-14, it is characterized in that, the microstructure of the soft zone of described component includes in terms of area: the retained austenite of 30% to 60%, the martensite of the body-centered cubic crystal structure of 40% to 70% or ferrite, carbide less than 3%, the mechanical property of soft zone is: tensile strength 900～1500MPa, and elongation percentage is more than 15%；The microstructure in hard area is counted with area and is included: the carbide of retained austenite, 0～2% of 3% to 23%, remaining as martensite, the mechanical property in hard area is: yield strength is more than 1200MPa, and tensile strength is more than 1600MPa, and elongation percentage is more than 10%.
Priority Applications (3)
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| PCT/CN2016/090629 WO2017219427A1 (en) | 2015-12-04 | 2016-07-20 | Treatment process for obtaining graded performance and member thereof |
| ES16905967T ES2971678T3 (en) | 2015-12-04 | 2016-07-20 | Treatment process to obtain progressive performance and member thereof |
| EP16905967.2A EP3473735B1 (en) | 2016-06-20 | 2016-07-20 | Treatment process for obtaining graded performance and member thereof |
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| CN2015108783235 | 2015-12-04 | ||
| CN201510878323.5A CN105483531A (en) | 2015-12-04 | 2015-12-04 | Steel for stamping formation and forming component and heat treatment method thereof |
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| CN106011418A true CN106011418A (en) | 2016-10-12 |
| CN106011418B CN106011418B (en) | 2018-05-22 |
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| CN201580085081.2A Active CN108474081B (en) | 2015-12-04 | 2015-12-25 | Steel material for press forming, formed member thereof, and heat treatment method |
| CN201610440901.1A Active CN106011418B (en) | 2015-12-04 | 2016-06-20 | For obtaining the treatment process of gradient distribution performance and its component |
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| CN101238233A (en) * | 2005-08-03 | 2008-08-06 | 住友金属工业株式会社 | Hot-rolled steel sheet and cold-rolled steel sheet and manufacturing method thereof |
| CN102232123A (en) * | 2008-09-18 | 2011-11-02 | 国立大学法人冈山大学 | Hot-pressed steel plate member and manufacturing method therefor |
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| CN113802065B (en) * | 2021-11-18 | 2022-03-29 | 育材堂（苏州）材料科技有限公司 | Hot press-formed member, steel sheet for hot press forming, and hot press process |
| CN114643309A (en) * | 2022-03-25 | 2022-06-21 | 本钢板材股份有限公司 | Processing method of variable-strength hot forming steel part |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2017219427A1 (en) | 2017-12-28 |
| CN105483531A (en) | 2016-04-13 |
| CN106011418B (en) | 2018-05-22 |
| CN108474081A (en) | 2018-08-31 |
| ES2971678T3 (en) | 2024-06-06 |
| CN108474081B (en) | 2021-09-17 |
| WO2017092104A1 (en) | 2017-06-08 |
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