CN106011418B - For obtaining the treatment process of gradient distribution performance and its component - Google Patents
For obtaining the treatment process of gradient distribution performance and its component Download PDFInfo
- Publication number
- CN106011418B CN106011418B CN201610440901.1A CN201610440901A CN106011418B CN 106011418 B CN106011418 B CN 106011418B CN 201610440901 A CN201610440901 A CN 201610440901A CN 106011418 B CN106011418 B CN 106011418B
- Authority
- CN
- China
- Prior art keywords
- soft zone
- hard area
- blank material
- region
- austenite
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 238000000034 method Methods 0.000 title claims abstract description 76
- 230000008569 process Effects 0.000 title claims abstract description 51
- 238000009826 distribution Methods 0.000 title claims abstract description 27
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 72
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 68
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 65
- 239000000463 material Substances 0.000 claims abstract description 52
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 37
- 238000012545 processing Methods 0.000 claims abstract description 36
- 238000001816 cooling Methods 0.000 claims abstract description 34
- 238000005192 partition Methods 0.000 claims abstract description 32
- 238000010438 heat treatment Methods 0.000 claims description 31
- 230000000717 retained effect Effects 0.000 claims description 29
- 239000011572 manganese Substances 0.000 claims description 18
- 229910052748 manganese Inorganic materials 0.000 claims description 13
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 12
- 238000000137 annealing Methods 0.000 claims description 12
- 239000013078 crystal Substances 0.000 claims description 10
- 229910000859 α-Fe Inorganic materials 0.000 claims description 10
- 238000004321 preservation Methods 0.000 claims description 9
- 238000004080 punching Methods 0.000 claims description 9
- 230000009466 transformation Effects 0.000 claims description 6
- 238000009413 insulation Methods 0.000 claims description 4
- 238000007493 shaping process Methods 0.000 claims 1
- 238000005516 engineering process Methods 0.000 abstract description 11
- 229910000831 Steel Inorganic materials 0.000 description 46
- 239000010959 steel Substances 0.000 description 46
- 238000004519 manufacturing process Methods 0.000 description 10
- 238000013461 design Methods 0.000 description 9
- 238000000576 coating method Methods 0.000 description 7
- 239000011248 coating agent Substances 0.000 description 6
- 239000004615 ingredient Substances 0.000 description 5
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical group [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 4
- 239000011701 zinc Substances 0.000 description 4
- 229910052725 zinc Inorganic materials 0.000 description 4
- 230000008859 change Effects 0.000 description 3
- 239000010960 cold rolled steel Substances 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000000265 homogenisation Methods 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 238000007747 plating Methods 0.000 description 2
- 230000011218 segmentation Effects 0.000 description 2
- 230000006641 stabilisation Effects 0.000 description 2
- 238000011105 stabilization Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 235000019628 coolness Nutrition 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000004093 laser heating Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000012720 thermal barrier coating Substances 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a kind of for obtaining the treatment process of gradient distribution performance, comprise the following steps：A, prepare blank material, blank material is divided into the region in hard area to be formed and the region of soft zone to be formed；B, the region in hard area to be formed is heated to 720 DEG C or more, its microstructure is made to be changed into austenite；C, blank material is integrally carried out stamping, and is cooled down with the arbitrary type of cooling after stamping；D, the hard area of the component to obtaining after stamping carries out carbon partition processing, and carbon is made to be spread from martensite into austenite；Keep that the temperature in the region of soft zone to be formed increases step E less than 720 DEG C or after step D, region to forming soft zone is heated to 600 ~ 720 DEG C and keeps the temperature 0.5 60 minutes simultaneously in stepb.The invention further relates to pass through formed parts made of above-mentioned treatment process.The treatment process of the present invention, mold is simple, and reliability of technology is good, and can realize that 900~1500MPa of soft zone tensile strength, elongation percentage are more than 15%, is much better than the level of the prior art.
Description
Technical field
The present invention relates to a kind of for obtaining the treatment process of gradient distribution performance.Specifically, the present invention relates to one kind to exist
On Same Part realize gradient distribution performance technique, process for stamping and forming, heat treatment method and the mechanical performance in hard area and its
The process for stamping and forming and heat treatment method of soft zone are different.The invention further relates to via component made of the treatment process,
Its hard area for having mechanical performance different simultaneously and soft zone.
Background technology
Energy-saving and emission-reduction are the problem of automotive field are in the urgent need to address, and automotive light weight technology is the effective of realization energy-saving and emission-reduction
One of means and approach.The lightweight of automobile can be realized with advanced manufacturing process by reasonably designing.High strength steel
Use the security that can ensure automobile while automobile lightweight.But there are relatively low stretch flange formabilities for high strength steel
Property and low hole expansibility, so there are easily crack during punching press and it is stamping after part rebound increase the problems such as.
In order to solve the Problems in forming of high strength steel, one kind is referred to as hot press-formed or hot forming, has for manufacturing
The manufacturing process of the vehicle part of 1000MPa or higher intensity has been commercialized.But although the part after hot forming is strong
Degree is very high, but elongation percentage is very low.In actual automobile collision procedure, not requiring nothing more than safety member has higher intensity effectively to support
Collision object intrusion is kept off, and often wholly or partially has the requirement of ductility and toughness to part, to ensure that high collision is inhaled
It can property.Traditional hot forming is difficult under once hot formed technique with steel 22MnB5 while has both high intensity and high ductility, institute
With in order to solve this problem, industrial quarters develops splicing performance technologies（Tailored properties）, make single part by
The region of two different performances of high intensity and high-elongation is combined, such as a B column, has high intensity and good in upper end
Good prevents intrusion performance, and lower end has compared with low-intensity and preferable elongation percentage, so as to achieve the purpose that energy absorption.Splicing
Performance technologies are usually divided into as tailor welded（Tailor welded Blank）Technology and the technique that passes through realize that segmentation/gradient is strengthened
Two kinds of technology.
The common practices of tailor welded is exactly the method for using laser welding at some positions, by two pieces of heterogeneities and difference
The steel plate of thickness welds together, and obtains different performances after processing.The welding of dissimilar material and different-thickness is relatively difficult,
And it adds production process and there are the reduction of potential weld seam or destruction risks.
Realize that segmentation/gradient reinforcement technique is usually cooling velocity of the control part in hot stamping operation by technique,
It obtains different tissues and obtains different performances.Mainly there is the heat conduction of control mold, including active cooling（CN 102212742
A）, it is passive to cool down（CN104831020A、CN103521581A、CN103409613A）.CN102212742A is flexible by designing
Controllably the hot stamping forming die with cooling pipe, the different zones of part design different water velocities and realize different coolings greatly
Speed.CN104831020A causes temperature by the water channel design in mold with the distance that cooling water stayed in a mold
Difference forms non-uniform temperature field and realizes the gradient in punching course and control in a mold.CN103521581A and
CN103409613A is to change the cooling rate of part by thermal barrier coatings in a mold to realize performance gradient distribution.
WO2006/038868 A1 describe a kind of gradient distribution method, recessed between mold and part to be punched by controlling
Slot forms the air gap, carrys out cooling velocity.US2013/0048160A1 by steel plate austenitizing and it is hot press-formed between
Precooling is carried out to the part zone that needs soften and obtains soft phase constitution, realizes the gradient distribution of part after drop stamping after.
CN101861265A describes a kind of B columns and its manufacturing method for vehicle.The purpose is to design one kind to have
There is at least soft zone of 30mm in the B columns of gradient performance, manufacturing method is the cold of control soft zone close to B columns lower end fixed part
But speed.
The method that CN103878237A discloses a kind of hot press-formed part processing of high-strength steel, to equal after hot forming
One component carries out local annealing, realizes the gradient distribution of part.This method needs to design special load coil, annealing temperature
Degree is higher, is 600~1000 DEG C, and preferable temperature is 800 DEG C, and is air-cooled to 100~500 DEG C after annealing and is processed.
The method in various comparison patents in summary, is mainly characterized by after steel plate austenitizing and hot forming, leads to
It crosses the phase transformation of control soft zone in cooling procedure and obtains its structure property, obtained not by controlling the cooldown rate of different parts
Same intensity or the design or groove or precooling treatment that are cooled down by mold obtain soft zone.Significantly the shortcomings that is to need to change original
Some mold design, technology stability is poor, and die life is short, and the soft zone on the material foundation of 22MnB5 is difficult breakthrough 15%
Elongation percentage.
The content of the invention
The present invention relates to it is a kind of on Same Part realize gradient distribution performance technique, the process for stamping and forming in hard area,
Heat treatment method and the process for stamping and forming and heat treatment method of mechanical performance and its soft zone are different.The invention further relates to same
When the component with hard area and soft zone, because high intensity can ensure small collision deformation, soft zone can because of high elongation percentage in hard area
Ensure collision energy-absorbing.
According to a preferred embodiment of the present invention, a kind for the treatment of process for being used to obtain gradient distribution performance is provided,
It is characterized in that, comprises the following steps：A, prepare blank material, blank material is divided into the region in hard area to be formed and the area of soft zone to be formed
Domain；B, the region in hard area to be formed is heated to 720 DEG C or more, its microstructure is made to be changed into austenite, while keep treating shape
Temperature into the region of soft zone is less than 720 DEG C；C, blank material is integrally carried out it is stamping, and with arbitrary cold after stamping
But mode is cooled down；D, the hard area of the component to obtaining after stamping carries out carbon partition processing, makes carbon from martensite to Austria
It is spread in family name's body.
According to another preferred embodiment of the invention, a kind for the treatment of process for being used to obtain gradient distribution performance is provided,
It is characterized in that, comprises the following steps：A, prepare blank material, blank material is divided into the region in hard area to be formed and the area of soft zone to be formed
Domain；B, the region in hard area to be formed is heated to 720 DEG C or more, its microstructure is made to be changed into austenite, while keep treating shape
Temperature into the region of soft zone is less than 720 DEG C；C, blank material is integrally carried out it is stamping, and with arbitrary cold after stamping
But mode is cooled down；D, the hard area of the component to obtaining after stamping carries out carbon partition processing, makes carbon from martensite to Austria
It is spread in family name's body.
Further embodiment according to the present invention provides a kind of component with gradient distribution performance, which is characterized in that
The component is made up of the treatment process of above preferred embodiment.
In the scheme of the present invention, hard area is different with the heating process of soft zone（The non-full austenite heating of soft zone）, punching
Pressing formation technique soft zone is consistent with hard area, therefore mold modification is not required, and reliability of technology is good.Another scheme of the present invention is then
It is to first pass through process for stamping and forming to form formed parts, then soft zone is individually heat-treated, is not had to stamping die and technique
There is any influence.It is emphasized that the soft zone elongation percentage that the two schemes of the present invention are obtained can ensure that more than 15%, preferably
For 25~35%, it is much better than the level of the prior art.
It should be noted that in the present specification, capability gradient part includes but not limited to the B columns of automobile, A columns, preceding
Longeron etc.." hard area " refers to the hardened area that intensity is high on part, and " soft zone " refers to that intensity is low on part and area that elongation percentage is high
Domain.By taking automobile B-column as an example, hard area is that upper end needs to prevent the region that collision invades, and soft zone is that lower end needs to absorb collision energy
Region.
The microstructure of soft zone in terms of area including：30% to 60% retained austenite, 40% to 70% body-centered cubic are brilliant
Martensite or ferrite, the carbide less than 3% of body structure.The mechanical property of soft zone is：900~1500MPa of tensile strength,
Elongation percentage is more than 15%.
The microstructure in hard area in terms of area including：3% to 23% retained austenite, the carbide less than 2%, remaining be
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%。
Description of the drawings
The preferred embodiment of the present invention described below with reference to the accompanying drawings, in attached 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 the schematic diagram of the automobile B-column containing hard area and soft zone.
It is pointed out that the processing route that is subjected to of solid line representative in diagram, and dotted line represent it is nonessential optional
Processing route.
Specific embodiment
The process route of the present invention is more fully described below with reference to exemplary embodiment.Following embodiment is intended to solve
Release the illustrative process route of the present invention, it will be apparent to those skilled in the art be that the present invention is not restricted to these and implement
Example.
It according to the present invention, can provide first a kind of for stamping steel, the steel wrap by weight percentage
0.22~0.48% C, 5~9.5% Mn, Fe and the inevitable impurity of 0.2~3.0% Si+Al and surplus is included,
Described in steel be hot rolled coil（Plate）, hot rolling acid-cleaning volume（Plate）, cold rolled annealed volume（Plate）, cold rolling coating volume（Plate）One of.Its is soft
Area part is before stamping（Scheme one, soft zone temperature controls in the austenitizing heating process of hard area）Or after drop stamping
（Scheme two, soft zone individually heats）It is heated to 600~780 DEG C of heat preservations（680,700,720,750 DEG C of isothermals wherein may be selected
Degree）0.5~60 minute（The times such as 1,3,5,10,20,30,40,50 wherein may be selected）Heat treatment and obtain.Utilize thermodynamics
Soft com-puting goes out the variation of manganese, carbon and other alloying elements in austenite when two-phase section annealing balances.Binding constituents design and processes
Selection, soft zone obtain the volume fraction of retained austenite 30%~60%, the martensite of volume fraction 40%~70%（Ferrite）
Tissue and the carbide less than 3%.Since carbon and manganese element are spread into austenite and rich in the heating process of soft zone
Collection, and carbon content and manganese content are designed in alloy and has reached 0.22% and more than 5% respectively, thus with the medium managese steel pair of the prior art
Than, it need not reach or can form stable retained austenite close to the carbon in austenite during thermodynamical equilibrium and manganese content,
The carbon content in retained austenite is finally surveyed under above-mentioned heating process more than 0.5%, manganese content is more than 7%, the crystalline substance of austenite
Grain is less than 2 μm or austenite lath thickness is less than 1 μm.For steel plate in deformation process, retained austenite has high deformation in itself
Ability and toughness, and generation martensitic traoformation and/or deformation twin are conducive to improve the energy-absorbing of steel plate inside retained austenite
Property and elongation percentage.
The present invention composition design of the steel based on manganese in high-carbon, carbon content between 0.22~0.48%, preferably 0.25~
0.45%, manganese content is preferably 6~8% between 5~9.5%.Carbon and manganese are all among the austenite stabilizing elements, the strong reduction of energy
The austenitizing temperature and martensite of steel start phase transition temperature, during annealing heat-treats, form austenite/ferritic plate
Alternating structure, and carbon and manganese partition make into austenite below austenite stabilization to room temperature, retained austenite has height in itself
Deformability and toughness, TRIP effects can also occur in deformation process and gradually mutually become martensite, improve steel intensity and
Ductility.Particularly, the composition design and the steel of annealing process optimized in steel of the invention, retained austenite have higher
Carbon and manganese, the stacking fault energy of partial austenitic is higher, and deformation twin is formed in deformation process, can further improve work hardening rate
And the strength of materials and ductility are improved simultaneously.When carbon and relatively low manganese content, to obtain more austenite, preferably moved back with it
Fiery temperature needs to improve, and causes carbon and manganese content reduction and crystal grain in austenite coarseer, and causes stabilization of austenite poor,
The obdurability of steel reduces in deformation process.When carbon content is higher, hypereutectoid tissue may be formed, in above-mentioned heating process
It easily forms more coarse carbide and deteriorates the mechanical property of steel, and further improving for carbon content can deteriorate hard area
Toughness.It is found by the applicant that the control of Mn contents 5~9.5%, carbon content control can obtain preferably between 0.22~0.48%
Strong plasticity.
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%.By at least one of these ingredients and the combination of above-mentioned basis, the superelevation of punching component can be further ensured that
Obdurability matches so that its mechanical mechanics property reaches：0.5~1.2GPa of yield strength, 1.0~1.5GPa of tensile strength, by force
Modeling product（Tensile strength × elongation percentage）More than 25GPa %.
According to a preferred embodiment of the present invention, the steel include hot rolled steel plate, cold-rolled steel sheet or with coated layers
Steel plate.The steel plate with coated layer can be zinc coating steel plate, it be formed on metal zinc layers hot rolled steel plate or
Cold-rolled steel sheet.The zinc coating steel plate is included selected from galvanizing by dipping（GI）, zinc-plated annealing（GA）, zinc plating or the plating of zinc-ferroelectricity
(GE) one kind in.The steel plate with coated layer also can be the hot rolled steel plate or cold-rolled steel sheet for being formed on al-si layer,
Or organic coating steel plate or steel plate with other galvanneal coatings.
Several selection process routes of the gradient distribution property treatment technique of steel of the present invention are described more fully below, it can be
The performance of gradient distribution is realized on Same Part.Certainly, it should be appreciated by those skilled in the art process routes of the invention
It is not limited to concrete technology route described below.
Process route 1：
First, the plate after blank material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Blank material for example may be used
For ingredient and the blank material of performance with above-mentioned steel.
Then, as shown in Figure 1, integrally being made annealing treatment to blank material, light plate and coil of strip etc. can be continuous in steel plant
Anneling production line or continuous annealing coating production line are heat-treated.For example, blank material can be integrally heated to 600~720 DEG C, protect
Temperature 0.5~60 minute, then with the arbitrary type of cooling（Such as in the air-cooled of continuous annealing production line, air cooling or mould in drop stamping
Cooling or air-cooled in tool）, -100 DEG C or more of a certain temperature is cooled to, is preferably cooled to room temperature.In the annealing
Afterwards, the microstructure of blank material may include in terms of area：30% to 60% retained austenite, 40% to 70% body centred cubic crystal
Martensite or ferrite, the carbide less than 3% of structure, wherein, include by weight percentage in the retained austenite big
In the Mn equal to 7% and the carbon more than or equal to 0.5%.After annealed processing, the tensile strength of blank material is 900~1500MPa,
Elongation percentage is up to more than 15%, therefore the blank material has favorable forming property at room temperature.
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, simultaneously
Ensure that the temperature of the region of soft zone to be formed in the process is less than 720 DEG C（For example, the region of soft zone to be formed is not added
Heat and hold it in room temperature or be heated to 650 DEG C）.It in the process, for example, can be first by hard area sensing heating
To such as 650 DEG C, soft zone does not heat（It is maintained at room temperature or a relatively low temperature is risen to due to heat transfer when hard area is heated
Degree）, then blank is integrally inserted in the stove that furnace temperature is such as 780 DEG C and heated.For hard area, from 650 DEG C of heating
It is shorter to heating time needed for 780 DEG C, such as 40 seconds, followed by and keep the temperature such as 20 seconds to realize the homogenization of austenite structure,
Then the blank whole time in 780 DEG C of stove is such as 1 minute.In this 1 minute, soft zone is since charging temperature is low, 780
DEG C stove in cannot be heated to 780 DEG C, as long as in practice control below 720 DEG C.It is it is pointed out that traditional
Hot forming Steel material（Such as 22MnB5）Because austenitizing temperature far above the present invention involved in material due to can not be at 1 minute
The homogenization of austenite structure is realized in heating time.
Then, blank material is integrally carried out stamping.It, can be via arbitrary cooling after hard area is stamping in full austenite area
Mode（Such as cooling or air-cooled in mold）It is cooled to its martensite start temperature point（Ms）150~260 DEG C below.Soft zone
After stamping, it can be cooled down via the type of cooling consistent with hard area, such as cooling or air-cooled in mold.Soft zone it is micro-
See tissue may include in terms of area：The martensite or iron of 30% to 60% austenite, 40% to 70% body-centered cubic crystal structure
Ferritic and the carbide less than 3%.
Then, the component to obtaining after stamping（That is formed parts）Hard area carry out carbon partition processing, such as will be hard
Area is heated to 160~450 DEG C, heat preservation 1~10000 second, is allowed to carbon occurs to spread into austenite from oversaturated martensite, causes
Make in austenite rich carbon, so as to greatly improve the stability of austenite, increase its residual quantity at room temperature.Preferred situation
It is that phase transformation of the martensite to austenite occurs, so as to increase retained austeniteization content, improves its mechanical performance.In addition, to soft
For area comes, consistent carbon partition processing can be carried out with hard area or does not carry out the processing of carbon partition to it (that is, hard area
Individually carry out the processing of carbon partition).Whether carbon partition processing is carried out, the mechanical property of the soft zone of formed parts can reach anti-
900~1500MPa of tensile strength, and elongation percentage more than 15%.But in order to easy to operate, preferably formed parts can integrally be carried out
The processing of carbon partition.
Process route 2：
First, the plate after blank material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Blank material for example may be used
For ingredient and the blank material of performance with above-mentioned steel.
Then, as shown in Fig. 2, the region of the soft zone to be formed and hard area to blank material be carried out at the same time heating and keep the temperature 0.5~
60 minutes, 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 in hard area to be formed
Temperature is 720~850 DEG C, its microstructure is made to be changed into austenite.During heating and thermal insulation, the microstructure of soft zone is with area
Meter includes：30% to 60% retained austenite, the martensite of 40% to 70% body-centered cubic crystal structure or ferrite, less than 3%
Carbide, include the Mn more than or equal to 7% and the carbon more than or equal to 0.5% in retained austenite by weight percentage,
And hard area includes fully austenitic structure and the carbide less than 3%.In the process, for example, can first add hard area sensing
Heat is to such as 650 DEG C, and for soft zone by sensing heating to such as 500 DEG C, then it is such as 780 DEG C that blank is integrally inserted to furnace temperature
It is heated in stove.For hard area, it is shorter to be heated to heating time needed for 780 DEG C from 650 DEG C, such as 40 seconds, followed by and
To realize the homogenization of austenite structure, then the blank whole time in 780 DEG C of stove is such as 1 point within such as 20 seconds for heat preservation
Clock.In this 1 minute, soft zone cannot be heated to 780 DEG C since charging temperature is low in 780 DEG C of stove, as long as in practice
Control is below 720 DEG C.
Then, blank material is integrally carried out it is stamping, with the arbitrary type of cooling after punching press（Cooling or air-cooled in mold）It is cold
But.Hard area is cooled to below its martensite start temperature point 150~260 DEG C, and soft zone is cooled to -50 DEG C or more arbitrary
Temperature.Preferably, in order to facilitate punching press and the implementation of cooling technique, the whole type of cooling according to hard area of formed parts cools down,
Soft zone structure property can also be met the requirements.
Then, carbon partition processing is carried out to the hard area of formed parts, such as hard area is heated to 160~450 DEG C, heat preservation 1
It~10000 seconds, is allowed to carbon occurs to spread into austenite from oversaturated martensite, causes rich carbon in austenite, so as to significantly
The stability of austenite is improved, increases its residual quantity at room temperature.Preferably, martensite occurs to austenite
Phase transformation so as to increase retained austeniteization content, improves its mechanical performance.In addition, for soft zone is come, one can be carried out with hard area
The carbon partition processing of cause does not carry out it carbon partition processing (that is, hard area individually carries out the processing of carbon partition).No matter
Whether carbon partition processing is carried out, and the mechanical property of the soft zone of formed parts can reach 900~1500MPa of tensile strength, and prolong
Stretch rate more than 15%.But in order to easy to operate, preferably can formed parts integrally be carried out with carbon partition processing.
Process route 3：
First, the plate after blank material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Blank material for example may be used
For ingredient and the blank material of performance with above-mentioned steel.
Then, as shown in figure 3, blank material to be integrally heated to 720~850 DEG C, 0.5~60min is kept the temperature, it is made to be organized as entirely
Austenite structure and the carbide less than 3%.
Then, blank material is integrally carried out it is stamping, it is stamping after through the arbitrary type of cooling（Cooling or empty in mold
It is cold）Cooling.In cooling procedure, the region in hard area to be formed is cooled to 150 below its martensite start temperature point~
260 DEG C, and soft zone is cooled to less than -100 DEG C or more 600 DEG C of arbitrary temp.Preferably, in order to facilitate the work of punching press and cooling
Skill is implemented, and the whole type of cooling according to hard area of formed parts is cooled down, soft zone structure property can also be met the requirements.
Then, carbon partition processing is carried out to the region in the hard area to be formed of the formed parts after stamping, such as will be hard
Area is heated to 160~450 DEG C, heat preservation 1~10000 second, is allowed to carbon occurs to spread into austenite from oversaturated martensite, causes
Make in austenite rich carbon, so as to greatly improve the stability of austenite, increase its residual quantity at room temperature.Preferred situation
It is that phase transformation of the martensite to austenite occurs, so as to increase retained austeniteization content, improves its mechanical performance.In addition, to soft
For area comes, consistent carbon partition processing can be carried out with hard area or does not carry out the processing of carbon partition to it (that is, hard area
Individually carry out the processing of carbon partition).Whether carbon partition processing is carried out, the mechanical property of the soft zone of formed parts can reach anti-
900~1500MPa of tensile strength, and elongation percentage more than 15%.But in order to easy to operate, preferably formed parts can integrally be carried out
The processing of carbon partition.
Then, as shown in figure 3, being individually heat-treated again to soft zone, 600~720 DEG C are heated to, heat preservation 0.5~60
Minute, then in any way（It is such as air-cooled）It is cooled to room temperature.After the heat treatment, the microstructure of the steel is with area
Meter includes：30% to 60% retained austenite, the martensite or ferrite of 40% to 70% body-centered cubic crystal structure, less than 3%
Carbide, include the Mn more than or equal to 7% and the carbon more than or equal to 0.5% in retained austenite by weight percentage,
Its mechanical property reaches 900~1500MPa of tensile strength, elongation percentage more than 15%.
Process route 4：
First, the plate after blank material, such as steel plate, coil of strip or blanking is prepared or through preformed component.Blank material for example may be used
For ingredient and the blank material of performance with above-mentioned steel.
Then, as shown in figure 4, blank material to be integrally heated to 720~800 DEG C, 0.5~60min is kept the temperature, it is made to be organized as entirely
Austenite structure and the carbide less than 3%.
Then, blank material is integrally carried out it is stamping, it is stamping after through the arbitrary type of cooling（Cooling or empty in mold
It is cold）Cooling.In cooling procedure, the region in hard area to be formed is cooled to 150 below its martensite start temperature point~
260 DEG C, and soft zone is cooled to -100 DEG C or more above arbitrary temps.Preferably, it is real in order to facilitate the technique of punching press and cooling
It applies, the whole type of cooling according to hard area of formed parts is cooled down, soft zone structure property can also be met the requirements.
Then, as shown in figure 4, being individually heat-treated again to soft zone, such as 600~720 DEG C are heated to, heat preservation 0.5
~60 minutes, then in any way（It is such as air-cooled）It is cooled to room temperature.After the heat treatment, the microstructures of the steel with
Area meter includes：30% to 60% retained austenite, the martensite or ferrite of 40% to 70% body-centered cubic crystal structure are low
Include being more than or equal to 7% Mn and more than or equal to 0.5% by weight percentage in 3% carbide, retained austenite
Carbon, mechanical property reach 900~1500MPa of tensile strength, elongation percentage more than 15%.
Then, carbon partition processing is carried out to the region in the hard area to be formed of the formed parts after stamping, such as will be hard
Area is heated to 160~450 DEG C, heat preservation 1~10000 second, is allowed to carbon occurs to spread into austenite from oversaturated martensite, causes
Make in austenite rich carbon, so as to greatly improve the stability of austenite, increase its residual quantity at room temperature.Preferred situation
It is that phase transformation of the martensite to austenite occurs, so as to increase retained austeniteization content, improves its mechanical performance.In addition, to soft
For area comes, consistent carbon partition processing can be carried out with hard area or does not carry out the processing of carbon partition to it (that is, hard area
Individually carry out the processing of carbon partition).Whether carbon partition processing is carried out, the mechanical property of the soft zone of formed parts can reach anti-
900~1500MPa of tensile strength, and elongation percentage more than 15%.But in order to easy to operate, preferably formed parts can integrally be carried out
The processing of carbon partition.
It is pointed out that in the individual heat treatment process of soft zone, add for example, such as flame can be used in soft zone
The modes such as heat, sensing heating, laser heating heat or the whole heating furnace that enters is using the different method of soft or hard area's heating temperature
The baffle of thermal radiation resistant is placed in processing, such as hard area up and down, and coating heat insulating coat on heat-barrier material and hard area is wrapped up on hard area.
According to an embodiment of the invention, by carrying out different heating process to hard area and soft zone（The non-full austenite of soft zone
Heating）, but the process for stamping and forming in soft zone and hard area is consistent, therefore mold modification is not required, reliability of technology is good.
The present invention above-mentioned process route can be used for the parts for manufacturing any required gradient distribution performance, including but not
It is limited to B columns, A columns, front longitudinal beam of automobile etc..Fig. 5 is shown made of a kind of above-mentioned treatment process by the present invention comprising hard
The schematic diagram of the automobile B-column of area and soft zone, hard area are that upper end needs to prevent the region that collision invades, and soft zone is that lower end needs to inhale
Receive the region of collision energy.
According to an embodiment of the invention, the microstructure of the soft zone of made formed parts in terms of area including：30% to
60% retained austenite, the martensite of 40% to 70% body-centered cubic crystal structure or ferrite, the carbide less than 3%.It is soft
The mechanical property in area is：900~1500MPa of tensile strength, elongation percentage are more than 15%.The microstructure in hard area in terms of area including：
3% to 23% retained austenite, 0~2% carbide, remaining be martensite.The mechanical property in hard area is：Yield strength is more than
1200MPa, tensile strength are more than 1600MPa, and elongation percentage is more than 10%.
The foregoing describe the preferred embodiment of the present invention, but those skilled in the art is not it is to be understood that taking off
Any possible change or replacement carried out on the premise of from present inventive concept, all belong to the scope of protection of the present invention.
Claims (13)
1. a kind for the treatment of process for being used to obtain gradient distribution performance, which is characterized in that comprise the following steps：
A, prepare blank material, blank material is divided into the region in hard area to be formed and the region of soft zone to be formed, the carbon of the blank material contains
Amount is by weight percentage between 0.22~0.48%, and manganese content is between 5~9.5%；
B, the region in hard area to be formed is heated to 720~850 DEG C, its microstructure is made to be changed into austenite, while keep treating
The temperature for forming the region of soft zone is less than 720 DEG C；
C, blank material is integrally carried out stamping, and is cooled down with the arbitrary type of cooling after stamping；
D, the hard area of the component to obtaining after stamping carries out carbon partition processing, and carbon is made to be spread from martensite into austenite.
It is 2. as described in claim 1 for obtaining the treatment process of gradient distribution performance, which is characterized in that after step and
It is further comprising the steps of before step B：Blank material is integrally made annealing treatment, i.e., blank material is integrally heated to 600~720 DEG C,
Heat preservation 0.5~60 minute, is then cooled to room temperature with the arbitrary type of cooling.
3. the treatment process as described in claim 1 for being used to obtain gradient distribution performance, which is characterized in that in stepb to base
The soft zone to be formed of material and the region in hard area are carried out at the same time heating and keep the temperature 0.5~60 minute, wherein, the region of soft zone to be formed
Heating and thermal insulation temperature is more than or equal to 600 DEG C, less than 720 DEG C.
4. the treatment process for being used to obtain gradient distribution performance as any one of claim 1-3, which is characterized in that in step
In rapid C, hard area is cooled to below its martensite start temperature point 150~260 DEG C, soft zone is cooled to -100 DEG C or more
Arbitrary temp.
5. the treatment process for being used to obtain gradient distribution performance as any one of claim 1-3, which is characterized in that in step
Hard area is heated to 160~450 DEG C in rapid D, keeps the temperature 1~10000 second.
6. the treatment process for being used to obtain gradient distribution performance as any one of claim 1-3, which is characterized in that in step
In rapid D, soft zone is also carried out to carry out consistent carbon partition processing with hard area or is handled without carbon partition.
7. the treatment process for being used to obtain gradient distribution performance as any one of claim 1-3, which is characterized in that punching press
The microstructure of the soft zone of the component obtained after shaping in terms of area including：30% to 60% retained austenite, 40% to 70%
Martensite or ferrite, the carbide less than 3% of body-centered cubic crystal structure, the mechanical property of soft zone are：Tensile strength 900
~1500MPa, elongation percentage are more than 15%；The microstructure in hard area in terms of area including：3% to 23% retained austenite, 0~2%
Carbide, remaining be martensite, the mechanical property in hard area is：Yield strength is more than 1200MPa, and tensile strength is more than
1600MPa, elongation percentage are more than 10%.
8. a kind for the treatment of process for being used to obtain gradient distribution performance, which is characterized in that comprise the following steps：
A, prepare blank material, blank material is divided into the region in hard area to be formed and the region of soft zone to be formed, the carbon of the blank material contains
Amount is by weight percentage between 0.22~0.48%, and manganese content is between 5~9.5%；
Blank material is integrally heated to 720~800 DEG C, keep the temperature 0.5~60min B, it is austenite to make its structural transformation；
C, blank material is integrally carried out it is stamping, it is stamping after through the arbitrary type of cooling cool down；
D, the hard area of the component to obtaining after stamping carries out carbon partition processing, and carbon is made to be spread from martensite into austenite；
E, soft zone is individually heat-treated before or after step D, that is, is heated to 600~720 DEG C, keep the temperature 0.5~60 point
Then clock is cooled to room temperature in any way.
9. the treatment process as claimed in claim 8 for being used to obtain gradient distribution performance, which is characterized in that in step C, will treat
The region for forming hard area is cooled to below its martensite start temperature point 150~260 DEG C, and soft zone be cooled to -100 DEG C with
On arbitrary temp.
10. the treatment process as claimed in claim 8 for being used to obtain gradient distribution performance, which is characterized in that independent to soft zone
After being heat-treated, the microstructure of blank material or stamping component in terms of area including：30% to 60% retained austenite,
The martensite or ferrite of 40% to 70% body-centered cubic crystal structure, the carbide less than 3%, with weight in retained austenite
Measuring percentages includes the Mn more than or equal to 7% and carbon more than or equal to 0.5%, mechanical property reach tensile strength 900~
1500MPa, elongation percentage more than 15%.
11. a kind of component with gradient distribution performance, which is characterized in that the component passes through any one of claim 1-10 institutes
The treatment process stated is made.
12. component as claimed in claim 11, which is characterized in that the component includes B columns, A columns, the front longitudinal beam of automobile.
13. the component as described in claim 11 or 12, which is characterized in that the microstructure of the soft zone of the component is in terms of area
Including：30% to 60% retained austenite, the martensite of 40% to 70% body-centered cubic crystal structure or ferrite, less than 3%
Carbide, the mechanical property of soft zone are：900~1500MPa of tensile strength, elongation percentage are more than 15%；The microstructure in hard area is with face
Product meter includes：3% to 23% retained austenite, 0~2% carbide, remaining be martensite, the mechanical property in hard area is：Surrender
Intensity is more than 1200MPa, and tensile strength is more than 1600MPa, and elongation percentage is more than 10%.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| ES16905967T ES2971678T3 (en) | 2015-12-04 | 2016-07-20 | Treatment process to obtain progressive performance and member thereof |
| PCT/CN2016/090629 WO2017219427A1 (en) | 2015-12-04 | 2016-07-20 | Treatment process for obtaining graded performance and member thereof |
| EP16905967.2A EP3473735B1 (en) | 2016-06-20 | 2016-07-20 | Treatment process for obtaining graded performance and member thereof |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| 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 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106011418A CN106011418A (en) | 2016-10-12 |
| CN106011418B true CN106011418B (en) | 2018-05-22 |
Family
ID=55670798
Family Applications (3)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510878323.5A Pending CN105483531A (en) | 2015-12-04 | 2015-12-04 | Steel for stamping formation and forming component and heat treatment method thereof |
| 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 |
Family Applications Before (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510878323.5A Pending CN105483531A (en) | 2015-12-04 | 2015-12-04 | Steel for stamping formation and forming component and heat treatment method thereof |
| CN201580085081.2A Active CN108474081B (en) | 2015-12-04 | 2015-12-25 | Steel material for press forming, formed member thereof, and heat treatment method |
Country Status (3)
| Country | Link |
|---|---|
| CN (3) | CN105483531A (en) |
| ES (1) | ES2971678T3 (en) |
| WO (2) | WO2017092104A1 (en) |
Families Citing this family (32)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10619223B2 (en) | 2016-04-28 | 2020-04-14 | GM Global Technology Operations LLC | Zinc-coated hot formed steel component with tailored property |
| WO2018055425A1 (en) * | 2016-09-22 | 2018-03-29 | Arcelormittal | High strength and high formability steel sheet and manufacturing method |
| CN107287401B (en) * | 2017-06-10 | 2020-10-09 | 山东建筑大学 | Method for improving performance of traditional Q & P steel through carbon-manganese comprehensive distribution |
| CN110944765B (en) * | 2017-07-25 | 2022-02-25 | 蒂森克虏伯钢铁欧洲股份公司 | Sheet metal component produced by hot forming a flat steel product and method for producing the same |
| CN114369768A (en) * | 2017-11-02 | 2022-04-19 | 重庆哈工易成形钢铁科技有限公司 | Steel material for hot press forming, hot press forming process, and formed member |
| CN111542635B (en) * | 2017-12-28 | 2022-07-01 | 通用汽车环球科技运作有限责任公司 | Steel for hot stamping with enhanced oxidation resistance |
| JP7354119B2 (en) * | 2018-02-08 | 2023-10-02 | タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップ | Method of forming articles from steel blanks coated with zinc or zinc alloys |
| JP7214973B2 (en) * | 2018-03-30 | 2023-01-31 | マツダ株式会社 | HOT PRESSING METHOD AND PROCESSING APPARATUS |
| US11613789B2 (en) | 2018-05-24 | 2023-03-28 | GM Global Technology Operations LLC | Method for improving both strength and ductility of a press-hardening steel |
| CN108754103B (en) * | 2018-06-07 | 2019-08-30 | 浙江大学 | A kind of superfine crystalline pure iron functionally gradient material (FGM) preparation method |
| WO2019241902A1 (en) * | 2018-06-19 | 2019-12-26 | GM Global Technology Operations LLC | Low density press-hardening steel having enhanced mechanical properties |
| WO2020256031A1 (en) * | 2019-06-17 | 2020-12-24 | 日本製鉄株式会社 | Bonded joint, and member for automobile |
| US11530469B2 (en) | 2019-07-02 | 2022-12-20 | GM Global Technology Operations LLC | Press hardened steel with surface layered homogenous oxide after hot forming |
| DE102019215053A1 (en) * | 2019-09-30 | 2021-04-01 | Thyssenkrupp Steel Europe Ag | Method for producing an at least partially tempered sheet steel component and at least partly tempered sheet steel component |
| CN110735022A (en) * | 2019-11-20 | 2020-01-31 | 安徽工业大学 | High-strength-ductility ultrahigh-strength automobile steel with cold and hot forming flexibility application |
| CN112233735B (en) * | 2020-09-07 | 2022-04-19 | 包头钢铁（集团）有限责任公司 | Design method for chemical components of pearlitic rail steel |
| CN113136529B (en) * | 2021-03-10 | 2022-05-20 | 首钢集团有限公司 | Medium manganese drill rod and preparation method thereof |
| CN113106339B (en) * | 2021-03-22 | 2022-02-11 | 北京科技大学 | Preparation method of ultrahigh-strength high-plasticity high-temperature-oxidation-resistant hot stamping formed steel |
| CN115261742B (en) * | 2021-04-30 | 2023-06-13 | 宝山钢铁股份有限公司 | Hot stamping part with tensile strength of 1000MPa and manufacturing method thereof |
| CN113416893B (en) * | 2021-05-24 | 2022-10-18 | 鞍钢股份有限公司 | High-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for automobile and production method thereof |
| CN113462956B (en) * | 2021-05-25 | 2022-06-14 | 上海大学 | Large-section high-hardenability high-strength medium manganese forged steel and preparation method thereof |
| CN115491583B (en) * | 2021-06-18 | 2023-09-05 | 上海梅山钢铁股份有限公司 | Ultra-deep drawing cold-rolled hot-dip aluminum-zinc steel plate and manufacturing method thereof |
| CN114032475B (en) * | 2021-10-15 | 2022-12-16 | 首钢集团有限公司 | High-strength cold-rolled hot-galvanized medium manganese steel, preparation method thereof and hot-formed part |
| 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 |
| CN114318161B (en) * | 2021-12-15 | 2022-06-03 | 常州大学 | Low-temperature high-strain-rate superplastic medium manganese steel and preparation method thereof |
| CN114293103B (en) * | 2021-12-31 | 2022-07-29 | 台州绿创包装容器股份有限公司 | Metal aerosol can |
| CN114686774B (en) * | 2022-03-08 | 2022-12-02 | 四川大学 | High-strength high-toughness nano precipitation-strengthened ultrafine-grained martensite austenite dual-phase steel and preparation method thereof |
| 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 |
| CN114836688B (en) * | 2022-04-20 | 2023-10-27 | 攀钢集团攀枝花钢铁研究院有限公司 | Reverse phase transformation niobium microalloyed light high-strength steel and production method thereof |
| CN115161549A (en) * | 2022-05-27 | 2022-10-11 | 郑州轻研合金科技有限公司 | High-tensile-strength alloy steel plate and preparation method thereof |
| CN115323135B (en) * | 2022-08-12 | 2023-05-23 | 华北理工大学 | Preparation method of ultra-high strength-plastic product medium manganese steel with strength-plastic product not lower than 45GPa percent |
| CN116516252B (en) * | 2023-04-28 | 2024-03-19 | 鞍钢股份有限公司 | 1200MPa ultra-high strength plastic hot rolled Mn-TRIP steel and preparation method thereof |
Family Cites Families (23)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5983744A (en) * | 1982-11-04 | 1984-05-15 | Sumitomo Metal Ind Ltd | Shape memory alloy |
| JPH0768583B2 (en) * | 1984-03-07 | 1995-07-26 | 住友金属工業株式会社 | High-tensile cold-rolled steel sheet manufacturing method |
| JPH04333526A (en) * | 1991-05-08 | 1992-11-20 | Sumitomo Metal Ind Ltd | Hot rolled high tensile strength steel plate having high ductility and its production |
| FR2851774B1 (en) * | 2003-02-27 | 2006-08-18 | Inst Francais Du Petrole | LOW-ALLOY ANTICOKAGE STEELS WITH INCREASED SILICON AND MANGANESE CONTENT, AND THEIR USE IN REFINING AND PETROCHEMICAL APPLICATIONS |
| SE528130C2 (en) | 2004-10-04 | 2006-09-12 | Gestamp Hardtech Ab | Ways to heat mold and harden a sheet metal |
| KR100979854B1 (en) * | 2005-08-03 | 2010-09-02 | 수미도모 메탈 인더스트리즈, 리미티드 | Hot rolled steel sheet, cold rolled steel sheet, and process for producing the same |
| SE531499C2 (en) | 2007-11-15 | 2009-04-28 | Gestamp Hardtech Ab | B-pillar for vehicles |
| JP5637342B2 (en) * | 2008-09-18 | 2014-12-10 | 国立大学法人 岡山大学 | Hot-pressed steel plate member and method for manufacturing the same |
| JP5287770B2 (en) * | 2010-03-09 | 2013-09-11 | Ｊｆｅスチール株式会社 | High strength steel plate and manufacturing method thereof |
| SE1000236A1 (en) | 2010-03-16 | 2011-02-22 | Gestamp Hardtech Ab | Pressure curing plant and means of pressure curing |
| CN102212742B (en) | 2011-05-16 | 2013-08-28 | 马鸣图 | Hot-stamping automobile part with flexibly-distributed intensity and control method thereof |
| FI20115832L (en) * | 2011-08-26 | 2013-02-27 | Rautaruukki Oyj | Method for manufacturing a steel product with excellent mechanical properties, steel product manufactured with the method and use of strain-hardened steel |
| JP5982906B2 (en) * | 2012-03-19 | 2016-08-31 | Ｊｆｅスチール株式会社 | Method for producing high-strength hot-dip galvanized steel sheet |
| JP5982905B2 (en) * | 2012-03-19 | 2016-08-31 | Ｊｆｅスチール株式会社 | Method for producing high-strength hot-dip galvanized steel sheet |
| JP5962541B2 (en) * | 2012-07-23 | 2016-08-03 | Ｊｆｅスチール株式会社 | Manufacturing method of high-strength steel sheet |
| JP5962540B2 (en) * | 2012-07-23 | 2016-08-03 | Ｊｆｅスチール株式会社 | Manufacturing method of high-strength steel sheet |
| EP2940176B1 (en) * | 2013-03-04 | 2019-03-27 | JFE Steel Corporation | High-strength steel sheet, method for manufacturing same, high-strength molten-zinc-plated steel sheet, and method for manufacturing same |
| CN103409613B (en) | 2013-08-30 | 2014-09-10 | 上海交通大学 | Method for realizing gradient property distribution of hot stamping workpiece |
| CN103521581B (en) | 2013-10-23 | 2015-12-02 | 武汉理工大学 | Obtain method and the mould of mechanical performance gradient drop stamping part |
| CN103878237B (en) | 2014-03-24 | 2015-04-15 | 华中科技大学 | Method for machining high-strength steel hot stamping formed parts |
| CN104726677B (en) * | 2015-03-30 | 2017-03-15 | 盐城科奥机械有限公司 | Fixed liner plate formula van-type heating furnace and its hot forming segmentation reinforcement process |
| CN104729278B (en) * | 2015-03-30 | 2016-09-28 | 盐城科奥机械有限公司 | Motion roller-type van-type heating furnace and hot forming segmentation reinforcement process |
| CN104831020A (en) | 2015-04-03 | 2015-08-12 | 燕山大学 | Method for stamping quenching molding in non-uniform temperature field |
-
2015
- 2015-12-04 CN CN201510878323.5A patent/CN105483531A/en active Pending
- 2015-12-25 WO PCT/CN2015/098890 patent/WO2017092104A1/en active Application Filing
- 2015-12-25 CN CN201580085081.2A patent/CN108474081B/en active Active
-
2016
- 2016-06-20 CN CN201610440901.1A patent/CN106011418B/en active Active
- 2016-07-20 WO PCT/CN2016/090629 patent/WO2017219427A1/en unknown
- 2016-07-20 ES ES16905967T patent/ES2971678T3/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN108474081A (en) | 2018-08-31 |
| ES2971678T3 (en) | 2024-06-06 |
| WO2017219427A1 (en) | 2017-12-28 |
| CN106011418A (en) | 2016-10-12 |
| CN108474081B (en) | 2021-09-17 |
| CN105483531A (en) | 2016-04-13 |
| WO2017092104A1 (en) | 2017-06-08 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106011418B (en) | For obtaining the treatment process of gradient distribution performance and its component | |
| JP5727037B2 (en) | Method for producing a cured structural element | |
| US8733144B2 (en) | Method and apparatus for hot forming and hardening a blank | |
| KR101707019B1 (en) | Method for producing workpieces from lightweight steel having material properties that can be adjusted over the wall thickness | |
| US7618503B2 (en) | Method for improving the performance of seam-welded joints using post-weld heat treatment | |
| JP6093702B2 (en) | Cold rolled flat steel product made from multiphase steel and its manufacturing method | |
| FI3728670T3 (en) | Cold-rolled and heat-treated steel sheet, resistance spot welded joint and their manufacturing methods | |
| JP6001541B2 (en) | Cold rolled flat steel product made from multiphase steel and its manufacturing method | |
| WO2015037060A1 (en) | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article | |
| WO2015037061A1 (en) | Hot-pressing steel plate, press-molded article, and method for manufacturing press-molded article | |
| CA2930313A1 (en) | Structural component including a tempered transition zone | |
| CA3076934C (en) | Press hardened steel with tailored properties after novel thermal treatment | |
| EP3473735B1 (en) | Treatment process for obtaining graded performance and member thereof | |
| WO2008088834A1 (en) | Method for improving the performance of seam-welded joints using post-weld heat treatment | |
| CN104630647B (en) | A kind of preparation method of high-strength hot-dip zinc-coated Q ＆ P steel | |
| JP5894470B2 (en) | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product | |
| CA2877175C (en) | Microtreatment and microstructure of carbide containing iron-based alloy | |
| JP5894469B2 (en) | Steel sheet for hot pressing, press-formed product, and method for producing press-formed product | |
| CA2952255C (en) | High strength iron-based alloys, processes for making same, and articles resulting therefrom | |
| JP2017524813A5 (en) | ||
| Lee et al. | Effect of aluminum on thermally induced ε-martensite for Fe-Mn-C TWIP steels | |
| BR112019025123A2 (en) | steel sheet, parts, methods for making a sheet and for making a part and using a part |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |