CN107815593A - A kind of economical high-aluminum low-silicon TRIP steel of automobile using and preparation method thereof - Google Patents
A kind of economical high-aluminum low-silicon TRIP steel of automobile using and preparation method thereof Download PDFInfo
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- CN107815593A CN107815593A CN201711078318.1A CN201711078318A CN107815593A CN 107815593 A CN107815593 A CN 107815593A CN 201711078318 A CN201711078318 A CN 201711078318A CN 107815593 A CN107815593 A CN 107815593A
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- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 18
- 229910052710 silicon Inorganic materials 0.000 title claims abstract description 16
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 229910000794 TRIP steel Inorganic materials 0.000 title claims description 25
- 239000010703 silicon Substances 0.000 title abstract description 9
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 28
- 239000010959 steel Substances 0.000 claims abstract description 28
- 238000000137 annealing Methods 0.000 claims abstract description 12
- 238000000034 method Methods 0.000 claims abstract description 12
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 238000005097 cold rolling Methods 0.000 claims abstract description 8
- 238000005098 hot rolling Methods 0.000 claims abstract description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 230000008569 process Effects 0.000 claims abstract description 8
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 238000002844 melting Methods 0.000 claims abstract description 7
- 230000008018 melting Effects 0.000 claims abstract description 7
- 238000005554 pickling Methods 0.000 claims abstract description 7
- 238000005242 forging Methods 0.000 claims abstract description 6
- 238000009413 insulation Methods 0.000 claims abstract description 6
- 230000001681 protective effect Effects 0.000 claims description 10
- 239000001257 hydrogen Substances 0.000 claims description 8
- 229910052739 hydrogen Inorganic materials 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 7
- 239000007789 gas Substances 0.000 claims description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N nitrogen Substances N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 125000004435 hydrogen atom Chemical class [H]* 0.000 claims 1
- 229940062057 nitrogen 80 % Drugs 0.000 claims 1
- 238000005516 engineering process Methods 0.000 abstract description 7
- 238000010438 heat treatment Methods 0.000 abstract description 7
- 229910001563 bainite Inorganic materials 0.000 abstract description 6
- 238000012545 processing Methods 0.000 abstract description 5
- 238000005246 galvanizing Methods 0.000 abstract description 4
- 238000004519 manufacturing process Methods 0.000 abstract description 3
- 239000006104 solid solution Substances 0.000 abstract description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 abstract description 2
- 239000010960 cold rolled steel Substances 0.000 abstract description 2
- 238000007747 plating Methods 0.000 abstract description 2
- 238000001556 precipitation Methods 0.000 abstract description 2
- 238000011084 recovery Methods 0.000 abstract description 2
- 239000011701 zinc Substances 0.000 abstract description 2
- 229910052725 zinc Inorganic materials 0.000 abstract description 2
- 230000009286 beneficial effect Effects 0.000 abstract 1
- 230000007547 defect Effects 0.000 abstract 1
- 239000011572 manganese Substances 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 5
- 238000005275 alloying Methods 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 150000002431 hydrogen Chemical group 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000009966 trimming Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 239000004615 ingredient Substances 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000010583 slow cooling Methods 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 229910052720 vanadium Inorganic materials 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0273—Final recrystallisation annealing
-
- 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
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- 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 Sheet Steel (AREA)
Abstract
The invention discloses economical high-aluminum low-silicon TRIP high-strength steel of a kind of automobile using and preparation method thereof, belong to automobile using high-strength steel production technical field.The mass percent of the TRIP composition of steel is：C：0.15~0.25%, Si：0.1~0.5%, Al：1.5~3.0%, Mn：1.5~2.5%, Cu：0.1~1.0%, P<0.01%, S<0.005%, surplus Fe.Preparation method, including following process：Melting, cast, forging, insulation, hot rolling, batch, pickling, cold rolling, annealing.Contained microalloy element is few in steel, and economy is beneficial to recovery；Si is substituted with Al parts, elongation percentage is improved, strengthens the zinc-plated performance of cold-rolled steel sheet；A small amount of Cu is added, by solid solution, precipitation strength, Al is made up in terms of intensity the defects of, increases tensile strength.Technology for Heating Processing is incubated by two-phase section annealing and Bainite Region, is obtained tensile strength and is more than 780MPa, elongation percentage is more than 25%, and highest elongation percentage reaches 30%, the good cold-reduced sheet of plate shape, surface quality.Bainite Region temperature can coordinate zincincation more than 460 DEG C, realize that annealing plating is zinc integrated, produce automobile using high-strength galvanizing plate.
Description
Technical field
The invention belongs to automobile using high-strength steel production technical field, more particularly to a kind of economical high-aluminum low-silicon of automobile using
TRIP steel and preparation method thereof.
Background technology
Advanced continuous annealing proposes with coating technology for hot rolling-cooling-heat treatment integration organization Properties Control will
Ask：Develop controlled rolling of new generation and controlled cooling technique；Greenization hot-strip composition and process system are established, is realized
" resources conservation " and " technique decrement "；60~80% hot-strip intensity improves 100~200MPa, or main alloy element section
20~30% are saved, saves steel 5~10%, energy-conservation 10~15%.Low-carbon micro steel-alloy adapts to continuous annealing and galvanizing is moved back
Fire, the high-strength TRIP steel of a new generation have the good energy premium properties of intensity height, ductility, had a extensive future.Chinese invention patent Shen
Please prospectus CN102312157A disclose a kind of preparation method of high-strength cold rolling TRIP steel, composition is：C:0.18~
0.23%, Si:1.3~1.6%, Mn:2.1~2.3%, Nb:0.03~0.05%, V:0.03~0.09%, P≤0.01%, S
≤ 0.01%, Al:0.8~1.2%, N≤0.005%.Although intensity reaches 1000MPa, but elongation percentage is less than 20%.And add
It is more to enter expensive alloying elements, increases cost, silicone content is too high, and surface quality is bad, and zinc-plated performance is inadequate.
Chinese invention patent application prospectus CN106868403A discloses a kind of galvanizing of great surface quality
TRIP steel plates and its manufacture method, composition are：C:0.10~0.15%, Mn:1.20~1.80%, Al:1.20~2.40%, P
≤ 0.03%, S≤0.03%, surplus are Fe and inevitable impurity.The steel of this composition, due to eliminating in TRIP steel
Si elements are simultaneously replaced with Al, and solid solution strengthening effect significantly reduces, and the hardness of steel produced is relatively low, it is impossible to meet that young mobile is used
The requirement of steel.
The content of the invention
The problem of existing for prior art, it is an object of the invention to provide a kind of economical high-aluminum low-silicon TRIP of automobile using
Steel and preparation method thereof, being designed by using economical TRIP composition of steel, the content for improving Al ensures the zinc-plated performance of cold-reduced sheet,
The intensity of a certain amount of Cu compensation steel is added, formulates suitable cold rolled annealed technique, tensile strength is obtained and is more than 780MPa, finally
Strength and ductility product can exceed 25GPa% high-strength TRIP steel.
One aspect of the present invention provides a kind of TRIP steel, and composition is by weight percent：C：0.15~0.25%, Si：0.1~
0.5%, Al：1.5~1.8%, Mn：1.5~2.0%, Cu：0.1~1.0%, P<0.01%, S<0.08%, surplus Fe.
Another aspect of the invention provides the preparation method of above-mentioned TRIP steel, including following process：Melting, cast, forging, guarantor
Temperature, hot rolling, batch, pickling, cold rolling, annealing, it is characterised in that
The annealing, including three phases：
(1) under protective atmosphere, 900~950 DEG C are heated to, is incubated 1~3min；
(2) 600~650 DEG C are down to 20~30 DEG C/s cooling rate；
(3) 460 ± 5 DEG C are down to 1~10 DEG C/s, are incubated 1~10min, most after-blow protective gas, are cooled to room temperature.
Preferably, described protective atmosphere is hydrogen nitrogen mixed gas, and hydrogen proportion is 20%, hydrogen 80%.
Tensile strength >=780MPa of TRIP steel prepared by the present invention, elongation percentage >=24%, it is further preferred that described
The elongation percentage of TRIP steel is 30%, strength and ductility product 25GPa%.
Compared with prior art, economical high-aluminum low-silicon TRIP steel of automobile using of the invention and preparation method thereof, have with
Lower feature and advantage：
1. alloying component is few used in, and cost is relatively low, and steel recovery utilization rate is higher.
2.Al and Cu is relatively easy to the alloying element for obtaining and being easily recycled, can be with by adding two kinds of alloying elements
TRIP steel is set to obtain excellent combination property.
3. substituting the Si in TRIP steel with Al parts, phase transition temperature is improved, expands two-phase section annealing range, improves steel
Plate surface quality and elongation percentage, strengthen the zinc-plated performance of cold-rolled steel.Add a certain amount of Cu simultaneously, by its stronger solid solution and
Precipitation strength, crystal grain thinning, reductions of the Al to armor plate strength is made up, lift the tensile strength of TRIP steel.
4. Technology for Heating Processing is incubated using two-phase section annealing and Bainite Region, in two-phase section annealing process, cementite decomposes,
Carbon is assembled into the austenite of formation, while in bainite constant temperature process, is not readily dissolved in the elements such as silicon, the aluminium of cementite
The content of effect, carbon and manganese is further assembled into austenite so that the austenite ultimately formed has enough stability, room temperature
The retained austenite of lower acquisition is more.
5. obtaining tensile strength is more than 780MPa, elongation percentage is more than 25%, and highest elongation percentage reaches 30%, plate shape, surface
The second best in quality cold-reduced sheet.
6. Bainite Region temperature more than 460 DEG C, can coordinate zincincation, realize that annealing-plating is zinc integrated, produce vapour
Automobile-used high-strength galvanizing plate
Brief description of the drawings
The width of accompanying drawing 4 of the present invention,
Fig. 1 is rolling and the Technology for Heating Processing flow of the economical high-aluminum low-silicon TRIP steel of automobile using of the present invention；
Fig. 2 is the tensile stress strain curve of embodiment 1；
Fig. 3 is the tensile stress strain curve of embodiment 2；
Fig. 4 is the tensile stress strain curve of embodiment 3.
Embodiment
In order that those skilled in the art more fully understand the present invention program, it is right with reference to the accompanying drawings and detailed description
The present invention is further described in detail.
Fig. 1 is rolling and the Technology for Heating Processing flow of the economical high-aluminum low-silicon TRIP steel of automobile using provided by the present invention
A kind of embodiment.
1st, forging ingot is first heated to 1200 DEG C of 1~2h of insulation, is down to 1050 ± 50 DEG C of beginning hot rollings in atmosphere.Control is every
Percentage pass reduction is 30%~35%, altogether using 5 passes, ensures finishing temperature at 750~800 DEG C, and temperature is down to 500~
550 DEG C are batched.
2nd, pickling after the hot rolling slab trimming batched is removed into oxide on surface again, carries out cold rolling, cold roling reduction control
60~80%.
3rd, anneal
(1) due to adding a certain amount of Al in steel, therefore heat treatment experiment will be in protective atmosphere (if using cold-reduced sheet heat
Processing-zinc-plated integral process, then protective atmosphere is with hydrogen nitrogen mixed gas) under carry out, prevent decarburization.
(2) under certain protective atmosphere, cold-reduced sheet is heated to 900~950 DEG C, is incubated 1~3min, is carried out in two-phase section
Austenite richness carbon and Fu Meng.
(3) 600~650 DEG C are down to 20~30 DEG C/s cooling rate, Cu is constantly separated out in this process, analysed
Go out to strengthen.460 ± 5 DEG C are down to 1~10 DEG C/s again, is then incubated 1~10min, 460 are in the Bainite Region of this steel, hair
Raw bainitic transformation, as hard phase last in steel, increase the intensity of steel.Finally air blowing (protective gas) is cooled to room temperature.
In a kind of embodiment, the forging ingot of the rolling of above-mentioned TRIP steel and Technology for Heating Processing selection is in vacuum sense
To answer and melting is carried out in stove, ingot casting is poured into a mould to obtain at 1600~1700 DEG C, gained ingot casting is heated into 1100~1200 DEG C is forged,
The rectangle forging ingot of the certain size of acquisition.
Following non-limiting examples can make one of ordinary skill in the art be more fully understood the present invention, but not with
Any mode limits the present invention.
Embodiment 1
The present embodiment is stocked up by composition design proportioning, is actually obtained in 1600 DEG C of Quick pourings after melting in vaccum sensitive stove
The mass percent of steel product ingredient is：C：0.19%, Si：0.36%, Al：1.59%, Mn：1.57%, Cu：0.37%, P：
0.004%, S：0.0029%, surplus Fe, ingot casting is then heated to 1100 DEG C and is forged into the thick rectangular blocks of 60mm.By rectangle
Bloom is heated to 1200 DEG C of insulation 2h, is air-cooled to 1050 DEG C of beginning hot rollings, finishing temperature is measured when 6mm thickness is rolled to as 780 DEG C,
Batched when being then air-cooled to 550 DEG C.Cold rolling will be carried out after cold-reduced sheet pickling, for control drafts 70%, it is 1.6mm to obtain thickness
Cold-reduced sheet.
Next by the cold-reduced sheet after trimming in the H that hydrogen volume fraction is 5%2+N2Annealed in mixed atmosphere.First
Cold-reduced sheet is heated to 930 DEG C, 60s is incubated, is then cooled to 650 DEG C with 30 DEG C/s speed, then with 5 DEG C/s speed slow cooling extremely
450 DEG C, it is incubated 180s after-blow air cooling room temperatures.Gained TRIP surface of steel plate is smooth, and oxide is less, does not observe obvious Mn
With Si oxide.Standard tensile test is carried out to steel plate according to ASTM international standards, obtains stress-strain diagram such as Fig. 2 institutes
Show, tensile strength is 790 ± 5MPa, elongation percentage 32.2%, and strength and ductility product is more than 25GPa%.
Embodiment 2
The present embodiment is stocked up by composition design proportioning, is actually obtained in 1620 DEG C of Quick pourings after melting in vaccum sensitive stove
The mass percent of steel product ingredient is：C：0.22%, Si：0.43%, Al：1.61%, Mn：1.86%, Cu：0.42%, P：
0.0072%, S：0.0074%, surplus Fe, ingot casting is then heated to 1100 DEG C and is forged into the thick rectangular blocks of 60mm.By square
Shape bloom is heated to 1200 DEG C of insulation 1.5h, is air-cooled to 1100 DEG C of beginning hot rollings, and measuring finishing temperature when 6.2mm thickness is rolled to is
800 DEG C, batched when being then air-cooled to 560 DEG C.Cold rolling will be carried out after cold-reduced sheet pickling, control drafts obtains thickness 70%
For 1.7mm cold-reduced sheet.
Next by the cold-reduced sheet after trimming in the H that hydrogen volume fraction is 5%2+N2Annealed in mixed atmosphere.First
Cold-reduced sheet is heated to 950 DEG C, 60s is incubated, is cooled to 650 DEG C with 30 DEG C/s speed, then with 5 DEG C/s speed slow cooling to 460
DEG C, it is incubated 180s after-blow air cooling room temperatures.Gained TRIP surface of steel plate is smooth, and oxide layer is relatively thin.According to ASTM international standards pair
Steel plate carries out standard tensile test, obtains stress-strain diagram as shown in figure 3, tensile strength is 782 ± 2MPa, elongation percentage is
30%, strength and ductility product is about 23.2GPa%.
Embodiment 3
The present embodiment is stocked up by composition design proportioning, is actually obtained in 1650 DEG C of Quick pourings after melting in vaccum sensitive stove
The mass percent of steel product ingredient is：C：0.23%, Si：0.43%, Al：1.72%, Mn：1.87%, Cu：0.56%, P：
0.0064%, S：0.0062%, surplus Fe, ingot casting is then heated to 1100 DEG C and is forged into the thick rectangular blocks of 60mm.By square
Shape bloom is heated to 1200 DEG C of insulation 1.5h, is air-cooled to 1030 DEG C of beginning hot rollings, and measuring finishing temperature when 6mm thickness is rolled to is
770 DEG C, batched when being then air-cooled to 530 DEG C.Cold rolling will be carried out after cold-reduced sheet pickling, control drafts obtains thickness 70%
For 1.6mm cold-reduced sheet.
Next by the cold-reduced sheet after trimming in the H that hydrogen volume fraction is 5%2+N2Annealed in mixed atmosphere.First
Cold-reduced sheet is heated to 930 DEG C, 60s is incubated, is cooled to 650 DEG C with 30 DEG C/s speed, then with 5 DEG C/s speed slow cooling to 460
DEG C, it is incubated 180s after-blow air cooling room temperatures.Gained TRIP surface of steel plate is smooth, and oxide layer is relatively thin.According to ASTM international standards pair
Steel plate carries out standard tensile test, obtains stress-strain diagram as shown in figure 4, tensile strength is 820 ± 3MPa, elongation percentage is
29%, strength and ductility product is about 23.8GPa%.
Claims (5)
1. a kind of TRIP steel, it is characterised in that the mass percent of the TRIP composition of steel is：C：0.15~0.25%, Si：
0.1~0.5%, Al：1.5~3.0%, Mn：1.5~2.5%, Cu：0.1~1.0%, P<0.01%, S<0.005%, surplus
For Fe.
2. the preparation method of TRIP steel described in claim 1, including following process：Melting, cast, forging, insulation, hot rolling, volume
Take, pickling, cold rolling, annealing, it is characterised in that
The annealing, including three phases：
(1) under protective atmosphere, 900~950 DEG C are heated to, is incubated 1~3min；
(2) 600~650 DEG C are down to 20~30 DEG C/s cooling rate；
(3) 460 ± 5 DEG C are down to 1~10 DEG C/s, are incubated 1~10min, most after-blow protective gas, are cooled to room temperature.
3. preparation method according to claim 2, it is characterised in that described protective atmosphere is hydrogen-nitrogen mixture gas, its
Middle hydrogen proportion is 20%, nitrogen 80%.
4. the TRIP steel that preparation method described in claim 2 obtains, it is characterised in that the tensile strength of the TRIP steel >=
780MPa, elongation percentage >=24%.
5. TRIP steel according to claim 4, it is characterised in that the elongation percentage of the TRIP steel is 30%, and strength and ductility product is
25GPa%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711078318.1A CN107815593B (en) | 2017-11-06 | 2017-11-06 | A kind of economical high-aluminum low-silicon TRIP steel of automobile and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711078318.1A CN107815593B (en) | 2017-11-06 | 2017-11-06 | A kind of economical high-aluminum low-silicon TRIP steel of automobile and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107815593A true CN107815593A (en) | 2018-03-20 |
| CN107815593B CN107815593B (en) | 2019-01-22 |
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| CN201711078318.1A Expired - Fee Related CN107815593B (en) | 2017-11-06 | 2017-11-06 | A kind of economical high-aluminum low-silicon TRIP steel of automobile and preparation method thereof |
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011241474A (en) * | 2010-04-20 | 2011-12-01 | Kobe Steel Ltd | Method of producing high strength cold rolled steel sheet excellent in ductility |
| CN103249847A (en) * | 2010-11-10 | 2013-08-14 | Posco公司 | Method for manufacturing high-strength cold-rolled/hot-rolled trip steel having a tensile strength of 590 mpa grade, superior workability, and low mechanical-property deviation |
| CN106868399A (en) * | 2017-03-08 | 2017-06-20 | 东北大学 | A kind of two-phase TRIP steel strips and preparation method thereof |
| WO2017103516A1 (en) * | 2015-12-16 | 2017-06-22 | Compagnie Generale Des Etablissements Michelin | Carbon steel strip, use thereof for reinforcing rubber articles |
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2017
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011241474A (en) * | 2010-04-20 | 2011-12-01 | Kobe Steel Ltd | Method of producing high strength cold rolled steel sheet excellent in ductility |
| CN103249847A (en) * | 2010-11-10 | 2013-08-14 | Posco公司 | Method for manufacturing high-strength cold-rolled/hot-rolled trip steel having a tensile strength of 590 mpa grade, superior workability, and low mechanical-property deviation |
| WO2017103516A1 (en) * | 2015-12-16 | 2017-06-22 | Compagnie Generale Des Etablissements Michelin | Carbon steel strip, use thereof for reinforcing rubber articles |
| CN106868399A (en) * | 2017-03-08 | 2017-06-20 | 东北大学 | A kind of two-phase TRIP steel strips and preparation method thereof |
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