CN106435380A - Microalloyed high-aluminum high-ductility steel plate and manufacturing method thereof - Google Patents
Microalloyed high-aluminum high-ductility steel plate and manufacturing method thereof Download PDFInfo
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- CN106435380A CN106435380A CN201610946306.5A CN201610946306A CN106435380A CN 106435380 A CN106435380 A CN 106435380A CN 201610946306 A CN201610946306 A CN 201610946306A CN 106435380 A CN106435380 A CN 106435380A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 98
- 239000010959 steel Substances 0.000 title claims abstract description 98
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 13
- 238000004519 manufacturing process Methods 0.000 title abstract description 7
- 238000011282 treatment Methods 0.000 claims abstract description 29
- 238000005098 hot rolling Methods 0.000 claims abstract description 22
- 238000005266 casting Methods 0.000 claims abstract description 20
- 238000000137 annealing Methods 0.000 claims abstract description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 13
- 238000003723 Smelting Methods 0.000 claims abstract description 10
- 239000000126 substance Substances 0.000 claims abstract description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 9
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 23
- 238000005097 cold rolling Methods 0.000 claims description 20
- 238000005242 forging Methods 0.000 claims description 20
- 239000000243 solution Substances 0.000 claims description 20
- 238000002360 preparation method Methods 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 14
- 230000014759 maintenance of location Effects 0.000 claims description 14
- 229910052720 vanadium Inorganic materials 0.000 claims description 14
- 229910052758 niobium Inorganic materials 0.000 claims description 12
- 238000010791 quenching Methods 0.000 claims description 12
- 229910052719 titanium Inorganic materials 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims description 8
- 230000000171 quenching effect Effects 0.000 claims description 7
- 238000009825 accumulation Methods 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 6
- 238000005406 washing Methods 0.000 claims description 6
- 239000006104 solid solution Substances 0.000 claims description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 2
- 238000000265 homogenisation Methods 0.000 claims description 2
- 239000007787 solid Substances 0.000 claims description 2
- 239000002994 raw material Substances 0.000 abstract description 9
- 239000000463 material Substances 0.000 abstract description 8
- 238000001816 cooling Methods 0.000 abstract description 6
- 229910000851 Alloy steel Inorganic materials 0.000 abstract description 2
- 239000010960 cold rolled steel Substances 0.000 abstract 1
- 230000006835 compression Effects 0.000 abstract 1
- 238000007906 compression Methods 0.000 abstract 1
- 238000004321 preservation Methods 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 238000002844 melting Methods 0.000 description 9
- 230000008018 melting Effects 0.000 description 9
- 239000011572 manganese Substances 0.000 description 8
- 238000000034 method Methods 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 238000009413 insulation Methods 0.000 description 5
- 230000001186 cumulative effect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000006698 induction Effects 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 239000011573 trace mineral Substances 0.000 description 4
- 235000013619 trace mineral Nutrition 0.000 description 4
- 238000011161 development Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000001228 spectrum Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 208000016261 weight loss Diseases 0.000 description 2
- 230000004580 weight loss Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000000969 carrier Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 208000020442 loss of weight Diseases 0.000 description 1
- 239000011785 micronutrient Substances 0.000 description 1
- 235000013369 micronutrients Nutrition 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910017464 nitrogen compound Inorganic materials 0.000 description 1
- 150000002830 nitrogen compounds Chemical class 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000007704 transition Effects 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/12—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
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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 relates to a microalloyed high-aluminum high-ductility steel plate and a manufacturing method thereof, and belongs to the field of alloy steel. The steel plate comprises the chemical components, by mass, including 0.8%-1.0% of C, 28%-30% of Mn, 8.0%-10% of Al, 0.02%-0.10% of Nb, 0.02%-0.10% of V, 0.02%-0.10% of Ti, 0.02%-0.08% of N, 0-0.003% of P, 0-0.003% of S and the balance Fe and inevitable impurities. The manufacturing method comprises the steps that firstly, raw materials are prepared according to the chemical components, then a plate billet is forged after smelting and casting, the plate billet is heated, homogenized and subjected to multi-pass hot rolling deformation with the accumulative deformation rate being 85%-90%, water cooling after rolling is conducted, and then the plate billet is air-cooled to the room temperature; secondly, the hot-rolled steel plate is subjected to solution treatment, fast heated to a solution treatment temperature for heat preservation for a period of time, and then water-quenched to the room temperature; thirdly, the steel plate subjected to the solution treatment is pickled, cold-rolled and subjected to multi-pass rolling deformation with the accumulative compression amount being 65%-80%; and fourthly, the cold-rolled steel plate is subjected to final annealing treatment, and then water-quenched to the room temperature, so that the microalloyed high-aluminum high-ductility steel plate is obtained. According to the steel plate manufactured through the manufacturing method, the strength and ductility product can reach 50 GPa*%, and the impact and collision resistance of the material is obviously improved.
Description
Technical field
The invention belongs to field of alloy steel, more particularly to a kind of microalloying high alumina high-ductility steel plate and preparation method thereof.
Background technology
With the high speed development of auto industry and the continuous improvement of mankind's environmental protection and awareness of saving energy, automobile metal material
Just towards energy-conservation and the big main target development of safety two.For this purpose, on the one hand the specific strength of metal material should be improved so as to reduce
Tare, reduces oil consumption, has not only been beneficial to energy saving but also can mitigate ambient pressure；On the other hand touching for metal material should be improved
Absorbability is hit, most of energy of collision is converted into the plastic deformation of the reasonable part material of vehicle body so that human pilot
Safety is protected.
Chinese invention patent CN103667883A discloses a kind of low-density, high tough automotive sheet and preparation technology,
It is characterized in that：Its composition and mass fraction are consisted of：C：0.60%~0.70%、Si：0.30%~0.40%、Mn：10.0%~
15.0%、Al：5.0%~10.0%、P<0.005%、S<0.003%, balance of Fe and inevitable impurity.The steel grade tensile strength is
905MPa, it is 38% that elongation after fracture is 42%, strength and ductility product, and low cross-intensity does not reach the requirement of unimach.Middle promulgated by the State Council
Bright patent CN104694816A discloses a kind of preparation method of strength and ductility product more than the high Al medium managese steel of 30GPa %, and its feature exists
In：Its composition and mass fraction are consisted of：0.10%~0.35%C、5.0%~9.0%Mn、4.0%~7.5%Al、P<0.003%、S
<0.002%, balance of Fe and inevitable impurity.The elongation after fracture of this steel is pretty good, reaches 45% or so, but its tension
Intensity is somewhat low, and comprehensive mechanical property is not very excellent, all in 800MPa or so, possibly cannot meet some automobiles to superelevation
The requirement of strength steel.
Content of the invention
It is an object of the invention to provide a kind of microalloying high alumina high-ductility steel plate, the chemical composition of the steel plate and matter
Measuring percentage ratio is：C：0.8% ~ 1.0%, Mn：28% ~ 30%, Al：8.0% ~ 10%, Nb：0.02~0.10%、V：0.02~
0.10%、Ti：0.02~0.10%、N：0.02~0.08%、P<0.003%th, S<0.003%, balance of Fe and inevitable impurity.
Another object of the present invention is to providing the preparation method of the microalloying high alumina high-ductility steel plate, specifically include
Following steps：
（1）Slab is forged into after smelting, casting；
（2）Hot rolling：By heating of plate blank, after Homogenization Treatments, carry out multistage hot deformation deformation, accumulative deflection 85% ~ 90%,
Rear water-cooled is rolled, is air cooled to room temperature；
（3）Solution treatment：Steel plate after hot rolling is carried out solution treatment, a period of time is incubated using solid solubility temperature is heated rapidly to
Water quenching is to room temperature afterwards；
（4）Cold rolling：To carry out cold rolling after steel plate acid-washing after solution treatment, deform through multi- pass rolling, accumulation decrement is
65%~80%；
（5）Annealing：Steel plate after will be cold rolling carries out final annealing, and water quenching afterwards to room temperature obtains microalloying height
Aluminum high-ductility steel plate.
Preferably, step of the present invention（2）Billet heating temperature is 1150 ~ 1200 DEG C, 1 ~ 2h of temperature retention time, start rolling temperature
1100 ~ 1150 DEG C, 850 ~ 900 DEG C of finishing temperature, 400 ~ 500 DEG C of coiling temperature.
Preferably, step of the present invention（3）Steel billet solid solution temperature is 950 ~ 1100 DEG C, and temperature retention time is 0.5 ~ 2h.
Preferably, step of the present invention（5）It is 15 ~ 30min that annealing temperature is 900 ~ 1050 DEG C, temperature retention time.
Preferably, step（1）Ingot casting heating-up temperature is 1170 ~ 1200 DEG C, 1 ~ 2h of temperature retention time, starting forging temperature 1100 ~
1200 DEG C, 800 ~ 900 DEG C of final forging temperature；Under this temperature conditions, iron and steel performance is best.Steel plate after casting is due to contracting
The defective effect mechanical property of steel plate such as hole, shrinkage porosite, therefore will forge to which, eliminate the defects such as shrinkage cavity and porosity, improve material
Mechanical property.
The present invention is 1150 ~ 1200 DEG C, 1 ~ 2h of temperature retention time in steel billet of hot rolling when being heated temperature, start rolling temperature 1100 ~ 1150
DEG C, 850 ~ 900 DEG C of finishing temperature, 400 ~ 500 DEG C of coiling temperature, under this temperature conditions, iron and steel performance is best.Due to finally will
Steel plate is obtained, thickness is smaller, so rolling deformation will be carried out to obtain using size and the bright and clean table of acquisition needed for us to which
Face, rolling is divided into hot rolling and cold rolling two parts, and temperature is higher, the intensity decreases of material, and plasticity is raised, i.e. resistance capacity to deformation
Reduce, the roll-force of roll mill required to reduce, so first carry out hot rolling deformation to which, finally which is carried out cold roller and deformed, by
In processing hardening, the steel plate of high intensity can be obtained, afterwards which is made annealing treatment, that is, obtain the high-ductility steel required for us
Plate.
The steel billet solid solution temperature is 950 ~ 1100 DEG C, and temperature retention time is 0.5 ~ 2h.Steel after hot rolling deformation
Plate has alloy carbide to separate out in thermal deformation and cooling procedure, is unfavorable for following process, therefore, which need to be carried out at solid solution
Reason, makes the various phases in alloy and carbide fully dissolve, and eliminates stress and softening, improves plasticity and the toughness of alloy, with
Just following process or molding.
The annealing billet treatment temperature is 900 ~ 1050 DEG C, and temperature retention time is 15 ~ 30min.Cold rolling after annealing
Steel plate, deformation crystal grain is again after recrystallization, more uniformly tiny, and steel plate elongation after fracture substantially increases, and eliminates material
Each diversity, the comprehensive mechanical property of material（Strength and ductility product）More excellent.
The present invention adds Nb, V, Ti microalloy element to be strengthened to high manganese high alumina high-carbon steel grade, is significantly improving surrender
While intensity and tensile strength, it is ensured that elongation after fracture reduces by a small margin or do not reduce, to ensure the resultant force of steel plate
Learn performance greatly to improve, meet the demand of the automobile with ultrahigh-strength high-plasticity steel plate of contemporary high speed development.
The present invention has advantages below：
（1）Relatively low to equipment requirements：The present invention using conventional equipment of hot rolling can, meet working condition.Slab heating temperature
Low, energy saving；Finishing temperature is higher, and required roll-force is relatively low, also can reducing energy consumption.
（2）Mechanical property of steel plate is good：The steel plate of present invention production has excellent comprehensive mechanical property（High intensity, high-ductility
Property）, after present invention annealing, steel plate has the good combination of intensity and plasticity, with good impact absorption performance.
（3）Weight loss effect is obvious：The automobile structural steels such as DP steel, TRIP steel are compared, the present invention adopts rational alloy
Element proportioning, with the addition of the lightweight element such as Al, on the basis of the excellent mechanical property of steel plate is ensured, reduce steel plate density, loss of weight
Effect is obvious.
（4）Have a extensive future：High alumina high-ductility steel plate of the present invention meets the requirement of the advanced high-strength steel of the third generation,
It is the required new material of current automobile industry, the material of preparation extensively can also be answered except can be used for auto manufacturing
For industries such as petroleum pipeline, railway traffic, engineering machinery, aircraft carriers.
The present invention carries out refined crystalline strengthening by Nb, V, Ti microalloying to which, and precipitation strength is improving its intensity and mould
Property reduce and do not reduce substantially or the stable height with excellent toughness and fabulous anticollision performance of final availability
Flexible steel plate；Which has the tensile strength of 1100 ~ 1250MPa, 40 ~ 50% elongation percentage, and strength and ductility product is up to 50GPa % or so；
Its density is 6.7 ~ 7.0 g/cm3, weight loss effect is up to 11% ~ 15%.
Description of the drawings
Fig. 1 is the process chart of the present invention.
Fig. 2 is the high alumina high-ductility steel plate heat processing technique schematic diagram of the present invention.
Fig. 3 is the steel plate sample XRD spectrum in the present invention after 1 solution treatment of example.
Fig. 4 is the stretching fracture pattern of 1 steel plate of example in the present invention.
Specific embodiment
With reference to the accompanying drawings and detailed description, the invention will be further described, but protection scope of the present invention is simultaneously
It is not limited to the content.
Embodiment 1
Described in the present embodiment, the chemical composition of microalloying high alumina high-ductility steel plate and mass percent are：C：0.88%、Mn：
28.8%、Al：8.5%、Nb：0.045%、V：0.05%、Ti：0.05%、N：0.06%、P<0.003%th, S<0.003%, balance of Fe
And inevitable impurity.
Described in the present embodiment, the preparation method of microalloying high alumina high-ductility steel plate, specifically includes following steps：
（1）Slab is forged into after smelting, casting：The melting in vacuum induction melting furnace by the raw material for preparing, smelting temperature exists
1650 DEG C, and ingot casting is poured into, ingot casting being carried out forging deformation, slab is finally swaged into, cumulative deformation is 70%, air cooling after forging
To room temperature, wherein, ingot casting heating-up temperature is 1180 DEG C, temperature retention time 1.5h, 1150 DEG C of starting forging temperature, 850 DEG C of final forging temperature.
（2）Hot rolling：By heating of plate blank to 1200 DEG C, 2h is incubated, hot rolled thickness is that 4mm, hot rolling start rolling temperature is 1150 DEG C,
Finishing temperature is 870 DEG C, carries out 6 passes, and coiling temperature is 400 DEG C, to roll rear water-cooled, be air cooled to room temperature；Accumulative deflection
85%.
（3）Solution treatment：Steel plate after hot rolling is carried out solution treatment, water after 1h is incubated using being heated rapidly to 1000 DEG C
Quench to room temperature.
（4）Cold rolling：To carry out after steel plate acid-washing after solution treatment cold rolling, through 8 passes deform, accumulation decrement
For 70%；
（5）Annealing：Steel plate after will be cold rolling is heated to 1000 DEG C, and insulation 30min carries out final annealing, Zhi Houshui
Quench to room temperature and microalloying high alumina high-ductility steel plate is obtained, according to GB, its mechanical property is tested to the steel plate after finished heat treatment
Can, its tensile strength 850MPa, elongation percentage 45%, strength and ductility product is up to 38.3GPa %.
The present embodiment step（3）The steel plate sample XRD spectrum for preparing is as shown in figure 3, test steel as seen from the figure
Plate is single austenite structure, i.e. sample under forging state and different temperatures solution treatment not to be had in this heat treatment process
Undergo phase transition.The stretching fracture shape appearance figure of steel plate as shown in figure 4, as seen from the figure fracture surface of sample microscopic appearance present many
Tiny, etc. shaft-like dimple structure, the dimple of fracture is very deep, illustrates that the plasticity of this sample is fine.
Embodiment 2
Described in the present embodiment, the chemical composition of microalloying high alumina high-ductility steel plate and mass percent are：C：0.8%th, Mn：
30%th, Al：9%th, Nb：0.02%、V：0.10%、Ti：0.10%、N：0.02%、P<0.003%th, S<0.003%, balance of Fe and
Inevitable impurity.
Described in the present embodiment, the preparation method of microalloying high alumina high-ductility steel plate, specifically includes following steps：
（1）Slab is forged into after smelting, casting：The melting in vacuum induction melting furnace by the raw material for preparing, smelting temperature exists
1650 DEG C, and ingot casting is poured into, ingot casting being carried out forging deformation, slab is finally swaged into, cumulative deformation is 75%, air cooling after forging
To room temperature, wherein, ingot casting heating-up temperature is 1200 DEG C, temperature retention time 2h, 1100 DEG C of starting forging temperature, 800 ~ 900 DEG C of final forging temperature.
（2）Hot rolling：By heating of plate blank to 1200 DEG C, 2h is incubated, hot rolled thickness is that 4mm, hot rolling start rolling temperature is 1100 DEG C,
Finishing temperature is 850 DEG C, carries out 8 passes, and coiling temperature is 450 DEG C, to roll rear water-cooled, be air cooled to room temperature；Accumulative deflection
87%.
（3）Solution treatment：Steel plate after hot rolling is carried out solution treatment, is incubated after 0.5h using being heated rapidly to 950 DEG C
Water quenching is to room temperature.
（4）Cold rolling：To carry out after steel plate acid-washing after solution treatment cold rolling, through 6 passes deform, accumulation decrement
For 65%；
（5）Annealing：Steel plate after will be cold rolling is heated to 900 DEG C, and insulation 20min carries out final annealing, Zhi Houshui
Quench to room temperature and microalloying high alumina high-ductility steel plate is obtained, according to GB, its mechanical property is tested to the steel plate after finished heat treatment
Can, its tensile strength 1100MPa, elongation percentage 45%, strength and ductility product is up to 49.5GPa %.
Embodiment 3
Described in the present embodiment, the chemical composition of microalloying high alumina high-ductility steel plate and mass percent are：C：1.0%th, Mn：
28%th, Al：10%th, Nb：0.10%、V：0.02%、Ti：0.02%、N：0.08%、P<0.003%th, S<0.003%, balance of Fe and
Inevitable impurity.
Described in the present embodiment, the preparation method of microalloying high alumina high-ductility steel plate, specifically includes following steps：
（1）Slab is forged into after smelting, casting：The melting in vacuum induction melting furnace by the raw material for preparing, smelting temperature exists
1650 DEG C, and ingot casting is poured into, ingot casting being carried out forging deformation, slab is finally swaged into, cumulative deformation is 80%, air cooling after forging
To room temperature, wherein, ingot casting heating-up temperature is 1170 DEG C, temperature retention time 1h, 1200 DEG C of starting forging temperature, 800 DEG C of final forging temperature.
（2）Hot rolling：By heating of plate blank to 1200 DEG C, 2h is incubated, hot rolled thickness is that 4mm, hot rolling start rolling temperature is 1150 DEG C,
Finishing temperature is 900 DEG C, carries out 8 passes, and coiling temperature is 500 DEG C, to roll rear water-cooled, be air cooled to room temperature；Accumulative deflection
90%.
（3）Solution treatment：Steel plate after hot rolling is carried out solution treatment, is incubated after 2h using being heated rapidly to 1100 DEG C
Water quenching is to room temperature.
（4）Cold rolling：To carry out after steel plate acid-washing after solution treatment cold rolling, through 8 passes deform, accumulation decrement
For 80%；
（5）Annealing：Steel plate after will be cold rolling is heated to 1050 DEG C, and insulation 15min carries out final annealing, Zhi Houshui
Quench to room temperature and microalloying high alumina high-ductility steel plate is obtained, according to GB, its mechanical property is tested to the steel plate after finished heat treatment
Can, its tensile strength 1080MPa, elongation percentage 45%, strength and ductility product is up to 48.6GPa %.
Comparative example 1
The preparation technology of the high alumina high-ductility steel plate, which comprises the following steps that：
（1）Dispensing：Using raw material based on ingot iron, it is 99.85% with electrolytic manganese metal and purity that purity is 99.9%
Rafifinal is alloy raw material, prepares chemical constituent by mass fraction (wt%) and is：C：0.88%、Mn：28.8%、Al：8.5%、N：
0.06%、P<0.003%th, S<0.003%, balance of Fe and inevitable impurity.
（2）Melting：The melting in vacuum induction melting furnace by the raw material for preparing, smelting temperature is at 1650 DEG C, and pours into a mould
Become ingot casting.
（3）Forging：Casting ingot is carried out forging deformation, is finally swaged into slab, cumulative deformation 70%, air cooling after forging
To room temperature.
（4）Hot rolling：By heating steel billet to 1200 DEG C, 2h is incubated, according to experimental mill ability, design hot rolled thickness is 4mm,
Hot rolling start rolling temperature is 1150 DEG C, and finishing temperature is 870 DEG C, to carry out 6 passes, set coiling temperature as 400 ~ 500 DEG C, empty
It is cooled to room temperature；
（5）Solution treatment：Steel plate after hot rolling is carried out solution treatment, steel plate is heated rapidly to 1000 DEG C, water after insulation 1h
Quench to room temperature.
（6）Cold rolling：To carry out cold rolling after steel plate acid-washing after solution treatment, according to mill capacity, become through 8 passes
Shape, accumulation decrement is 70%.
（7）Annealing：Steel plate after will be cold rolling carries out final annealing, and steel plate is heated to 1000 DEG C, insulation
After 0.5h, water quenching tests its mechanical property to the steel plate after finished heat treatment according to GB to room temperature, its tensile strength 850MPa,
Elongation percentage 45%, strength and ductility product is up to 38.3GPa %.
Comparative example 2
It is with the difference of comparative example 1, Nb trace element in the chemical composition of raw material, is with the addition of, Nb content is 0.045%,
According to GB, its mechanical property is tested to the steel plate after annealing, its tensile strength 950MPa, elongation percentage 47%, strength and ductility product height
Reach 44.7GPa %.
Comparative example 3
It is with the difference of comparative example 1, Nb, V trace element in the chemical composition of raw material, is with the addition of, its content is：Nb：
0.045%、V：0.05%, according to GB, its mechanical property is tested to the steel plate after finished heat treatment, its tensile strength 1050MPa,
Elongation percentage 44%, strength and ductility product is up to 46.2GPa %.
Table 1 is the mechanical property of the embodiment of the present invention
From table 1, the steel plate of Nb, V, Ti trace element is individually added into, its intensity has appropriate raising, plasticity also somewhat has
Improved, effect of the individual element in steel has its limitation, and steel after tri- kinds of trace element of Nb, V, Ti are simultaneously introduced
Plate, intensity and plasticity are all greatly improved, and as shown in one embodiment 1 of table, when micronutrient levelss are：Nb：
0.045%、V：0.05%、Ti：When 0.05%, the comprehensive mechanical property of steel plate is best, i.e. the value maximum of strength and ductility product；This is because micro-
Secondary element suppresses the Deformation recrystallization of austenite in hot procedure and prevents growing up for its crystal grain；Two is the carbon by them
The precipitation of nitrogen compound, plays the precipitation enhancement of Nb, V, Ti；And combined microalloying takes full advantage of Nb, V, Ti phase
Reciprocal action between mutually, has been effectively saved resource, has greatly reduced the production cost of high-strength steel.
The preferred embodiments of the present invention are the foregoing is only, the present invention is not limited to, in the common skill in this area
In the ken that art personnel possess, can also be variously modified on the premise of without departing from present inventive concept, here no
Method is exhaustive to all of embodiment, every belongs to obvious variation that technical scheme amplified out still
Row in protection scope of the present invention.
Claims (6)
1. a kind of microalloying high alumina high-ductility steel plate, it is characterised in that：The chemical composition and mass percent of the steel plate be：
C：0.8% ~ 1.0%, Mn：28% ~ 30%, Al：8.0% ~ 10%, Nb：0.02~0.10%、V：0.02~0.10%、Ti：0.02~
0.10%、N：0.02~0.08%、P<0.003%th, S<0.003%, balance of Fe and inevitable impurity.
2. the preparation method of microalloying high alumina high-ductility steel plate described in claim 1, it is characterised in that specifically include following step
Suddenly：
（1）Slab is forged into after smelting, casting；
（2）Hot rolling：By heating of plate blank, after Homogenization Treatments, carry out multistage hot deformation deformation, accumulative deflection 85% ~ 90%,
Rear water-cooled is rolled, is air cooled to room temperature；
（3）Solution treatment：Steel plate after hot rolling is carried out solution treatment, a period of time is incubated using solid solubility temperature is heated rapidly to
Water quenching is to room temperature afterwards；
（4）Cold rolling：To carry out cold rolling after steel plate acid-washing after solution treatment, deform through multi- pass rolling, accumulation decrement is
65%~80%；
（5）Annealing：Steel plate after will be cold rolling carries out final annealing, and water quenching afterwards to room temperature obtains microalloying height
Aluminum high-ductility steel plate.
3. the preparation method of microalloying high alumina high-ductility steel plate according to claim 1, it is characterised in that：Step（1）Casting
Ingot heating-up temperature is 1170 ~ 1200 DEG C, 1 ~ 2h of temperature retention time, 1100 ~ 1200 DEG C of starting forging temperature, 800 ~ 900 DEG C of final forging temperature.
4. the preparation method of microalloying high alumina high-ductility steel plate according to claim 1, it is characterised in that：Step（2）Steel
Base heating-up temperature is 1150 ~ 1200 DEG C, 1 ~ 2h of temperature retention time, 1100 ~ 1150 DEG C of start rolling temperature, 850 ~ 900 DEG C of finishing temperature, volume
400 ~ 500 DEG C of Qu Wendu.
5. the preparation method of microalloying high alumina high-ductility steel plate according to claim 1, it is characterised in that：Step（3）Steel
Base solid solution temperature is 950 ~ 1100 DEG C, and temperature retention time is 0.5 ~ 2h.
6. the preparation method of microalloying high alumina high-ductility steel plate according to claim 1, it is characterised in that：Step（5）Move back
Fiery treatment temperature is 900 ~ 1050 DEG C, and temperature retention time is 15 ~ 30min.
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| CN107058854A (en) * | 2017-03-13 | 2017-08-18 | 昆明理工大学 | A kind of vacuum smelting method of the high manganese high-aluminum steel of Nb, V, Ti microalloying |
| CN107217204A (en) * | 2017-05-02 | 2017-09-29 | 昆明理工大学 | A kind of preparation method of Fe Mn Al systems alloy |
| CN107641763A (en) * | 2017-09-29 | 2018-01-30 | 安徽工业大学工商学院 | A kind of low-density potassium steel of high strength and ductility |
| CN107674955A (en) * | 2017-09-29 | 2018-02-09 | 安徽工业大学工商学院 | A kind of preparation method of low density steel of the strength and ductility product more than 50GPa% |
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| CN107058854A (en) * | 2017-03-13 | 2017-08-18 | 昆明理工大学 | A kind of vacuum smelting method of the high manganese high-aluminum steel of Nb, V, Ti microalloying |
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| CN113088828A (en) * | 2021-03-25 | 2021-07-09 | 江苏省沙钢钢铁研究院有限公司 | high-Mn high-Al steel and vacuum melting process thereof |
| CN114774806A (en) * | 2022-04-25 | 2022-07-22 | 燕山大学 | High-strength and high-toughness light steel plate and preparation method and application thereof |
| CN115216704A (en) * | 2022-06-29 | 2022-10-21 | 张家港中美超薄带科技有限公司 | Short-process production method of low-density steel based on thin strip continuous casting |
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Application publication date: 20170222 |