CN106498278A - Low-density cut deal of a kind of high-strength high-elongation ratio and preparation method thereof - Google Patents
Low-density cut deal of a kind of high-strength high-elongation ratio and preparation method thereof Download PDFInfo
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- CN106498278A CN106498278A CN201610867065.5A CN201610867065A CN106498278A CN 106498278 A CN106498278 A CN 106498278A CN 201610867065 A CN201610867065 A CN 201610867065A CN 106498278 A CN106498278 A CN 106498278A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- Heat Treatment Of Steel (AREA)
Abstract
The invention provides low-density cut deal of a kind of high-strength high-elongation ratio and preparation method thereof.The steel chemical composition mass percent is：C：0.105 0.30%, Al：2.00 6.00%, Mn：1.50 4.00%, Ni：1.80% 3.00%, Nb：0.012 0.06%, Si：0.00 0.20%, other are Fe and inevitable impurity.The present invention recrystallizes controlled rolling using two benches, and γ austenite recrystallizations area rolling temperature is that delta ferrite recrystallization zone rolling temperature is between 930 800 DEG C, rolls rear thickness of slab for 10 20mm between 1,000 950 DEG C；High tempering process is carried out after rolling, the heterogeneous structure of delta ferrite, tempered martensite and converes instruction is obtained after air cooling, delta ferrite level is less than 50%, converes instruction content reaches more than 10%, yield strength is more than 480Mpa, tensile strength is more than 570Mpa, and elongation after fracture is more than 25%, and 20 DEG C of horizontal Charpy-V impact power is more than 42J.
Description
Technical field
The invention belongs to metal material field, more particularly to a kind of low-density cut deal of high-strength high-elongation ratio and its roll
System and Technology for Heating Processing.
Background technology
In recent years, it is to reduce fuel consumption, reduce CO2Discharge capacity, automotive light weight technology are increasingly becoming industry trend, and lightweight is closed
Gold is also increasingly paid attention to by industry therewith.The little aluminium alloy plate of density that research worker is considered as first, its price are held high
Expensive, processing, welding control difficulty are higher, it is more difficult to used as Vehicle Materials.The development and application of low density steel solve this well
Problem, adds a certain amount of aluminum on iron-based, produces high aluminium content steel plate, is allowed to have both the intensity of steel plate, plasticity and aluminium alloy
Low-density feature.The addition of aluminum can also improve the decay resistance of steel, and this low-density, corrosion resistant combination property make high alumina
Low density steel is provided with very good prospect in ocean engineering application aspect.
The prior art (such as Chinese patent, publication number CN103484771B) of High-aluminum low-density steel cut deal discloses one kind
High-aluminum low-density medium-thickness steel plate for ocean platform and its rolling and Technology for Heating Processing, it is achieved that the spy of low-density and high intensity
Levy, but and unresolved low density steel low-temperature impact toughness problem.
Plus the steel of Al elements is possible to separate out κ carbides under suitable heat treatment condition, κ carbides can become crackle
Starting point causes material plasticity to reduce, therefore low density steel usually cracking phenomenon in cold-rolled process.In addition, aluminum is had with nitrogen
Stronger affinity, easily forms AlN granules, and when casting solidification, rate of cooling is less, the easier precipitations of AlN, and cast steel is 880
DEG C quenching after, AlN granules with hexagonal crystal form along original austenite crystal boundary separate out steel can be made to become fragile.Accordingly, it is desirable to provide a kind of
High-strength high-elongation ratio low-density and the preferable cut deal material of toughness.
Content of the invention
It is an object of the invention to provide a kind of high intensity, high-elongation, low-density cut deal and preparation method thereof.Pass through
The alloying element design of high alumina, recrystallizes controlled rolling using two benches, and carrying out critical heat process experiment after rolling is tempered steel plate,
The heterogeneous structure of ferrite, tempered martensite and converes instruction is obtained after air cooling, to improve the low-temperature flexibility of steel, while tool
Standby high intensity and good decay resistance, can preferably be applied to ocean platform or automotive field.
High intensity involved in the present invention, high-elongation, low-density cut deal, its chemical composition mass percent is：
C：0.105-0.30%, Al：2.00-6.00%, Mn：1.50-4.00%, Ni：1.80%-3.00%, Nb：0.012-
0.06%, Si：≤ 0.20%, control S, P, N content for S≤0.005%, P≤0.01%, N≤0.005%, other be Fe and
Inevitable impurity, for making γ austenite contents after homogenizing is processed answer more than delta ferrite level, the wherein content of C, Mn, Ni, Al
Coincidence formula：+ 1 ＞ [Al] of 12 [C]+0.25 [Mn]+0.2 [Ni].
The chemical composition of preferred mass percent is：C：0.11-0.30%, Al：3.20-6.00%, Mn：2.40-
4.00%, Ni：1.80%-3.00%, Nb：0.012-0.055%, Si：≤ 0.20%.
The chemical composition of optimal mass percent is：C：0.18%, Al：3.24%, Mn：2.48%, Ni：1.94%,
Nb：0.053%, Si：0.19%.
For improving cut deal intensity, in above-mentioned chemical composition, can also add one or more in Mo, V, Ti, Cu element
Substitute Fe, addition by mass percentage, Mo≤0.5%, V≤0.05%, Ti≤0.08%, Cu≤1%.
The effect of each element of the present invention and proportioning are according to following (with mass percent as counting)：
Carbon：One important function of C is solution strengthening, dissolves in austenite and expands austenite phase field, and enough C can shape
Into enough rich carbon converes instructions and make it stable to room temperature, in tissue, the alloying element of solid solution such as Al, Mn, Nb can be tied with C
Conjunction forms various carbides, and the precipitation enhancement of these carbides can properly increase the intensity of steel, affect austenite and ferrum
Ferritic recrystallization temperature；But C content is too high that steel can be made to occur more twins sub-structure after quenching, reduce the plasticity of steel and tough
Property, and C content more than 0.23% when, the welding performance of material degenerates, therefore, in steel of the present invention carbon content select in 0.105-
Between 0.30%.
Aluminum：Al is ferrite former, suppresses the formation of cementite, make the Ovshinsky of reverted austenite in the assigning process of C
Body richness C, effectively improves converes instruction content and stability.Adding in steel as lightweight element to reduce ferrous materials
Density, it is also possible to play a part of solution strengthening, and improve the decay resistance of steel.But, for guaranteeing Ovshinsky during homogenizing process
Body percentage composition increases Al content, need to improve C, Mn, Ni among the austenite stabilizing elements content, material cost simultaneously more than delta ferrite
Increase, therefore, in the present invention, the content of aluminum is selected between 2.00-6.00%.
Manganese：Mn is the element for expanding austenite phase field, is conducive to the raising of the stability of austenite, increases steel grade and reverses Austria
The content of family name's body, can effectively improve the quenching degree and intensity and hardness of steel.But, Mn contents can excessively make smelting and the operation of rolling
In there is segregation (different from routine Mn segregations in steel, to be negative segregation, delta ferrite Pin Mn areas occur), grain coarsening trend increases
By force, reduce the plasticity and toughness of steel, cause welding to deteriorate.Therefore, the present invention in manganese content select 1.50-4.00% it
Between.
Nickel：Ni is among the austenite stabilizing elements, can hinder grain coarsening under high temperature.Ni can also improve the quenching degree of steel with
Corrosion resistance.Reduce toughness as the expensive and Al and Ni of Ni can generate NiAl intermetallic compounds, so nickel in the present invention
Content select between 1.80-3.00%.
Niobium：Nb can effectively improve the intensity of steel by refined crystalline strengthening and precipitation strength, and Nb can strong inhibition dynamic recrystallization
Generation.But the Nb of excess can weaken the hot-working character of steel and the toughness of steel plate.Therefore, in the present invention, the content of niobium is selected
Between 0.012-0.06%.
In addition, grain coarsening when Mo can be organized with crystal grain thinning and be suppressed hot-working, V also can crystal grain thinning tissue, improve
Thermal structure stability simultaneously improves the intensity and toughness of steel, Ti can refined cast structure and hot-working hinder grain coarsening in time.
Cu can increase the yield strength of steel and reduce ductile-brittle transition temperature, and the precipitation strength of Cu can keep the uniformity of performance,
These elements can be added during smelting as one sees fit.
A kind of manufacturing process of the low-density cut deal of high-strength high-elongation ratio involved in the present invention is as follows：
(1) smelt, forge：Smelted with vacuum induction smelting furnace, by the pig iron and various alloying elements according to above-mentioned chemistry into
Distribution ratio Hybrid Heating melts；Temperature is come out of the stove after rising to 1500-1550 DEG C cast；After Heating Steel Ingots to 1200 DEG C are incubated, in
Between 1200-1000 DEG C forging become thickness 100mm steel billet and rapid water-cooled to room temperature.
(2) rolling mill practice：Homogenization Treatments, Ran Houjin will be carried out in homogenizing treatment temperature insulation 60-180min after forging
Row two benches recrystallize controlled rolling；First stage be γ austenite recrystallizations area rolling, rolling temperature be 1000-950 DEG C it
Between, three passages of the stage point, every time reduction ratio is in 28-32%；Second stage is delta ferrite recrystallization zone rolling temperature,
Rolling temperature is that three passages of the stage point, every time reduction ratio add up in 24-28% or so, two benches between 930-800 DEG C
Reduction ratio is more than 85%；Subsequently to be cooled to room temperature more than 10 DEG C/s cooling rates, it is 10-20mm that steel plate is thick eventually.
(3) Technology for Heating Processing：The hot rolled plate temper that step (2) is obtained, temperature is Tt± 10 DEG C, Tt=
50ln[C]-1.5[Al]2- 20 [Ni]+858 of+14 [Al] -13 [Mn], unit DEG C are incubated 30-60min, and then air cooling, obtains steel
Plate.
Homogenizing treatment temperature in step (2) is Th± 10 DEG C, preferred formula Th=1220-2400 [C]2+1270
[C] -17 [Mn] -27 [Ni] -30 [Al], unit DEG C.
The step 2) Homogenization Treatments when, obtain delta ferrite and γ austenites, austenite molar percentage reaches 50%
More than.
The step 3) steel plate that obtains obtains the heterogeneous structure of ferrite, tempered martensite and converes instruction, reverses
Austenite content reaches more than 10%.
In said method, the yield strength of steel plate is more than 480Mpa, and tensile strength is more than 570Mpa, and elongation after fracture is more than
25%, -20 DEG C of Charpy-V impact power is more than 42J.
The effect of each element of the present invention and proportioning are according to following (with mass percent as counting)：
It is a feature of the present invention that the heterogeneous structure of delta ferrite, tempered martensite and converes instruction is obtained, so as to reality
The excellent properties such as high-elongation, high intensity are showed.As delta ferrite is that high temperature forms phase, crystallite dimension is more thick, through six roads
The rolling of secondary recrystallization zone, deflection ＜ 90%, still more difficult be refined to less than 20 μm, be that -20 DEG C of Charpy-V impact powers of satisfaction are higher than
42J, delta ferrite level should be less than 50%, to be this derive through thermodynamics, Thermo-Calc computed in software and experimental verification C, Al,
The content of Mn, Ni meets formula：+ 1 ＞ [Al] of 12 [C]+0.25 [Mn]+0.2 [Ni], it can be ensured that there is a certain temperature and cause γ ＞
δ, i.e., in Thermo-Calc property figures, as shown in figure 4, austenite and ferrite phase line are present intersect；And it is solderable for improving
Property, and reducing cost of alloy, C, Mn, Ni content should be as low as possible, and Homogenization Treatments temperature should be selected in the alloying component Ovshinsky
Body phase area maximum, equally shows through Thermo-Calc computed in software and experimental verification, and Homogenization Treatments preferable temperature is Th=
1220-2400[C]2+1270[C]-17[Mn]-27[Ni]-30[Al].
The content that is organized as of Homogenization Treatments is less than the γ austenitic duplex groups that 50% delta ferrite and content are more than 50%
Knit, be abundant refining grain size, using Deformation recrystallization, due to delta ferrite different with the recrystallization temperature of γ austenites, this
Invention is rolled using two-stage control：First stage be γ austenite recrystallizations area rolling, rolling temperature be 1000-950 DEG C it
Between, rolling γ austenites and delta ferrite can be recrystallized at this temperature, but delta ferrite, in this temperature range, crystal grain holds
Easily grow up rapidly, recrystallization softening DeGrain；Second stage is delta ferrite recrystallization zone rolling temperature, and rolling temperature is
Between 930-800 DEG C, recrystallize in this temperature delta ferrite, ferrite grain size is refined, γ austenites will not occur again
Crystallization, deformation accumulation promote martensite transfor mation, and after quenching, martensite lath is more tiny, so as to the martensite after being tempered and reverse
Austenite is equally comparatively fine, and austenite martensitic phase transformation area crystallite dimension greatly improves low-temperature flexibility up to less than 2 μm.
Another feature of the present invention is that two isothermal processs i.e. Homogenization Treatments are actually two units with critical heat treatment
Plain partition process.Homogenization Treatments process realizes the composition partition of delta ferrite and γ austenites, obtains delta ferrite and moles hundred
The γ austenites than reaching more than 50%, C, Mn, Ni is divided to be enriched with austenite for the first time, Al is enriched with delta ferrite.Biphase
In area's drawing process, in temperature Tt±10℃(Tt=50ln [C] -1.5 [Al]2- 20 [Ni]+858 of+14 [Al] -13 [Mn],
Unit DEG C) insulation 30-60min carries out critical heat treatment experiment, and tempered martensite realizes composition with converes instruction in the process
Partition.As C, Mn, Ni element is enriched with converes instruction, Al elements are enriched with tempered martensite, and therefore obtained returns
In fiery martensite and converes instruction, the content of C, Mn, Ni, Al element is also different, due to spreading speed when C is more than 500 DEG C
Degree is very fast, therefore through two isothermal processs after, C element is enriched with converes instruction camber, can account for C content in whole steel
More than 90%, and then obtain stable converes instruction.
It is an advantage of the present invention that the density of steel is relatively low compared with traditional bainitic steel, about showing for low density steel
There is Al content loss of weight at 3% in technology to can reach 4% or so, the Al content of the present invention can reach 6%, and its loss of weight can reach
8%.In terms of mechanical property, the average elongation after fracture of the present invention can reach 25%, and section Example is up to 40%；In the present invention
Slab low-temperature impact toughness, -20 DEG C of Charpy-V impact power is more than 42J.
Description of the drawings
Fig. 1 be the present invention Technology for Heating Processing figure, ThIt is Homogenization Treatments temperature, t1It is Homogenization Treatments temperature retention time, Tt
It is critical heat treatment temperature, t2It is critical heat treatment temperature retention time.
Fig. 2 is metallographic structure schematic diagram of the steel of 1 composition of embodiment under the heat treatment condition of the invention.
Fig. 3 is scanning electron microscope schematic illustration of tissue of the steel of 2 composition of embodiment under the heat treatment condition of the invention.
Fig. 4 is the property figure that the steel of 3 composition of embodiment is drawn using Thermo-Calc computed in software.
Fig. 5 is converes instruction X-ray diffraction knot of the steel of 5 composition of embodiment under the heat treatment condition of the invention
Fruit schematic diagram.
Specific embodiment
The specific embodiment of the present invention observes microstructure morphology using metallurgical microscope (OM), and X-ray diffractometer is measured
Converes instruction content, and combine the shape of scanning electron microscope (SEM) and transmission electron microscope (TEM) to precipitated phase in invention steel matrix tissue
Looks, distribution and composition are characterized.
In order to be illustrated more clearly that the present invention, with reference to preferred embodiment, the present invention is described further.Ability
Field technique personnel should be appreciated that following specifically described content is illustrative and be not restrictive, and should not limit this with this
The protection domain of invention.
Embodiment 1
The embodiment of the present invention is smelted in vaccum sensitive stove, and table 1 is alloying component (mass fraction)
| C | Al | Mn | Ni | Nb | Ti | Si | S | P | N | Fe |
| 0.11 | 2.01 | 1.57 | 1.86 | 0.041 | 0.02 | 0.13 | 0.001 | 0.001 | 0.001 | 94.256 |
Steel material according to composition shown in table 1 makes strand after smelting and casting.During forging, heating-up temperature is 1200 DEG C, opens
Forging temperature is 1200 DEG C, and higher than 1000 DEG C, forging terminates rear water quenching quick cooling to final forging temperature.
100mm thickness heating steel billet after by forging carries out Homogenization Treatments to 1190 DEG C of insulation 60min, then carries out two ranks
Section rolling.Breaking down temperature is 1000 DEG C, and after deforming through six passages, steel plate thickness is 13mm, and overall reduction is 87%, finishing temperature
For 870 DEG C.After rolling with more than 10 DEG C of cooling rate by steel plate water quenching cooling to room temperature.Critical heat treatment experiment is subsequently carried out：By steel
Plate is heated to air cooling after 712 DEG C of isothermal 60min tempering.Obtain the mechanical property shown in table 2 in embodiment 1.Understand that high intensity is high
The yield strength of the low-density cut deal of elongation percentage is 683MPa, tensile strength is 967MPa, elongation percentage is 29.2%, yield tensile ratio
Charpy-V impact power for 0.71 and -20 DEG C is 54.5J.The metallographic structure of embodiment 1 is obtained as shown in Fig. 2 white portion is δ
Ferrite, black region are tempered martensite.
The mechanical property of 2 steel example 1 of the present invention of table
Embodiment 2
The embodiment of the present invention is smelted in vaccum sensitive stove, and table 3 is alloying component (mass fraction)
| C | Al | Mn | Ni | Nb | Si | S | P | N | Fe |
| 0.18 | 3.24 | 2.48 | 1.94 | 0.053 | 0.19 | 0.001 | 0.001 | 0.001 | 91.914 |
Steel material according to composition shown in table 3 makes strand after smelting and casting.During forging, heating-up temperature is 1200 DEG C, opens
Forging temperature is 1200 DEG C, and higher than 1000 DEG C, forging terminates rear water quenching quick cooling to final forging temperature.
100mm thickness heating steel billet after by forging carries out Homogenization Treatments to 1180 DEG C of insulation 120min, then carries out two
Stage rolling.Breaking down temperature is 1000 DEG C, and after deforming through six passages, steel plate thickness is 13mm, and overall reduction is 87%, finish to gauge temperature
Spend for 870 DEG C.After rolling with more than 10 DEG C of cooling rate by steel plate water quenching cooling to room temperature.Critical heat treatment experiment is subsequently carried out：Will
Steel plate is heated to air cooling after 731 DEG C of isothermal 45min tempering.Obtain the mechanical property shown in table 4 in embodiment 2.Understand high intensity
The yield strength of the low-density cut deal of high-elongation is 629MPa, tensile strength is 780MPa, elongation percentage is 40.4%, Qu Qiang
Than the Charpy-V impact power 50.0J for 0.81 and -20 DEG C.The scanning electron microscope for obtaining embodiment 2 is organized as shown in figure 3, protuberance
It is divided into converes instruction, negative area is tempered martensite.
The mechanical property of 4 steel example 2 of the present invention of table
Embodiment 3
The embodiment of the present invention is smelted in vaccum sensitive stove, and table 5 is alloying component (mass fraction)
| C | Al | Mn | Ni | Nb | Cu | V | Si | S | P | N | Fe |
| 0.25 | 3.95 | 2.41 | 2.97 | 0.015 | 0.5 | 0.03 | 0.19 | 0.001 | 0.001 | 0.001 | 89.682 |
Steel material according to composition shown in table 5 makes strand after smelting and casting.During forging, heating-up temperature is 1200 DEG C, opens
Forging temperature is 1200 DEG C, and higher than 1000 DEG C, forging terminates rear water quenching quick cooling to final forging temperature.
100mm thickness heating steel billet after by forging carries out Homogenization Treatments to 1150 DEG C of insulation 60min, then carries out two ranks
Section rolling.Breaking down temperature is 1000 DEG C, and after deforming through six passages, steel plate thickness is 13mm, and overall reduction is 87%, finishing temperature
For 830 DEG C.After rolling with more than 10 DEG C of cooling rate by steel plate water quenching cooling to room temperature.Critical heat treatment experiment is subsequently carried out：By steel
Plate is heated to air cooling after 730 DEG C of isothermal 30min tempering.Obtain the mechanical property shown in table 6 in embodiment 3.Understand that high intensity is high
The yield strength of the low-density cut deal of elongation percentage is 484MPa, tensile strength is 570MPa, elongation percentage is 31.4%, yield tensile ratio
For 0.85 and -20 DEG C of Charpy-V impact power 53.0J.As shown in figure 4, the property drawn using Thermo-Calc computed in software
Figure, when Homogenization Treatments are described, is obtained delta ferrite and γ austenites, and austenite molar percentage reaches more than 50%.
The mechanical property of 6 steel example 3 of the present invention of table
Embodiment 4
The embodiment of the present invention is smelted in vaccum sensitive stove, and table 7 is alloying component (mass fraction)
| C | Al | Mn | Ni | Nb | Mo | Si | S | P | N | Fe |
| 0.28 | 4.67 | 2.99 | 2.53 | 0.028 | 0.2 | 0.13 | 0.001 | 0.001 | 0.001 | 89.169 |
Steel material according to composition shown in table 7 makes strand after smelting and casting.During forging, heating-up temperature is 1200 DEG C, opens
Forging temperature is 1200 DEG C, and higher than 1000 DEG C, forging terminates rear water quenching quick cooling to final forging temperature.
100mm thickness heating steel billet after by forging carries out Homogenization Treatments to 1130 DEG C of insulation 120min, then carries out two
Stage rolling.Breaking down temperature is 1000 DEG C, and after deforming through six passages, steel plate thickness is 13mm, and overall reduction is 87%, finish to gauge temperature
Spend for 850 DEG C.After rolling with more than 10 DEG C of cooling rate by steel plate water quenching cooling to room temperature.Critical heat treatment experiment is subsequently carried out：Will
Steel plate is heated to air cooling after 738 DEG C of isothermal 30min tempering.Obtain the mechanical property shown in table 8 in embodiment 4.Understand high intensity
The yield strength of the low-density cut deal of high-elongation is 562MPa, tensile strength is 1129MPa, elongation percentage is 26.4%, bends
The strong Charpy-V impact power 45.5J than for 0.50 and -20 DEG C.
The mechanical property of 8 steel example 4 of the present invention of table
Embodiment 5
The embodiment of the present invention is smelted in vaccum sensitive stove, and table 9 is alloying component (mass fraction)
| C | Al | Mn | Ni | Nb | Ti | Si | S | P | N | Fe |
| 0.29 | 5.56 | 3.89 | 2.94 | 0.023 | 0.065 | 0.17 | 0.001 | 0.001 | 0.011 | 87.059 |
Steel material according to composition shown in table 9 makes strand after smelting and casting.During forging, heating-up temperature is 1200 DEG C, opens
Forging temperature is 1200 DEG C, and higher than 1000 DEG C, forging terminates rear water quenching quick cooling to final forging temperature.
100mm thickness heating steel billet after by forging carries out Homogenization Treatments to 1070 DEG C of insulation 180min, then carries out two
Stage rolling.Breaking down temperature is 1000 DEG C, and after deforming through six passages, steel plate thickness is 13mm, and overall reduction is 87%, finish to gauge temperature
Spend for 850 DEG C.After rolling with more than 10 DEG C of cooling rate by steel plate water quenching cooling to room temperature.Critical heat treatment experiment is subsequently carried out：Will
Steel plate is heated to air cooling after 718 DEG C of isothermal 45min tempering.Obtain the mechanical property shown in table 10 in embodiment 5.Understand high intensity
The yield strength of the low-density cut deal of high-elongation is 644MPa, tensile strength is 1211MPa, elongation percentage is 25.8%, bends
The strong Charpy-V impact power 42.0J than for 0.55 and -20 DEG C.The converes instruction X-ray diffraction result of embodiment 5 is obtained as schemed
Shown in 5.
The mechanical property of 10 steel example 5 of the present invention of table
Comparative example 1
Comparative example is smelted in vaccum sensitive stove, and table 11 is alloying component (mass fraction)
| C | Al | Mn | Ni | Nb | Si | Fe |
| 0.068 | 3.93 | 1.06 | 0.84 | 0.040 | 0.32 | 93.742 |
Steel material according to composition shown in table 11 makes strand after smelting and casting.It is swaged into after being heated to 1200 DEG C of insulation 2h
Heating of plate blank to 1150 DEG C of insulation 2h, 1050 DEG C of start rolling temperature are carried out two-stage control to slab and are rolled by the thick slabs of 80mm
System, recrystallization zone rolling temperature >=980 DEG C, non-recrystallization zone rolling temperature≤930 DEG C, the accumulative deflection in non-recrystallization zone are more than
50%, roll rear water quenching.
Heat treatment experiment is subsequently carried out：1h temper is carried out to rolling rear steel plate, temperature is respectively 600 DEG C and 700
℃.The density of the cut deal in acquisition comparative example 1 shown in table 12, yield strength, tensile strength, elongation percentage, yield tensile ratio and 25
DEG C the mechanical property such as Charpy-V impact power.
The mechanical property of 12 steel comparative example 1 of the present invention of table
Claims (7)
1. the low-density cut deal of a kind of high-strength high-elongation ratio, it is characterised in that its chemical composition mass percent is：C：
0.105-0.30%, Al：2.00-6.00%, Mn：1.50-4.00%, Ni：1.80-3.00%, Nb：0.012-0.06%, Si：
0.00-0.20%, controls S, P, N content for S≤0.005%, P≤0.01%, N≤0.005%, and other are for Fe and unavoidably
The content of impurity, wherein C, Mn, Ni, Al answers coincidence formula：+ 1 ＞ [Al] of 12 [C]+0.25 [Mn]+0.2 [Ni].
2. the low-density cut deal of high-strength high-elongation ratio according to claim 1, it is characterised in that above-mentioned chemical composition
In, add Mo, V, Ti, Cu element in one or more replacement Fe, its addition by mass percentage, Mo≤0.5%, V
≤ 0.05%, Ti≤0.08%, Cu≤1%.
3. the preparation method of the low-density cut deal of high-strength high-elongation ratio according to claim 1-2, it is characterised in that
Comprise the steps：
1) carry out smelting, forge according to the chemical composition designed by claim 1 or 2；
2) rolling mill practice：Homogenization Treatments will be carried out in homogenizing treatment temperature insulation 60-180min after forging, then carry out two ranks
Section recrystallization controlled rolling；First stage is rolled for γ austenite recrystallizations area, and rolling temperature is the rank between 1000-950 DEG C
Three passages of section point, every time reduction ratio is in 28-32%；Second stage be delta ferrite recrystallization zone rolling temperature, rolling temperature
Between for 930-800 DEG C, three passages of the stage point, in 24-28% or so, the accumulative reduction ratio of two benches is big for every time reduction ratio
In 85%；Subsequently to be cooled to room temperature more than 10 DEG C/s cooling rates, it is 10-20mm that steel plate is thick eventually；
3) Technology for Heating Processing：By step 2) the hot rolled plate temper that obtains, temperature is Tt± 10 DEG C, Tt=50ln
[C]-1.5[Al]2- 20 [Ni]+858 of+14 [Al] -13 [Mn], unit DEG C are incubated 30-60min, and then air cooling, obtains steel plate.
4. the preparation method of the low-density cut deal of high-strength high-elongation ratio according to claim 3, it is characterised in that institute
State step 2) in homogenizing treatment temperature be Th± 10 DEG C, Th=1220-2400 [C]2+1270[C]-17[Mn]-27[Ni]-30
[Al], unit DEG C.
5. the preparation method of the low-density cut deal of high-strength high-elongation ratio according to claim 3, it is characterised in that institute
State step 2) Homogenization Treatments when, obtain delta ferrite and γ austenites, austenite molar percentage reaches more than 50%.
6. the preparation method of the low-density cut deal of high-strength high-elongation ratio according to claim 3, it is characterised in that institute
State step 3) steel plate that obtains obtains the heterogeneous structure of ferrite, tempered martensite and converes instruction, converes instruction content
Reach more than 10%.
7. the preparation method of the low-density cut deal of high-strength high-elongation ratio according to claim 3-6, it is characterised in that
The yield strength of steel plate is more than 480Mpa, and tensile strength is more than 570Mpa, and elongation after fracture is more than 25%, -20 DEG C of Charpy punching
Work(is hit more than 42J.
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