CN106756567B - A kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% - Google Patents
A kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% Download PDFInfo
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- CN106756567B CN106756567B CN201710068723.9A CN201710068723A CN106756567B CN 106756567 B CN106756567 B CN 106756567B CN 201710068723 A CN201710068723 A CN 201710068723A CN 106756567 B CN106756567 B CN 106756567B
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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
-
- 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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
A kind of hot rolling low density steel of strength and ductility product >=40GPa% and preparation method thereof, belongs to metal material field.The chemical composition of the hot rolling low density steel of strength and ductility product >=40GPa% of the present invention is by percentage to the quality：0.6%~1.0%C, 8%~12%Mn, 7%~11%Al, 0.01%~0.2%V, P≤0.003%, S≤0.002%, surplus are Fe and inevitable impurity.Step of preparation process includes：It smelts, forging, hot rolling, solution hardening processing, has annealing twin in obtained low density steel tissue, the transgranular precipitate for having nanoscale vanadium is strengthened with obvious effects.The steel has the characteristics that low, high-strength, the high ductility of density, and strength and ductility product is more than 40GPa%.
Description
Technical field
The invention belongs to metal material field, more particularly to a kind of hot rolling low density steel of strength and ductility product >=40GPa%
Preparation method.
Background technology
The development trend of Hyundai Motor is light weight, energy saving, anti-corrosion and safety and comfort etc..It is to improve automobile to mitigate automotive dead weight
One of fuel economy, the important measures for saving energy consumption.The report of world's Aluminum Association points out that automotive dead weight often reduces 10%,
Fuel consumption can reduce by 6%~8%；And the fuel consumption of 1L is often reduced, the CO of 2.45kg can be discharged less2。
Under conditions of safety is ensured, can Structural Materials for Automobile Parts be realized by using high-strength steel, its thinned thickness
Lightweight.At present, a series of high-strength steel such as dual phase steel, transformation induced plasticity steel, Multiphase Steel, martensite steel have obtained on automobile
To being widely applied.Although such steel realizes lightweight target by high-strength be thinned, the not lightweight of its material in itself,
For this purpose, people start to set about from the phsyical density of material, the low-density lighting of Study on Steel, passes through addition while high-strength thinned
Density smaller alloying element mitigates the density of steel, it is intended to realize lightweight from many aspects.
The density of steel material can usually be reduced by adding the light-alloys such as aluminium, silicon, manganese member.These alloys are added in steel
When, the lattice parameter that on the one hand can expand steel realizes volume increase, on the other hand the atomic mass of these alloying elements in itself
Relatively low, two aspects are implemented in combination with the reduction of density.But when the Al constituent contents added in steel are higher, the tough impatient of steel can be caused
Play declines, it is difficult to meet requirement of the automotive field to steel toughness.Therefore, high-intensity and high-tenacity low density steel is automotive field
Best applications material.
Invention content
The present invention will be reduced the density of steel, added by rational composition design within the optimum range of Al, Mn content control
Enter V element, improve the intensity of steel, and pass through the preparation process of optimization using refined crystalline strengthening and the precipitation strength effect of V, control it
Organizational composition and precipitate distribution, so as to which steel of the present invention be made to obtain required low-density, high intensity, high ductility, high strength and ductility etc.
Excellent mechanical performance index.
For steel of the present invention in composition design, emphasis considers following element, specially：
Using C as the strong austenizer of steel of the present invention, because C can expand and stable austenite phase region, play solid
The effect of molten reinforcing, and the increase of C content is conducive to improve the austenite phase content in steel makes steel obtain good intensity and tough
Property；But excessively high C content can influence steel welding performance.Therefore consider and C content is scheduled on to 0.6% by percentage to the quality~
In the range of 1.0%, preferably 0.7%~0.9%.
Using Mn as one of lighting element of steel of the present invention, because the density of Mn is 7.43g/cm3, and the density of Fe is
7.85g/cm3, therefore Mn can reduce the density of steel of the present invention.In addition, using Mn as one of main austenitizing alloying element,
Because Mn can expand austenite phase field, stable austenite tissue, while play the role of solution strengthening, compared to ferrite, Ovshinsky
Body has stronger work hardening capacity.Therefore consider, Mn contents are scheduled on 8%~12% range by percentage to the quality
It is interior, preferably 9%~11%.
Using Al as one of lighting element of steel of the present invention, because the density of Al is 2.7g/cm3, far below 7.85g/
cm3Fe density, density of material can be substantially reduced.Certain Al content can also significantly improve the Deformation Resistance of steel, carry
The corrosion resistance of Gao Gang postpones Dynamic cracking, and Al can also significantly improve the stacking fault energy of steel, changes deformation mechanism, containing Al's
Medium managese steel can have certain cushioning effect when fierce collision occurs.But it is strong ferritisey in view of Al, it is excessively high
Al content easily promotes the formation of ferritic phase, reduces austenite phase content, therefore Al content is scheduled on to 7% by percentage to the quality~
In the range of 11%, preferably 8%~9%.Herein it should be pointed out that Al melting loss of elements is serious in smelting process, it should also be noted that should
The rational proportion of element.
V is added in steel of the present invention, is mainly acted on using the refined crystalline strengthening of V and precipitation strength.V can be substantially dissolved in Ovshinsky
Tiny V (C, N) particle is precipitated in body and in pro-eutectoid ferrite, this precipitation can significantly improve the intensity of steel.In addition, in Austria
High V (C, N) solubility allows to use relatively low relation reheating temperature in family name's body, it means that relatively low production cost.The present invention
The deformation mechanism of steel is based on dislocation movement by slip, and tiny precipitated phase can be precipitated in the addition of V in steel, these precipitated phases are on the one hand
Nucleation rate can be improved, obstruction crystal grain grows up and carrys out crystal grain thinning；On the other hand dislocation motion can be hindered to improve intensity so that
Finally obtain good comprehensive mechanical property.Therefore V content is scheduled in the range of 0.01%~0.2% by percentage to the quality,
It is preferred that 0.05%~0.15%.
P, S in steel of the present invention are harmful element, easily cause the brittle failure of steel, reduce steel plate toughness, mouldability is made to be deteriorated,
Therefore it needs strictly to control P, S content in steel, but in practical smelting, content can not possibly be zero in smelting process, therefore this
Invention require both elements low as possible in controllable range, i.e., by percentage to the quality P≤0.003%, S≤
0.002%.
The specific technical solution that the present invention uses is as follows：
Hot rolling low density steel of a kind of strength and ductility product >=40GPa% of the present invention and preparation method thereof, chemical composition is with matter
Measuring percentages is：0.6%~1.0%C, 8%~12%Mn, 7%~11%Al, 0.01%~0.2%V, P≤0.003%,
S≤0.002%, surplus are Fe and inevitable impurity, which is 6.48~7.08g/cm3, specific step of preparation process
It is as follows：
1) it smelts and is cast into base, strand is forged into slab；
2) slab is heated to 1150 DEG C~1200 DEG C, 6 passage hot rollings, hot rolling open rolling is carried out after keeping the temperature to microstructure homogenization
1070 DEG C~1120 DEG C of temperature, 850 DEG C~900 DEG C of finishing temperature add up deflection 87%~92%, roll rear water cooling to 200 DEG C
~300 DEG C are batched, and are then air-cooled to room temperature, are obtained hot rolled strip；
3) hot rolled strip is subjected to solution treatment, then direct-water-quenching to room temperature, obtains finished product low density steel band.
Hot rolling low density steel of a kind of strength and ductility product >=40GPa% of the present invention and preparation method thereof, it is characterised in that：
The tissue defects of strand are eliminated in requirement in strand forging process, the slab being forged into without component segregation, no shrinkage cavity and
Rarefaction defect.
Preparation process 3) in solid solution temperature for 900 DEG C~950 DEG C, soaking time 1h.
Quenched hot rolling low density steel is organized as austenite+ferrite dual phase tissue, has annealing twin in austenite,
There are nano level vanadium precipitates in crystal grain, refined crystalline strengthening and precipitation strength can be played the role of.
Preferably, the chemical composition of steel of the present invention contains 0.7%~0.9%C by percentage to the quality.
Preferably, the chemical composition of steel of the present invention contains 9%~11%Mn by percentage to the quality.
Preferably, the chemical composition of steel of the present invention contains 8%~9%Al by percentage to the quality.
Preferably, the chemical composition of steel of the present invention contains 0.05%~0.15%V by percentage to the quality.
Hot rolling low density steel of a kind of strength and ductility product >=40GPa% of the present invention and preparation method thereof, it is characterised in that：It quenches
Yield strength 719MPa~752MPa of hot rolling low density steel after fire, tensile strength 910MPa~925MPa, elongation after fracture
43%~48%, strength and ductility product >=40GPa%.
The hot rolling low density steel of the present invention, compared with other advanced high-strength automobile steels, has the following advantages：
(1) steel of the present invention has excellent comprehensive mechanical property, has the good fitting of intensity and plasticity after solution treatment
(high intensity and high elongation after fracture), impact absorption can be higher.
(2) simple production process of the present invention, using hot rolling+solid solution treatment method, without cold rolling, production process is short, saves
Time and cost.
(3) present invention is matched using rational alloying element, on the basis of the excellent comprehensive mechanical property of steel plate is ensured,
Steel plate density is reduced, weight loss effect is apparent.
(4) steel of the present invention adds microalloy element vanadium, and nano level V (C, N) can be precipitated in crystal grain, play fine grain for vanadium
Strengthen the effect with processing hardening, improve the intensity and plasticity of steel.In addition, V is relatively inexpensive compared to other alloys, on the one hand drop
Low actual industrial production cost, while the carbon equivalent of steel can also be reduced, be conducive in steel plate subsequent production into welding assembly.
Description of the drawings：
Attached drawing 1 is typical metallographic structure photo after 1 solution treatment of the embodiment of the present invention.
Attached drawing 2 is the precipitate photo of the transgranular vanadium of transmission electron microscope observing after 1 solution treatment of the embodiment of the present invention.
Specific embodiment
Embodiment 1
The chemical composition and density of the embodiment of the present invention 1 are as shown in table 1, and specific implementation process is：(1) vacuum smelting furnace smelting
It refines and is cast into base, strand is forged into slab, the component segregation in strand, removal shrinkage cavity, loose etc. are eliminated in forging process
Defect；(2) slab is heated to 1150 DEG C, carries out 6 passage hot rollings after keeping the temperature to microstructure homogenization, 1080 DEG C of hot rolling start rolling temperature,
865 DEG C of finishing temperature adds up deflection 87%, rolls rear water cooling and is batched to 240 DEG C, is then air-cooled to room temperature, obtains hot rolling
Steel band；(3) hot rolled strip is subjected to solution treatment, 900 DEG C, soaking time 60min of solid solution temperature, then direct-water-quenching is extremely
Room temperature obtains finished product low density steel band.
Structure observation analysis is carried out to finished product steel belt, that observes finished product steel belt is organized as ferrite+austenitic duplex tissue,
There are annealing twin in austenite, there is nano level vanadium precipitates in crystal grain, metallographic structure photo as shown in Figure 1, precipitate
Photo is as shown in Figure 2.Mechanics properties testing obtains that the results are shown in Table 2.
Embodiment 2
The chemical composition and density of the embodiment of the present invention 2 are identical with embodiment 1, as shown in table 1, specific implementation process
For：(1) vacuum smelting furnace is smelted and is cast into base, strand is forged into slab, the ingredient eliminated in strand in forging process is inclined
Analysis, removal shrinkage cavity, it is loose the defects of；(2) slab is heated to 1180 DEG C, and 6 passage hot rollings are carried out after keeping the temperature to microstructure homogenization, heat
Roll 1100 DEG C of start rolling temperature, 890 DEG C of finishing temperature adds up deflection 92%, rolls rear water cooling and is batched to 265 DEG C, Ran Houkong
It is cooled to room temperature, obtains hot rolled strip；(3) hot rolled strip is subjected to solution treatment, 950 DEG C of solid solution temperature, soaking time
60min, then direct-water-quenching to room temperature, obtains finished product low density steel band.
Structure observation analysis is carried out to finished product steel belt, that observes finished product steel belt is organized as ferrite+austenitic duplex tissue,
There are annealing twin in austenite, there are nano level vanadium precipitates in crystal grain.The result that mechanics properties testing obtains such as 2 institute of table
Show.
Comparative example 1, comparative example 2, comparative example 3
Comparative example 1, comparative example 2, the chemical composition of comparative example 3 and density are same as Example 1, preparation method with it is real
It is essentially identical to apply example 1, the difference lies in the solid solution temperature of comparative example 1 is 800 DEG C, the solid solution temperature of comparative example 2
It it is 850 DEG C, the solid solution temperature of comparative example 3 is 1000 DEG C.Mechanics properties testing obtains that the results are shown in Table 2.
Embodiment 3
The chemical composition and density of the embodiment of the present invention 3 are as shown in table 1, and specific implementation process is same as Example 1.
Steel band is organized as ferrite+austenitic duplex tissue after observation is quenched, there are annealing twin in austenite,
There are nano level vanadium precipitates in crystal grain.Mechanics properties testing obtains that the results are shown in Table 2.
Embodiment 4
The chemical composition and density of the embodiment of the present invention 4 are as shown in table 1, and specific implementation process is same as Example 2.
Steel band is organized as ferrite+austenitic duplex tissue after observation is quenched, there are annealing twin in austenite,
There are nano level vanadium precipitates in crystal grain.Mechanics properties testing obtains that the results are shown in Table 2.
The chemical composition (mass percent, %) and density of 1 embodiment steel of table and comparative example steel
The solid solution temperature and mechanical property of 2 embodiment steel of table and comparative example steel
Three embodiments of steel of the present invention can be seen that：
Comparative example 1, comparative example 2, embodiment 1, embodiment 2, the mechanical property result of comparative example 3 can be seen that：Work as ingredient
When identical, solid solution temperature is affected to mechanical property；When solid solubility temperature is in the range of 800 DEG C~1000 DEG C,
The trend continuously decreased is presented in yield strength and tensile strength, and have no progeny can elongation percentage then present and first increase becoming of reducing afterwards
Gesture；When solid solubility temperature is 900 DEG C and 950 DEG C, elongation percentage is all higher than 40%, there is optimal strength plastic's matching, and strength and ductility product is up to
40GPa% grades.
The mechanical property yield strength of all embodiments be 719MPa~752MPa, tensile strength for 910MPa~
925MPa, elongation after fracture are 43%~48%, strength and ductility product >=40GPa%, there is high intensity, high elongation after fracture, excellent
The characteristics of different strength plastic matches, high strength and ductility.
Tissue sees that the tissue of steel of the present invention is ferrite+austenitic duplex tissue, deformation mechanism using dislocation movement by slip as
Main, tiny nanoscale precipitated phase can be precipitated in the addition of V in steel, on the one hand these precipitated phases can improve nucleation rate, resistance
Crystal grain is hindered to be grown up and carrys out crystal grain thinning；On the other hand dislocation motion can be hindered to improve intensity, it is good so as to obtain steel of the present invention
Good comprehensive mechanical property.
It should be noted last that above-described specific embodiment, to the purpose of the present invention, technical solution and beneficial
Effect has been further described, it should be understood that the foregoing is merely the specific embodiment of the present invention, and
Be not intended to limit the invention, it is all within the spirit and principle of technical solution of the present invention, any modification for being made, equivalent replacement,
Improve etc., it should be included within the claims of the present invention.
Claims (5)
1. a kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa%, which is characterized in that chemical composition is with quality
Percentages are：0.81%~0.85%C, 8%~12%Mn, 7%~11%Al, 0.01%~0.2%V, P≤0.003%,
S≤0.002%, surplus are Fe and inevitable impurity, which is 6.48~6.83g/cm3, specific step of preparation process
It is as follows：
1) it smelts and is cast into base, strand is forged into slab；
2) slab is heated to 1150 DEG C~1200 DEG C, hot rolling, hot rolling start rolling temperature 1070 is carried out after keeping the temperature to microstructure homogenization
DEG C~1120 DEG C, 850 DEG C~900 DEG C of finishing temperature, add up deflection 87%~92%, roll rear water cooling to 200 DEG C~300 DEG C into
Row batches, and is then air-cooled to room temperature, obtains hot rolled strip；
3) hot rolled strip is subjected to solution treatment, then direct-water-quenching to room temperature, obtains low density steel band；
Yield strength 719MPa~752MPa of the hot rolling low density steel, tensile strength 910MPa~925MPa, extension of having no progeny
Rate 43%~48%, strength and ductility product >=40GPa%；
Solid solution temperature described in step 3) is 900 DEG C~950 DEG C, soaking time 1h；
Hot rolling low density steel after the water quenching is organized as austenite+ferrite dual phase tissue, has annealing twin in austenite,
There are nano level vanadium precipitates in crystal grain.
2. a kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% as described in claim 1, feature exist
In needing to eliminate the tissue defects of strand in forging process, the slab being forged into no shrinkage cavity and loose is lacked without component segregation
It falls into.
3. a kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% as described in claim 1, feature exist
In the mass percent of Mn is 9%~11% in chemical composition.
4. a kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% as described in claim 1, feature exist
In the mass percent of Al is 8%~9% in chemical composition.
5. a kind of preparation method of the hot rolling low density steel of strength and ductility product >=40GPa% as described in claim 1, feature exist
In the mass percent of V is 0.05%~0.15% in chemical composition.
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| CN107674955B (en) * | 2017-09-29 | 2019-05-07 | 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 greater than 50GPa% |
| CN109694990B (en) * | 2017-10-20 | 2020-09-01 | 鞍钢股份有限公司 | Light transformation induced plasticity steel with good strong plasticity and production method thereof |
| CN109694997B (en) * | 2019-02-25 | 2021-08-06 | 上海大学 | Heat treatment process for improving mechanical property of Fe-Mn-Al-C dual-phase steel by utilizing gamma → alpha isomerous transformation |
| CN109943780B (en) * | 2019-04-29 | 2021-04-27 | 东北大学 | High-carbon medium-manganese wear-resistant steel and preparation method thereof |
| CN114015951B (en) * | 2021-11-16 | 2023-03-28 | 攀钢集团攀枝花钢铁研究院有限公司 | Hot-rolled light high-strength steel and preparation method thereof |
| CN114525443B (en) * | 2022-02-21 | 2022-11-29 | 北京科技大学 | Cu-Al alloyed high-strength medium manganese steel hot rolled plate and preparation method thereof |
| CN114752867B (en) * | 2022-04-25 | 2022-10-11 | 燕山大学 | High-strength and high-toughness lightweight steel and preparation method and application thereof |
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| CN103667883B (en) * | 2013-12-26 | 2017-01-11 | 北京科技大学 | Low-density and high-toughness automobile-used steel board and preparation process |
| CN104674109B (en) * | 2015-03-11 | 2017-01-18 | 北京科技大学 | Low-density Fe-Mn-Al-C system cold-rolled automobile steel plate and preparation method |
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