CN102828109A - Metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel and production method thereof - Google Patents
Metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel and production method thereof Download PDFInfo
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Abstract
The invention discloses a metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel and a production method thereof. The plastic product steel is used for producing a thin steel plate used for an automobile, so the anti-collision property is effectively improved, the automobile body weight is lowered, the fuel economical efficiency is realized, and the environment pollution caused by waste gas emission is lowered. The plastic product steel provided by the invention comprises the following chemical components in percentage by weight: 0.10-1.0% of C, 0.20-2.0% of Si, 5-14% of Mn, 0.005-0.015% of P, less than or equal to 0.005% of S, 0.02-0.50% of Als, less than or equal to 0.05% of N and the balance of Fe and inevitable impurities. The production method comprises the following steps of: adopting vacuum smelting, and pouring into a casting blank; carrying out hot rolling on the casting blank to form a hot rolling plate; performing interval annealing on the hot rolling plate in a metastable-state tissue; and obtaining the finished product, i.e. the hot rolling plate of the metastable-state phase-change plastification ultra-fine grain high-intensity plastic product steel. According to the invention, the steel cleanliness, the machinability and the surface quality are improved by an intermediate/ low C-Mn and Si and V alloy systems according to the metastable-state austenite phase change TRIP (transformation-induced plasticity) effect. The continuous casting plate blank is adopted for direct hot rolling and forming, and steel plates with different strong plastic product indexes are obtained.
Description
Technical field
The present invention relates to high strength and ductility steel plate and working method thereof, ultra-fine brilliant high strength and ductility steel of especially a kind of metastable state phase transformation plastifying and working method thereof.
Background technology
Young mobile is to use high-strength and super-strength steel to realize lightweight, low emission, the crashworthiness and energy-conservation of automobile with the developing direction of steel, and high strength and ductility has become high-performing car with the most important measurement index of steel.With DP, TRIP, TWIP and thermoforming steel etc. is the target that the advanced high-strength steel of representative has temporarily satisfied automobile industry development to a certain extent.But along with steel such as DP, TRIP applying on automobile; (15～20GPa%) only can accomplish the shaping of simple member to its limited strength and ductility product; And the performance deficiency that steel grade itself brings manifests gradually, and is big like raising, unit elongation decline, punching press resilience along with intensity; The difference of the ununiformity of microtexture and the strong plasticity of different tissues causes it in crooked and flanging forming, crackle to occur; The increase of chemical ingredients (especially element such as carbon, manganese) addition causes that welding property worsens; Some chemical elements (like silicon) that add in order to obtain tissues needed bring adverse influence but for cold-reduced sheet surface quality, coating etc.And the thermoforming steel is after intensity surpasses 1000MPa, and the decrease ductility amplitude strengthens, and (9～15GPa%) are difficult to satisfy the shaping needs of complex component to lower strength and ductility product.After this carried out having the foundational development than the TWIP steel of high strength and ductility, traditional TWIP steel is on the basis of Ha Defeier (Hadfield) steel, to develop, and its processing characteristics is very poor, and major cause is:
(1) the Mn element (>=20%) of superelevation content has reduced the thermal conductivity of steel, and free linear shrinkage value (2.4% ~ 3.0%) is 2 ~ 3 times of plain carbon stool, causes the as-cast structure of steel thick, and original strand/ingot surface is prone to produce thermal crack, crackle aggravation after the hot rolling.
(2) owing to contain a large amount of Mn elements in the steel, possibly cause in the steel component segregation and S and P element to gather partially during casting, reduction crystal boundary, brittle carbides (M in a large number simultaneously at crystal boundary
23C
6, M
5C
2) separate out the TWIP steel very easily produced along brilliant crackle in course of hot rolling.
(3) the high preliminary work hardening rate of high Mn steel inherent causes the rolling deformation drag higher, has increased mill load, makes it be difficult to cold machine-shaping.
(4) dynamic strain aging of high mangaenese steel is unfavorable to ream forming, and the delay fragility of punching press high mangaenese steel etc. all makes it on existing traditional auto sheet production line, be difficult to produce and apply in enormous quantities.
Open (bulletin) number is in " being produced the method for hot rolled band by lightweight structural steel " two publication documents of CN 101084073A for CN 101065503A " have high-strength steel strip or the tole of TWIP performance and through its method of steel band continuous casting preparation " with publication number, proposition employing steel band continuous casting (DSC) technology combination hot rolling, the cold rolling TWIP steel of preparing the high silicon of compound interpolation, high alumina and alloying elements such as Ni, Cr, V, Ti and Nb.But aluminium is a kind of ferrite stabilizer; Effect with raising stacking fault energy (SFE), reduction stabilization of austenite; With destroying HS and the high-ductility that is produced owing to strain inducing twin effect, therefore, the interpolation of aluminium is to the influence of stabilization of austenite; Must compensate through manganese or other austenite stabilizer element (like Ni etc.), this will improve the cost of steel; The easy oxidation of aluminium simultaneously makes the control difficulty of inclusion in smelting and the casting strengthen again, reduces purity of steel, and strong plasticity is had a negative impact.When the add-on of silicon is too much, can make cast material produce more complex deoxidization product, worsen its as-cast characteristic; And the silicon oxide that occurs viscosity on the hot rolled band surface reduces coating.Its hot workability of twin crystal inducing plasticity steel that contains high silicon, high alumina is very poor, and hot rolling tends to occur serious limit and splits, and reduces the utilization ratio of material.Though the adding of alloying elements such as a large amount of Ni, Cr can improve materials processed and part mechanical property to a certain extent, the economy of its production reduces greatly.
Open (bulletin) number is CN 101111622A; In the publication document of " austenitic steel with high intensity and formability; make the method and the application thereof of said steel " by name, reach performance requriements, need to adopt to reach the batch annealing more than 4 hours for making cold rolled sheet; Both increased energy consumption, improved production cost, and greatly reduced production efficiency again, prolong life cycle of the product.
Open (bulletin) number is in two China's patent documentation of CN 101215672A and CN 101235464A; Receive the restriction of superelevation manganese (>=20%) and high silicon, high alumina (>=2%); Ingot casting, forge hot are adopted in the preparation of hot rolling TWIP steel plate, to improve the surface imperfection of hot rolling plate.Yet the forge hot operation must be carried out by off-line, has not only destroyed the continuity of producing but also increased production cost.In the existing TWIP steel technology, carried out steel grades and technological design to the TWIP effect, its tensile strength fails to reach superstrength (>=900MPa) requirement; Though and its intensity of cold rolled automobile steel plate with TRIP effect is high, plasticity is on the low side (≤30%).
Summary of the invention
The invention provides ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying and working method thereof, produce thin steel sheet for automobile, effectively improve anti-collision property, reduce car body weight, realize fuel economy and reduce the environmental pollution that exhaust gas emission causes.
The ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying provided by the invention is characterized in that comprising by weight percentage following chemical composition:
C:0.10% ~ 1.0%; Si: 0.20% ~ 2.0%; Mn:5% ~ 14%; P:0.005% ~ 0.015%, S≤0.005%; Als:0.02% ~ 0.50%; N≤0.05%, all the other are Fe and unavoidable impurities.
The ultra-fine brilliant high strength and ductility steel of said a kind of metastable state phase transformation plastifying is characterized in that also comprising by weight percentage following chemical composition:
V:0.05 ~ 0.30%; Ni:0.15 ~ 0.50%; Nb:0.005% ~ 0.05%; Ti:0.005%～0.05%; Ca:0.001% ~ 0.006%; RE:0.0005% ~ 0.002%; In Mg:0.0005% ~ 0.002% a kind or any 2 ~ 6 kinds.
The comprehensive mechanical property of the ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying is following:
Tensile strength (Rm) 800～1300 MPa;
Ys (Rel) 450～900 MPa;
Unit elongation (A
50) 28%～45%;
Work hardening exponent (n) 0.25～0.45;
Strength and ductility product (Rm * A
50) 30～45GPa%.
The working method of the ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying is characterized in that this method may further comprise the steps:
A. adopt vacuum metling, pouring temperature is controlled at 1450 ℃～1550 ℃, pours into strand;
B. strand hot rolling, heating and temperature control are incubated 30～120min at 1050 ℃～1150 ℃; Start rolling temperature is controlled at 1100 ℃～800 ℃, and finishing temperature is controlled at 850 ℃～600 ℃, is rolled to 3 mm～5mm; Roll the back steel plate and cool off fast, rate of cooling >=15 ℃/s form hot-rolled sheet;
C. hot-rolled sheet forms interval annealing at the metastable state tissue, 600 ~ 720 ℃ of annealing temperatures, and soaking time 5min ~ 180min is chilled to room temperature soon with >=20 ℃/s cooling rate, obtains the ultra-fine brilliant high strength and ductility steel hot-rolled sheet of finished product metastable state phase transformation plastifying;
The working method of the ultra-fine brilliant high strength and ductility steel of said a kind of metastable state phase transformation plastifying; It is characterized in that through after the above-mentioned a.b step; The Cold Rolled Sheet Steel that the cold rolling one-tenth thickness of draft of hot-rolled sheet warp 40%～80% is 0.8mm～2.0mm; In 600 ℃～720 ℃ temperature ranges, Cold Rolled Sheet Steel is carried out isothermal annealing handle soaking time 3 min～30min then; Be chilled to room temperature soon with >=15 ℃/s cooling rate, obtain the ultra-fine brilliant high strength and ductility steel tole of metastable state phase transformation plastifying of suitable drawing.
Based on the ultra-fine brilliant high strength and ductility steel of metastable state phase transformation plastifying, the component effect of being adopted is following:
C: help inventing steel and obtain required intensity index; Increase austenitic stability, reduce the excessive reduction of the caused stabilization of austenite in back to avoid Mn, (low) C in steel, keeping suppresses ferritic and ε-martensitic too early formation, and therefore, preferred C content is 0.10%～1.0%.
Mn: be austenite stabilizer element, it can spread in austenite in the critical annealing district, makes Mn and C simultaneously enrichment and homogenizing in austenite, so stability and the pearlitic formation of change austenite in subsequent cooling process.Simultaneously, the adding of Mn makes the Ms point lower, and the amount of residual austenite increases.Compared with prior art, the invention steel greatly reduces Mn content in design mix, and the microsegregation, the rolling defect that have reduced in the casting blank solidification process produce chance and the too high rolling difficulty that causes of work hardening rate.When Mn content surpassed 20%, its TWIP effect was strong, is unfavorable for high-intensity acquisition; Be lower than 2% like Mn content,, be unfavorable for that material obtains high-ductility then fully by showing as the TRIP effect.
Si is distributed in the ferritic, improves the chemical potential of carbon in the ferritic, impels carbon in the ferritic to the austenite internal divergence, and the carbon concentration in the austenite raises.Because Si does not dissolve in carbide; Carbide precipitation is suppressed by Si; Correspondingly in residual austenite, can cause the enrichment of more carbon, make austenite have more residual or higher stabilization tendency, also help the raising of intensity and the lighting of material simultaneously.
P also can improve austenitic content and stability, and part replaces Si also can when bainite transformation, suppress the deposition of C, keeps little crystal grain austenite, comes the stable residual austenite through the restraint force of solution strengthening effect raising parent in addition.
Mg: different with other reductor; Magnesium combines to form very fine precipitate with oxygen; These fine precipitates even dispersion in steel distributes, and has avoided the macrobead oxide inclusion to be detained the stress concentration that is produced in the steel, reduce to mould, the flexible disadvantageous effect.
In addition, Ni is an austenite stabilizer element, and adding little amount of N i in the steel can the stable austenite microstructure.V can increase the amount of residual austenite.
The present invention combines design of alloy, smelting, rolling and thermal treatment process; It is the compound polyphase structure steel plate of ultra-fine lath metastable state austenite+ferrite lath that acquisition has the some amount original structure, and the metastable state austenite becomes in viscous deformation middle part distribution looks, changes ε+α martensite into; It is the TRIP effect; Through martensitic formation in the phase transformation, produce volumetric expansion and suppress the formation of material constriction and produce the plasticity enhancing, the mutually martensitic formation of hard produces superstrength simultaneously; The ferritic that exists with ultra-fine lath attitude then keeps good plasticity ductility in viscous deformation, make material have high-ductility.Band through above chemical ingredients makes up and preparation technology obtained has following tissue signature:
1) after hot rolling+metastable state critical annealing and cold rolling+subcritical annealing were handled, the microstructure of steel plate comprised the heterogeneous structure of the above ultra-fine austenite lath+ferrite lath of 30% (volume(tric)fraction).
2) tissue after the unilateral stretching distortion comprises heterogeneous complex tissues such as martensite, ultra-fine lath metastable state residual austenite and ultra-fine lath-shaped ferritic.
The present invention compared with prior art has following remarkable beneficial effect:
1) under preferred composition and technology; Acquisition has the metastable state residual austenite and the ferritic of the ultra-fine panel construction of certain set of dispense ratio; Utilize the TRIP effect of metastable state austenite phase transformation; Produce superstrength and plasticity and strengthen, and the high-ductility characteristic of soft phase ferritic structure, acquisition has the steel plate of high strength and ductility, high comprehensive performance.
2) during the invention steel adopts/low C-Mn with Si, V alloy is, greatly reduces Mn content, and do not have the adding of high silicon, high alumina and a large amount of valuable alloys, not only practices thrift product cost, also effectively reduced complex deoxidization product and fragility phase (SiO
2, Al
2O
3) and a large amount of generations, the gathering of sulfide (MnS), improve steel cleanliness factor, workability and surface quality.
3) adopt the continuous casting steel billet direct heat to roll into shape, need not to adopt DSC technology, save facility investment and production cost.
4) need not long term annealing, and through different metastable state isothermal annealing treatment process, the steel plate that acquisition has different strength and ductility product indexs satisfies the different diversified demands of plasticity component formings by force, realizes effective utilization of the resource and the energy.
Description of drawings
Fig. 1 is the ultra-fine brilliant high strength and ductility steel embodiment 1 unilateral stretching stress-strain curve of a kind of metastable state phase transformation plastifying.
Fig. 2 is the ultra-fine brilliant high strength and ductility steel embodiment 2 unilateral stretching stress-strain curves of a kind of metastable state phase transformation plastifying.
Fig. 3 is the ultra-fine brilliant high strength and ductility steel embodiment 4 unilateral stretching stress-strain curves of a kind of metastable state phase transformation plastifying.
Fig. 4 is the heterogeneous microstructure after the ultra-fine brilliant high strength and ductility steel embodiment 1 subcritical isothermal annealing of a kind of metastable state phase transformation plastifying.
Fig. 5 is the heterogeneous microstructure after the ultra-fine brilliant high strength and ductility steel embodiment 4 subcritical isothermal annealings of a kind of metastable state phase transformation plastifying.
Fig. 6 is the heterogeneous microstructure after the ultra-fine brilliant high strength and ductility steel embodiment 1 unilateral stretching distortion of a kind of metastable state phase transformation plastifying.
Embodiment
More describe the present invention in detail with embodiment below.
Embodiment 1-5, the chemical ingredients that the ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying is comprised, as shown in table 1, all the other are Fe and unavoidable impurities.
Table 1 chemical ingredients (wt %)
The comprehensive mechanical property of the ultra-fine brilliant high strength and ductility steel of the foregoing description 1-5 metastable state phase transformation plastifying is as shown in table 2:
Table 2 comprehensive mechanical property
Embodiment 4-5, the step of the working method of the ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying is:
A. adopt vacuum metling, pouring temperature is seen table 3 embodiment 4,5, pours into strand;
B. table 3 embodiment 4,5 is seen in strand hot rolling, Heating temperature, soaking time table 3 embodiment 4,5; Start rolling temperature is seen table 3 embodiment 4,5, and finishing temperature is seen table 3 embodiment 4,5, is rolled to 3 mm～5mm; Roll the back steel plate and cool off fast, rate of cooling is seen table 3 embodiment 4,5, forms hot-rolled sheet;
C. hot-rolled sheet forms interval annealing at the metastable state tissue, and annealing temperature is seen table 3 embodiment 4,5, and soaking time is seen table 3 embodiment 4,5, is chilled to room temperature soon with >=15 ℃/s cooling rate, obtains the ultra-fine brilliant high strength and ductility steel hot-rolled sheet of finished product metastable state phase transformation plastifying.
Embodiment 1-3, the step of the working method of the ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying is:
After a.b step among the embodiment 4-5; The Cold Rolled Sheet Steel that hot-rolled sheet is 0.8mm～2.0mm through the cold rolling one-tenth thickness of the draft of table 3 embodiment 1,2,3; Under table 3 embodiment 1,2,3 temperature, Cold Rolled Sheet Steel is carried out isothermal annealing handle then, soaking time is seen table 3 embodiment 1,2,3; Be chilled to room temperature soon with watch 3 embodiment 1,2,3 cooling rates, obtain the ultra-fine brilliant high strength and ductility steel tole of metastable state phase transformation plastifying of suitable drawing.
The preparation technology parameter of table 3 embodiment of the invention steel
Steel plate through above-mentioned processing has following characteristic: continuous surrender, low yield strength ratio, and the thing phase composite is ultra-fine lath-shaped residual austenite+ferritic, and original grain is of a size of 5～15 μ m, and phase composite is as shown in table 4 before and after the distortion.
Organizational composition under table 4 different steps
Steel of the present invention has been concentrated advantages such as high-strength plasticity, good uniform elongation, high work hardening exponent, low yield strength ratio and processibility are good; Can satisfy that 800～1300MPa is high-strength, performance requriementss such as the shaping of superstrength different stage structural part and anti-collision, become the young mobile structural steel preferred material of tool potentiality.
Claims (4)
1. ultra-fine brilliant high strength and ductility steel of metastable state phase transformation plastifying is characterized in that comprising by weight percentage following chemical composition:
C:0.10% ~ 1.0%; Si: 0.20% ~ 2.0%; Mn:5% ~ 14%; P:0.005% ~ 0.015%, S≤0.005%; Als:0.02% ~ 0.50%; N≤0.05%, all the other are Fe and unavoidable impurities;
The comprehensive mechanical property of the ultra-fine brilliant high strength and ductility steel of above-mentioned a kind of metastable state phase transformation plastifying is following:
Tensile strength (Rm) 800～1300 MPa;
Ys (Rel) 450～900 MPa;
Unit elongation (A
50) 28%～45%;
Work hardening exponent (n) 0.25～0.45;
Strength and ductility product (Rm * A
50) 30～45 GPa%.
2. according to the ultra-fine brilliant high strength and ductility steel of claims 1 described a kind of metastable state phase transformation plastifying, it is characterized in that also comprising by weight percentage following chemical composition:
V:0.05 ~ 0.30%; Ni:0.15 ~ 0.50%; Nb:0.005% ~ 0.05%; Ti:0.005%～0.05%; Ca:0.001% ~ 0.006%; RE:0.0005% ~ 0.002%; In Mg:0.0005% ~ 0.002% a kind or any 2 ~ 6 kinds.
3. the working method of the ultra-fine brilliant high strength and ductility steel of claims 1 described a kind of metastable state phase transformation plastifying is characterized in that this method may further comprise the steps:
A. adopt vacuum metling, pouring temperature is controlled at 1450 ℃～1550 ℃, pours into strand;
B. strand hot rolling, heating and temperature control are incubated 30～120min at 1050 ℃～1150 ℃; Start rolling temperature is controlled at 1100 ℃～800 ℃, and finishing temperature is controlled at 850 ℃～600 ℃, is rolled to 3 mm～5mm; Roll the back steel plate and cool off fast, rate of cooling >=15 ℃/s form hot-rolled sheet;
C. hot-rolled sheet forms interval annealing at the metastable state tissue, 600 ~ 720 ℃ of annealing temperatures, and soaking time 5min ~ 180min is chilled to room temperature soon with >=15 ℃/s cooling rate, obtains the ultra-fine brilliant high strength and ductility steel hot-rolled sheet of finished product metastable state phase transformation plastifying.
4. the working method of the ultra-fine brilliant high strength and ductility steel of a kind of metastable state phase transformation plastifying according to claim 3; It is characterized in that through after the above-mentioned a.b step; The Cold Rolled Sheet Steel that the cold rolling one-tenth thickness of draft of hot-rolled sheet warp 40%～80% is 0.8mm～2.0mm; In 600 ℃～720 ℃ temperature ranges, Cold Rolled Sheet Steel is carried out isothermal annealing handle soaking time 3 min～30min then; Be chilled to room temperature soon with >=15 ℃/s cooling rate, obtain the ultra-fine brilliant high strength and ductility steel tole of metastable state phase transformation plastifying of suitable drawing.
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