CN105568145A - Cold-rolled ultrahigh-strength biphase steel plate for vehicle with corrosion resistance and preparation method thereof - Google Patents
Cold-rolled ultrahigh-strength biphase steel plate for vehicle with corrosion resistance and preparation method thereof Download PDFInfo
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- CN105568145A CN105568145A CN201510982804.0A CN201510982804A CN105568145A CN 105568145 A CN105568145 A CN 105568145A CN 201510982804 A CN201510982804 A CN 201510982804A CN 105568145 A CN105568145 A CN 105568145A
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
-
- 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
- C21D2211/008—Martensite
Abstract
The invention discloses a cold-rolled ultrahigh-strength biphase steel plate for a vehicle with corrosion resistance and a preparation method thereof. The steel plate comprises the following chemical components in percentage by mass: 0.13-0.16% of C, 1.8-2.0% of Si, 2.3-2.5% of Mn, 1.8-2.2% of Cr, 0.010-0.025% of Al, 0.001-0.008% of S, 0.002-0.012% of P, 0.001-0.004% of N, and the balance Fe and inevitable impurity elements. The preparation method is simple in process and low in production cost; and the prepared steel plate is excellent in comprehensive mechanical performance and corrosion resistance, is better in welding performance and forming performance, and satisfies the requirements of the vehicle industry on such aspects as strength and corrosion resistance of high-strength steel.
Description
Technical field
The present invention relates to a kind of composition and the preparation method with the strong dual phase sheet steel of automobile cold-rolled superelevation of excellent corrosion resistance, belong to metal material field, particularly relate to automobile steel and produce and applied technical field.
Background technology
Along with the increase of China's economic situation downstream pressure, steel industry nip in the air as Chinese manufacturing basis is gradually dense, common iron production capacity is seriously superfluous, price continues to drop, but high-quality steel but still need import, this " strong greatly and not " has become the obvious characteristic of China's development of iron & steel industry, and a lot of high-end steel grade agricultural technology problem needs solution badly.
Dual phase steel is as the one of automobile with advanced high-strength steel, receive much concern because it has excellent strong plasticity, low yield tensile ratio, high hardenability value and good forming property, also because its alloy content is relatively less, there is excellent welding property and low cost.For a period of time, people have carried out a large amount of new varieties and research work to dual phase steel, and the dual phase steel maximum intensity commercially produced at present reaches 1200MPa level, and range of application constantly expands.In the alloying element commonly used, Al has remarkable effect to raising stabilization of austenite, but Al content higher (about 1.0 to 2.0%) in currently available technology, cause smelting castability significantly to reduce, be unfavorable for continuous seepage, herein Al content controlled below 0.025%.The present invention usually improves the comprehensive mechanical property of dual phase steel by adding a certain amount of Cr unit, and makes it have better corrosion resisting property, thus replaces part galvanized sheet, thus reduces production cost, and increase economic efficiency, this kind of trial still belongs to the first time.
CN104419878A discloses " having superhigh intensity cold rolling dual phase steel and the manufacture method thereof of weathering resistance ".The mass percentage of its chemical composition is: C:0.10% ~ 0.16%, Si:0.10% ~ 0.50%, Mn:1.4% ~ 2.2%, Cr:0.30% ~ 0.79%, Ni:0.08% ~ 0.20%, Cu:0.20% ~ 0.50%, Nb:0.01% ~ 0.05%, Ti:0.02% ~ 0.05%, Al:0.015% ~ 0.045%, P≤0.020%, S≤0.007%, N≤0.008%, surplus is Fe and inevitable impurity.Yield strength can be obtained and reach more than 700MPa, more than tensile strength 800MPa, the superhigh intensity cold rolling dual phase steel with weathering resistance of unit elongation more than 5%.But this steel grade alloying element is more, and production cost is higher, and intensity is lower, and in addition, yield tensile ratio is higher, what be unfavorable for manufacturing in automobile component processes is stamping.In contrast, Steel Alloy constituent content of the present invention is few, and cost of alloy is low, and technique is simple, and main is that its tensile strength will exceed its 1000MPa nearly, excellent anti-corrosion performance.
CN104328348A discloses " 800MPa level cold-rolled biphase steel and production method thereof ".The mass percentage of its chemical composition is: C:0.14 ~ 0.17%, Si:0.45 ~ 0.55%, Mn:1.6 ~ 1.8%, Cr:0.55 ~ 0.65%, P :≤0.016%, S :≤0.008%, Als:0.02 ~ 0.05%, N :≤0.004%, surplus is Fe.Having produced tensile strength is 800 ~ 850MPa, and yield strength is 450 ~ 550MPa, and unit elongation is the cold-rolled biphase steel of 15 ~ 17%, and strength level reduces, and does not have corrosion resistance nature.
CN103469097A discloses " the corrosion-resistant tubing and casing of high strength martensitic ferrite diphasic stainless steel and manufacture method thereof ".Its chemical component weight per-cent is: C:0.05 ~ 0.10%, Si:0.1 ~ 0.4%, Mn:0.20 ~ 1.0%, below P:0.03%, below S:0.01%, Cr:13.5 ~ 15.0%, Ni:0.5 ~ 1.5%, Mo:0.2 ~ 1.0%, Nb:0.005 ~ 0.02%, N:0.01 ~ 0.10%, below O:0.004%, and meet Cr+1.5Mo+2Ni+16N >=17 and Ni+30 (C+N)+8Nb >=3.5, wherein Cr, Ni, Mo, Si, Nb, Mn, C, N is the weight percentage content of element, all the other are Fe and inevitable impurity, obtain the pipe for oil well use martensite seamless stainless steel of the excellent low-temperature flexibility having high strength that yield strength is 110ksi level and less than vTrs:-60 DEG C concurrently, but and the tensile strength of steel grade and other mechanical properties in unexposed involved embodiment.It belongs to stainless steel field, and its alloying element content is higher, high cost, and production technique and performance requriements are obviously different from steel of the present invention, is not also suitable for the manufacture of automobile component.
Herein by changing the Composition Design of traditional cold rolling high-strength steel, add by Cr element the strong dual phase steel of cold rolling superelevation developed and have corrosion resisting property, under two kinds of simulating atmospheric environments, steel of the present invention all shows excellent corrosion resistance nature.Present invention process is simple, and prepared steel plate has excellent comprehensive mechanical property and corrosion resistance nature, and the automobile component met under varying environment use the requirement to dual phase steel.The present invention is intended to, for useful experimental data accumulation is made in the research and development of the strong automobile steel of high-quality superelevation, change the strong automobile steel of superelevation simultaneously and only focus on intensity and ignore the present situation of its over-all properties.
Summary of the invention
The object of the present invention is to provide a kind of strong dual phase steel of cold rolling superelevation and preparation method thereof with low cost, good plasticity, low yield strength ratio, excellent corrosion resistance.
For achieving the above object, the strong dual phase steel of cold rolling superelevation designed by the present invention, concrete composition is 0.13% ~ 0.16%C, 1.8% ~ 2.0%Si, 2.3% ~ 2.5%Mn, 1.8% ~ 2.2%Cr, 0.010% ~ 0.025%Al, 0.001% ~ 0.008%S, 0.002% ~ 0.012%P, 0.001% ~ 0.004%N, all the other are Fe and inevitable impurity element.
The cold rolling super-high strength steel that the present invention relates to, adopt vacuum induction furnace smelting, its manufacture method comprises the following steps:
Carry out smelting and casting according to mentioned component, be met the steel billet of above-mentioned chemical composition, steel billet is cooled to room temperature, stand-by as hot rolling raw material;
Described steel billet is heated to 1200 DEG C ~ 1250 DEG C with stove, insulation 2h, carry out hot rolling subsequently, the roughing start rolling temperature of described course of hot rolling is 1050 DEG C ~ 1110 DEG C, and finishing temperature is 840 DEG C ~ 880 DEG C, hot-rolled sheet total reduction is 80% ~ 90%, last percentage pass reduction is 20% ~ 30%, hot-rolled sheet is cooled to 630 DEG C ~ 680 DEG C and batches after finish to gauge terminates, and coiling temperature is 630 DEG C ~ 680 DEG C, batch rear insulation half an hour, with stove air cooling to room temperature;
Uncoiling of steel plate after described batching is carried out pickling and cold-rolling, and described cold-rolled process need control cold rolling draft between 50% ~ 80%, obtains cold-rolled steel sheet;
Described cold-rolled steel sheet is carried out continuous annealing, preheating section is heated to 100 DEG C ~ 200 DEG C with the rate of heating of 6.0 DEG C/s ~ 10.0 DEG C/s, steel plate is heated to two-phase region is incubated with the 2.0 DEG C/s ~ 5.0 DEG C/rate of heating of s afterwards, holding temperature is 760 DEG C ~ 820 DEG C, soaking time is 160s ~ 190s, then with the speed of cooling of 4 DEG C/s ~ 8 DEG C/s by steel plate slow cooling to 620 DEG C ~ 650 DEG C, with the speed of cooling of 35 DEG C/s ~ 50 DEG C/s, steel plate is chilled to 250 DEG C ~ 270 DEG C soon more subsequently, Wetted constructures 300s ~ 400s, then with the speed of cooling of 3 DEG C/s ~ 8 DEG C/s by steel plate slow cooling to room temperature.
Preferably, the start rolling temperature in described course of hot rolling is 1070 DEG C ~ 1100 DEG C, and finishing temperature is 815 ~ 835 DEG C, and the draft of last passage of hot rolling controls between 22% ~ 26%.
Preferably, described annealing holding temperature is 785 DEG C ~ 825 DEG C, and soaking time is 165s ~ 185s.Be chilled to 255 DEG C ~ 265 DEG C soon with 38 DEG C/s ~ 45 DEG C/s cooling rate subsequently, Wetted constructures 320s ~ 380s, slow cooling is to room temperature subsequently.
The tissue of this steel is mainly the ferrite of martensite and a small amount of Dispersed precipitate.
This steel has good comprehensive mechanical property, Rp
0.2=1020 ~ 1100MPa, R
m=1600MPa ~ 1850MPa, A
50=4.55% ~ 9.50%, Rp
0.2/ R
m=0.52 ~ 0.65.
This dual phase steel has excellent corrosion resistance nature.When uniform corrosion total immersion test simulation industrial atmospheric environment, the corrosive fluid of employing is the NaHSO of 0.005mol/L
3solution (0.52g/L), the erosion rate of the steel of the present invention obtained is 0.17gm
-2h
-1, be obviously better than the 0.25gm of traditional dual phase steel DP780
-2h
-1; When neutral salt spray test simulated marine atmosphere environment, the corrosive fluid of employing is the NaCl solution of 50g/L ± 5g/L, obtains the erosion rate of steel of the present invention within 96h and the 144h test period and is respectively 1.26gm
-2h
-1and 1.11gm
-2h
-1, be obviously better than the 1.87gm that traditional dual phase steel DP780 is corresponding
-2h
-1and 1.90gm
-2h
-1erosion rate.
Beneficial effect of the present invention
(1) alloying constituent of the present invention only has basic C, Si, Mn and a certain amount of Cr element, and by rational technology controlling and process, its mechanical property can reach Rp
0.2=1020 ~ 1100MPa, R
m=1600MPa ~ 1850MPa, A
50=4.55% ~ 9.50%, Rp
0.2/ R
m=0.52 ~ 0.65.
(2) the present invention takes low-temperature heat and hot rolling technology control techniques, effective refinement hot rolling microstructure.
(3) Mn content is controlled the scope 2.3% ~ 2.5% by the present invention, but can not be too high, middle manganese TRIP steel Mn content (5%<Mn%<8%) can not be exceeded, not only reduce cost, and improve processing performance, convenient test steel continuous casting and cold rolling.
(4) the present invention is by the reasonable interpolation of Cr element, effective refinement steel microscopic structure of the present invention, make steel of the present invention have corrosion resistance nature simultaneously, in simulation industrial atmospheric environment and atmospheric marine environment, all demonstrate the corrosion resistance nature more more superior than DP780.
Accompanying drawing explanation
Fig. 1 is the present embodiment steel hot rolling technology.
Fig. 2 is the present embodiment steel heat treatment process.
Fig. 3 is the present embodiment steel neutral salt spray test 96h test period erosion profile photomacrograph (96h test period erosion profile photomacrograph (a) steel (b) DP780 of the present invention steel, as Fig. 3).
Fig. 4 is the present embodiment steel neutral salt spray test 96h test period erosion profile SEM photo (96h test period erosion profile SEM photo (a) steel (b) DP780 of the present invention steel, as Fig. 4).
Fig. 5 is the present embodiment steel neutral salt spray test 144h test period erosion profile photomacrograph (144h test period erosion profile photomacrograph (a) steel (b) DP780 of the present invention steel, as Fig. 5).
Fig. 6 is the present embodiment steel neutral salt spray test 144h test period erosion profile SEM photo (144h test period erosion profile SEM photo (a) steel (b) DP780 of the present invention steel, as Fig. 6).
Embodiment
Below in conjunction with specific embodiment, technical scheme of the present invention is described further.
The embodiment of the present invention is a kind of strong dual phase steel of automobile cold-rolled superelevation with corrosion resistance nature, and its Ingredient percent is in table 1, and all the other are iron and inevitable impurity.
Table 1 specific embodiment steel chemical composition (mass percent, %)
Test steel strand is cooled to room temperature after smelting, then by blank heating to 1200 DEG C, be incubated 2 hours, 1100 DEG C of open rollings, obtain through six passage hot rollings the hot-rolled sheet that thickness is 2mm ~ 4mm, the draft of last passage is 25%, and finishing temperature is 850 DEG C ~ 880 DEG C, water-cooled to 640 ~ 660 DEG C are incubated half an hour afterwards, batch with the cold simulation of stove.Pickling is removed the hot-rolled sheet of surface oxide layer, four roller two-stand mills carry out cold rolling, draft is 50% ~ 70%, and the thickness finally obtaining cold-reduced sheet is 0.8mm ~ 1.5mm.Cold rolling rear steel plate is annealed on continuous annealing machine, and annealing process as shown in Figure 2.
The annealing process of embodiment 1 (composition 1) is, preheating section is heated to 150 DEG C with 7.4 DEG C/s, heating zone is heated to two-phase region holding temperature 800 DEG C with 2.6 DEG C/s, two-phase region insulation 180s, then in slow cooling section slow cooling to 640 DEG C, be chilled to 260 DEG C soon with 40 DEG C/s cooling rate subsequently, Wetted constructures 368s, slow cooling is to room temperature subsequently.
The annealing process of embodiment 2 (composition 2) is, preheating section is heated to 180 DEG C with 7.4 DEG C/s, heating zone is heated to two-phase region holding temperature 810 DEG C with 2.6 DEG C/s, two-phase region insulation 180s, then in slow cooling section slow cooling to 640 DEG C, be chilled to 250 DEG C soon with 40 DEG C/s cooling rate subsequently, Wetted constructures 320s, slow cooling is to room temperature subsequently.
The annealing process of embodiment 3 (composition 1) is, preheating section is heated to 150 DEG C with 7.4 DEG C/s, heating zone is heated to two-phase region holding temperature 820 DEG C with 2.6 DEG C/s, two-phase region insulation 180s, then in slow cooling section slow cooling to 620 DEG C, be chilled to 260 DEG C soon with 40 DEG C/s cooling rate subsequently, Wetted constructures 368s, slow cooling is to room temperature subsequently.
The present embodiment steel mechanical property is as shown in table 2, obtains Rp when wherein annealing temperature is 820 DEG C
0.2=1020MPa, R
m=1760MPa, A
50=8.06%, Rp
0.2/ R
mthe strong dual phase steel of cold rolling superelevation of=0.58.According to " metallic substance laboratory-uniform corrosion total immersion test method JB/T7901-2001 ", simulate industrial atmospheric environment by uniform corrosion total immersion test, adopt corrosive fluid to be the NaHSO of 0.005mol/L
3solution (0.52g/L), in the 130h test period, the erosion rate of steel of the present invention is 0.17gm
-2h
-1, be obviously better than the 0.25gm of DP780
-2h
-1; According to " artificial atmosphere corrosion test-salt-fog test GB/T10125-2012 ", carry out simulated marine atmosphere environment by neutral salt spray test, adopt concentration to be the NaCl solution of 50g/L ± 5g/L, within 96h and the 144h test period, erosion rate is respectively 1.26gm
-2h
-1, 1.11gm
-2h
-1, the erosion rate that in the identical test cycle, DP780 is corresponding is respectively 1.87gm
-2h
-1, 1.90gm
-2h
-1.Fig. 3, Fig. 4 are the present embodiment steel neutral salt spray test 96h test period erosion profile photomacrograph and SEM photo.Fig. 5, Fig. 6 are the present embodiment steel neutral salt spray test 144h test period erosion profile photomacrograph and SEM photo.
Table 2 the present embodiment steel mechanical property
The content be not described in detail in specification sheets of the present invention belongs to the known prior art of professional and technical personnel in the field.
The above is only the preferred embodiment of the present invention; it should be pointed out that for those skilled in the art, under the premise without departing from the principles of the invention; can also make some improvements and modifications, these improvements and modifications also should be considered as protection scope of the present invention.
Claims (7)
1. one kind has the strong dual phase sheet steel of automobile cold-rolled superelevation of corrosion resistance nature, it is characterized in that, the chemical composition (mass percent, %) of this steel plate is: 0.13% ~ 0.16%C, 1.8% ~ 2.0%Si, 2.3% ~ 2.5%Mn, 1.8% ~ 2.2%Cr, 0.010% ~ 0.025%Al, 0.001% ~ 0.008%S, 0.002% ~ 0.012%P, 0.001% ~ 0.004%N, all the other are Fe and inevitable impurity element.
2. the preparation method of dual phase sheet steel as claimed in claim 1, it is characterized in that, mentioned component carries out smelting and casting, and be met the steel billet of above-mentioned chemical composition, steel billet is cooled to room temperature, stand-by as hot rolling raw material;
Described steel billet is heated to 1200 DEG C ~ 1250 DEG C with stove, insulation 2h, carry out hot rolling subsequently, the roughing start rolling temperature of described course of hot rolling is 1050 DEG C ~ 1110 DEG C, and finishing temperature is 840 DEG C ~ 880 DEG C, hot-rolled sheet total reduction is 80% ~ 90%, last percentage pass reduction is 20% ~ 30%, hot-rolled sheet is cooled to 630 DEG C ~ 680 DEG C and batches after finish to gauge terminates, and coiling temperature is 630 DEG C ~ 680 DEG C, batch rear insulation half an hour, with stove air cooling to room temperature;
Uncoiling of steel plate after described batching is carried out pickling and cold-rolling, and described cold-rolled process need control cold rolling draft between 50% ~ 80%, obtains cold-rolled steel sheet;
Described cold-rolled steel sheet is carried out continuous annealing, preheating section is heated to 100 DEG C ~ 200 DEG C with the rate of heating of 6.0 DEG C/s ~ 10.0 DEG C/s, steel plate is heated to two-phase region is incubated with the 2.0 DEG C/s ~ 5.0 DEG C/rate of heating of s afterwards, holding temperature is 760 DEG C ~ 820 DEG C, soaking time is 160s ~ 190s, then with the speed of cooling of 4 DEG C/s ~ 8 DEG C/s by steel plate slow cooling to 620 DEG C ~ 650 DEG C, with the speed of cooling of 35 DEG C/s ~ 50 DEG C/s, steel plate is chilled to 250 DEG C ~ 270 DEG C soon more subsequently, Wetted constructures 300s ~ 400s, then with the speed of cooling of 3 DEG C/s ~ 8 DEG C/s by steel plate slow cooling to room temperature.
3. the preparation method of dual phase sheet steel as claimed in claim 2, is characterized in that: the start rolling temperature in described course of hot rolling is 1070 DEG C ~ 1100 DEG C, and finishing temperature is 815 ~ 835 DEG C, and the draft of last passage of hot rolling controls between 22% ~ 26%.
4. the preparation method of dual phase sheet steel as claimed in claim 2, is characterized in that: described annealing holding temperature is 785 DEG C ~ 825 DEG C, and soaking time is 165s ~ 185s.Be chilled to 255 DEG C ~ 265 DEG C soon with 38 DEG C/s ~ 45 DEG C/s cooling rate subsequently, Wetted constructures 320s ~ 380s, slow cooling is to room temperature subsequently.
5. the preparation method of dual phase sheet steel as claimed in claim 2, is characterized in that: the tissue of this steel is mainly the ferrite of martensite and a small amount of Dispersed precipitate.
6. the preparation method of dual phase sheet steel as claimed in claim 2, is characterized in that: this steel has good comprehensive mechanical property, R
p0.2=1020 ~ 1100MPa, R
m=1600MPa ~ 1850MPa, A
50=4.55% ~ 9.50%, R
p0.2/ R
m=0.52 ~ 0.65.
7. the preparation method of dual phase sheet steel as claimed in claim 2, is characterized in that: this dual phase steel has excellent corrosion resistance nature.When uniform corrosion total immersion test simulation industrial atmospheric environment, the corrosive fluid of employing is the NaHSO of 0.005mol/L
3solution (0.52g/L), the erosion rate of the steel of the present invention obtained is 0.17gm
-2h
-1; When neutral salt spray test simulated marine atmosphere environment, the corrosive fluid of employing is the NaCl solution of 50g/L ± 5g/L, obtains the erosion rate of steel of the present invention within 96h and the 144h test period and is respectively 1.26gm
-2h
-1and 1.11gm
-2h
-1.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108018503A (en) * | 2017-11-28 | 2018-05-11 | 西安交通大学 | A kind of stratiform Ultra-fine Grained dual phase ferritic/martensite steel and preparation method thereof |
| CN108660369A (en) * | 2017-03-29 | 2018-10-16 | 鞍钢股份有限公司 | Tensile strength is more than the quenching partition cold-rolled steel sheet and production method of 1180MPa |
| CN110616303A (en) * | 2018-06-19 | 2019-12-27 | 宝山钢铁股份有限公司 | Manufacturing method of 980MPa grade or above cold-rolled or galvanized dual-phase steel plate |
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| CN108018503B (en) * | 2017-11-28 | 2020-03-31 | 西安交通大学 | Layered superfine crystal dual-phase ferrite/martensite steel and preparation method thereof |
| CN110616303A (en) * | 2018-06-19 | 2019-12-27 | 宝山钢铁股份有限公司 | Manufacturing method of 980MPa grade or above cold-rolled or galvanized dual-phase steel plate |
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