CN116043118A - Ultra-high reaming performance 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof - Google Patents
Ultra-high reaming performance 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 81
- 239000010959 steel Substances 0.000 title claims abstract description 81
- 238000002360 preparation method Methods 0.000 title abstract description 8
- 238000000034 method Methods 0.000 claims abstract description 22
- 239000000126 substance Substances 0.000 claims abstract description 15
- 238000005098 hot rolling Methods 0.000 claims abstract description 14
- 238000003466 welding Methods 0.000 claims abstract description 13
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 239000002131 composite material Substances 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 32
- 229910000734 martensite Inorganic materials 0.000 claims description 29
- 229910000859 α-Fe Inorganic materials 0.000 claims description 28
- 238000001556 precipitation Methods 0.000 claims description 26
- 238000001816 cooling Methods 0.000 claims description 18
- 238000005097 cold rolling Methods 0.000 claims description 17
- 229910001566 austenite Inorganic materials 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 15
- 229910001563 bainite Inorganic materials 0.000 claims description 13
- 238000000137 annealing Methods 0.000 claims description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 10
- 238000003723 Smelting Methods 0.000 claims description 10
- 238000005096 rolling process Methods 0.000 claims description 10
- 238000010583 slow cooling Methods 0.000 claims description 10
- 239000010936 titanium Substances 0.000 claims description 10
- 239000010949 copper Substances 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 6
- 239000010955 niobium Substances 0.000 claims description 6
- 239000002253 acid Substances 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 238000005406 washing Methods 0.000 claims description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims 2
- 229910052758 niobium Inorganic materials 0.000 claims 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims 2
- 239000002244 precipitate Substances 0.000 claims 1
- 230000008569 process Effects 0.000 abstract description 14
- 238000004519 manufacturing process Methods 0.000 abstract description 6
- 230000001276 controlling effect Effects 0.000 abstract description 3
- 230000001105 regulatory effect Effects 0.000 abstract description 3
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 238000005728 strengthening Methods 0.000 description 6
- 229910052804 chromium Inorganic materials 0.000 description 5
- 150000002822 niobium compounds Chemical class 0.000 description 4
- 150000003609 titanium compounds Chemical class 0.000 description 4
- 239000000203 mixture Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000714 At alloy Inorganic materials 0.000 description 1
- 229910000885 Dual-phase steel Inorganic materials 0.000 description 1
- 206010016654 Fibrosis Diseases 0.000 description 1
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 125000004429 atom Chemical group 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000004761 fibrosis Effects 0.000 description 1
- 239000008397 galvanized steel Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 125000004433 nitrogen atom Chemical group N* 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/0226—Hot rolling
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- 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
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- 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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- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- 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
- C21D2211/002—Bainite
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- C21—METALLURGY OF IRON
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- 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
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Abstract
The invention relates to 980 MPa-grade hot dip galvanized composite steel with ultra-high reaming performance and a preparation method thereof, wherein the steel comprises the following chemical components: 0.05 to 0.1 percent of Mn:1.5 to 2.1 percent, si:0.1 to 0.3 percent, cr:0.4 to 1.0 percent of Mo, 0.4 to 1.0 percent of Mo; mn/Cr > 2, mn/Mo > 3; p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, ti:0.005% -0.015%, nb:0.025% -0.05%, cu:0.4 to 0.8 percent, and the balance of Fe and impurities. The high reaming performance of the complex phase steel is realized by regulating and controlling the hot rolling structure morphology and matching with the continuous galvanization process, the good welding performance of the complex phase steel is realized by component design and structure regulation, and the excellent surface quality of the complex phase steel is realized by integral regulation and control of the production process.
Description
Technical Field
The invention relates to the technical field of steel manufacturing for automobiles, in particular to 980 MPa-grade hot dip galvanized complex phase steel with ultrahigh reaming performance for new energy automobiles and a preparation method thereof.
Background
With the increasing severity of the automobile industry on light weight, safety and the like, galvanization and high strength become marks of high reinforcement and high end of automobiles in China. In the vehicle body structure designed by the project of 'ultra-light steel vehicle body-advanced vehicle concept', the proportion of high-strength steel with the tensile strength of 1000MPa is maximum, and the proportion is about 29-30% of the weight of the vehicle body. The high-strength steel above 1000MPa mainly comprises dual-phase steel, martensitic steel, complex phase steel, third-generation high-strength steel and the like. The complex phase steel has the characteristics of high strength and good flanging performance, and is suitable for roll forming in the automobile part forming process. The complex phase steel has higher energy absorption capacity, good mechanical property, forming property and welding property, is widely applied to the production of parts such as automobile chassis suspension parts, B columns, bumpers, seat sliding rails and the like, and has wide market prospect.
At present, the strength level of the complex phase steel produced internationally is mainly below 800MPa, the strength of a few complex phase steels can reach 1000MPa, but other force energy indexes such as surface quality, reaming performance and the like are not ideal, and the surface quality and the reaming performance directly influence the application and the forming capacity of the steel plate, so that the complex phase steel has important industrial application significance and value for further upgrading the surface quality and the reaming performance of the complex phase steel of 1000 MPa.
Chinese patent application publication No. CN104278194a discloses a "quenched and partitioned steel sheet with high strength and high plasticity" and a method for preparing the same. The method adopts a high C and high Si/Al component system, and the element C is used for stabilizing the residual austenite besides strengthening effect; the Si/Al element is used for inhibiting carbide precipitation and indirectly acts on stabilizing the residual austenite. The content of C in the components is 0.25-0.35 wt%, the content of Si is 0.8-1.2 wt% and the content of Al is 0.5-1.0 wt%. The tensile strength of the steel plate obtained after heat treatment is greater than 980MPa, the elongation is about 20%, but the reaming performance is lower.
Chinese patent application publication No. CN109576579 a discloses "980 MPa-grade cold-rolled steel sheet with high hole expansibility and higher elongation percentage and method for manufacturing the same". The annealing temperature is 820-870 ℃, the overaging temperature is 320-460 ℃, the overaging time is long (100-400 s), the hot dip galvanized product is not involved, and the structure is ferrite, bainite and martensite. The tensile strength of the steel plate obtained after heat treatment is greater than 980MPa, the yield strength is greater than 600MPa, the hole expansion rate is greater than or equal to 45%, and the elongation rate is greater than 11%.
The invention provides a 980 MPa-grade hot-dip galvanized composite steel with ultra-high reaming performance and a preparation method thereof, wherein the high reaming performance of the composite steel is realized by regulating and controlling the hot-rolled structure morphology and matching with a continuous galvanization process, the good welding performance of the composite steel is realized by component design and structure regulation, and the excellent surface quality of the composite steel is realized by regulating and controlling the whole production process.
In order to achieve the above purpose, the invention is realized by adopting the following technical scheme:
the hot dip galvanized composite steel with the ultra-high reaming performance of 980MPa grade comprises the following chemical components in percentage by mass: 0.05 to 0.1 percent of Mn:1.5 to 2.1 percent, si:0.1 to 0.5 percent, cr:0.4 to 1.0 percent of Mo, 0.4 to 1.0 percent of Mo; mn/Cr > 2, mn/Mo > 3; p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, ti:0.005% -0.025%, nb:0.025% -0.05%, cu:0.4 to 0.8 percent, and the balance of Fe and unavoidable impurities.
Further, the finished steel sheet structure includes ferrite, bainite, martensite, and carbide precipitation; wherein, the ferrite comprises ferrite in a critical zone and epitaxial ferrite, and the martensite comprises low-carbon martensite and high-carbon martensite; according to the volume percentage, the ferrite content of the critical zone is 5-20%, the ferrite content of the epitaxial zone is 5-10%, and the bainite content of the epitaxial zone is 45-55%; the content of the low-carbon martensite is 10% -15%, and the carbon content in the low-carbon martensite is less than 0.4%; the content of the high-carbon martensite is 2% -8%, and the carbon content in the high-carbon martensite is less than 0.8%; the average grain size of ferrite and prior austenite is 2-4 mu m.
Further, the finished steel plate structure comprises titanium compound precipitation, niobium compound precipitation and copper simple substance precipitation, wherein the titanium compound precipitation size is 30-50 nm, the niobium compound precipitation size is 20-30 nm, and the copper simple substance precipitation size is 5-15 nm.
Further, the tensile strength of the finished steel plate is over 980MPa, the yield strength is 700-850 MPa, the elongation is more than or equal to 12%, the hole expansion rate is more than or equal to 60%, the carbon equivalent C+1/6Mn is less than 0.4, and the welding current window is more than 2000mA.
The preparation method of the hot dip galvanized composite steel with the ultra-high reaming performance of 980MPa level comprises the working procedures of smelting, hot rolling, pickling, cold rolling, continuous annealing galvanization and finishing, and comprises the following specific procedures:
1) Smelting;
2) Hot rolling; the heating temperature is 1150-1300 ℃, the initial rolling temperature is 1080-1180 ℃, the final rolling temperature is 880-1030 ℃, and the coiling temperature is 450-500 ℃;
3) Acid washing;
4) Cold rolling; the cold rolling reduction is 40-58%;
5) Continuous annealing; heating to 740-790 ℃ for 80-150 s; the slow cooling temperature is 700-750 ℃, and the slow cooling speed is controlled to be 1-3 ℃/s; slowly cooling to 450-470 ℃ at a cooling rate of not less than 30 ℃/s, isothermally heating for 20-40 s, and finally cooling to room temperature at a cooling rate of more than 2 ℃/s;
6) Finishing; the finishing elongation is controlled to be 0.1% -0.4%.
Further, the thickness of the hot rolled steel sheet is 3.2 to 4.0mm.
Compared with the prior art, the invention has the beneficial effects that:
(1) The chemical components of the steel plate take C, mn as main elements, noble alloys such as Ni, V and the like are not added, and meanwhile, the content of C is lower than 0.1%, so that the laser welding and the resistance spot welding are adopted in the production and application processes;
(2) The structure distribution in the steel is more uniform, the hardness difference of each phase in the structure is effectively reduced, and the yield strength and the reaming performance of the steel plate are effectively improved;
(3) The purpose of combining good welding performance and high reaming performance is achieved through low-cost alloy design and scientific process design.
Drawings
FIG. 1 is a typical SEM photograph of the steel sheet produced in example 1 of the present invention.
Detailed Description
The invention relates to a 980 MPa-grade hot dip galvanized complex phase steel with ultra-high reaming performance, which comprises the following chemical components in percentage by mass: 0.05 to 0.1 percent of Mn:1.5 to 2.1 percent, si:0.1 to 0.5 percent, cr:0.4 to 1.0 percent of Mo, 0.4 to 1.0 percent of Mo; mn/Cr > 2, mn/Mo > 3; p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, ti:0.005% -0.025%, nb:0.025% -0.05%, cu:0.4 to 0.8 percent, and the balance of Fe and unavoidable impurities.
Further, the finished steel sheet structure includes ferrite, bainite, martensite, and carbide precipitation; wherein, the ferrite comprises ferrite in a critical zone and epitaxial ferrite, and the martensite comprises low-carbon martensite and high-carbon martensite; according to the volume percentage, the ferrite content of the critical zone is 5-20%, the ferrite content of the epitaxial zone is 5-10%, and the bainite content of the epitaxial zone is 45-55%; the content of the low-carbon martensite is 10% -15%, and the carbon content in the low-carbon martensite is less than 0.4%; the content of the high-carbon martensite is 2% -8%, and the carbon content in the high-carbon martensite is less than 0.8%; the average grain size of ferrite and prior austenite is 2-4 mu m.
Further, the finished steel plate structure comprises titanium compound precipitation, niobium compound precipitation and copper simple substance precipitation, wherein the titanium compound precipitation size is 30-50 nm, the niobium compound precipitation size is 20-30 nm, and the copper simple substance precipitation size is 5-15 nm.
Further, the tensile strength of the finished steel plate is over 980MPa, the yield strength is 700-850 MPa, the elongation is more than or equal to 12%, the hole expansion rate is more than or equal to 60%, the carbon equivalent C+1/6Mn is less than 0.4, and the welding current window is more than 2000mA.
The invention relates to a preparation method of 980 MPa-grade hot dip galvanized complex phase steel with ultra-high reaming performance, which comprises the following steps of smelting, hot rolling, pickling, cold rolling, continuous annealing, galvanizing and finishing:
1) Smelting;
2) Hot rolling; the heating temperature is 1150-1300 ℃, the initial rolling temperature is 1080-1180 ℃, the final rolling temperature is 880-1030 ℃, and the coiling temperature is 450-500 ℃;
3) Acid washing;
4) Cold rolling; the cold rolling reduction is 40-58%;
5) Continuous annealing; heating to 740-790 ℃ for 80-150 s; the slow cooling temperature is 700-750 ℃, and the slow cooling speed is controlled to be 1-3 ℃/s; slowly cooling to 450-470 ℃ at a cooling rate of not less than 30 ℃/s, isothermally heating for 20-40 s, and finally cooling to room temperature at a cooling rate of more than 2 ℃/s;
6) Finishing; the finishing elongation is controlled to be 0.1% -0.4%.
Further, the thickness of the hot rolled steel sheet is 3.2 to 4.0mm.
The chemical composition design reason of the 980 MPa-grade hot dip galvanized complex phase steel with the ultra-high reaming performance is as follows:
c: the C element is a traditional and economic strengthening element of low-carbon steel, but the excessive content of the C element can bring difficulty to smelting and welding, and the strength of the steel plate can hardly reach 980MPa when the content of the C element is too low. Therefore, the content of the C element is controlled to be about 0.08 percent, and the optimal range is 0.05 to 0.1 percent.
Si: si element is also a strengthening element, and it does not enter cementite during solid solution strengthening, and can suppress carbide precipitation. Meanwhile, si in the two-phase region can promote C to diffuse from ferrite to austenite, so that the effect of purifying ferrite is achieved. Therefore, the content of Si element is controlled to be 0.1-0.5%.
Mn/Cr: mn and Cr are solid solution strengthening elements and austenite stabilizing elements, and the addition of Mn and Cr can prevent the transformation from austenite to pearlite in the cooling process, so that the hardenability of the material is improved. When the Mn and Cr contents are too low, austenite stability is poor, resulting in insufficient strength of the steel sheet; and too high Mn and Cr contents can cause the segregation of P and S elements, thereby deteriorating the processability of the material.
Mo: the Mo and Cr are generally compounded and added with good effect.
Cu: the Cu element is a solid solution strengthening element, firstly plays a role in improving the strength, and secondly, cu can be separated out in a simple substance or compound form in the heat treatment process, so that the strength of the steel plate is improved.
Ti: ti can capture free N atoms in steel and plays a role of fixing N. Meanwhile, tiN can be separated out in the solidification process to play a role in pinning a grain boundary, and Ti (C, N) can be separated out in the hot rolling stage to play a role in pinning a prior austenite grain boundary and refining the prior austenite grains. Meanwhile, a small amount of Ti is precipitated in the continuous annealing stage to strengthen ferrite and bainite, but the effect of adding excessive Ti is limited and the cost is increased. Therefore, the Ti element content is controlled to be 0.0105% -0.025%.
Nb: nb element and C, N element can form Nb precipitation, and ferrite grains can be prevented from growing so as to refine the grains, and bainite transformation is accelerated, so that the formability of the steel plate is improved, and the content of Nb element is controlled in a proper range.
P: the P element is a harmful element in steel, and the lower the content is, the better. In view of cost, the invention controls the content of P element below 0.015%.
S: the S element is a harmful element in steel, and the lower the content is, the better. In view of cost, the invention controls the S element content below 0.005%.
The invention relates to a preparation method of 980 MPa-grade hot dip galvanized complex phase steel with ultra-high reaming performance, which comprises the following steps of smelting, hot rolling, pickling, cold rolling, continuous annealing, zinc plating, finishing and the like, and comprises the following specific steps:
1. smelting: smelting by a converter to obtain alloy components in accordance with the design range.
2. And (3) hot rolling:
(1) the heating temperature is controlled at 1150-1300 ℃, so that the Ti atom precipitation behavior is ensured, the good N fixing effect is achieved on the steel plate, the precipitation of Ti (C, N) is ensured, and the effects of pinning the prior austenite grain boundary and refining the prior austenite grain are achieved.
(2) The initial rolling temperature is controlled to 1080-1180 ℃, the final rolling temperature is controlled to 880-1030 ℃, the rolling temperature of a recrystallization zone is ensured, the dynamic recrystallization behavior of the prior austenite grains in the hot rolling stage is promoted, and the grains are refined.
(3) The coiling temperature is controlled between 450 and 500 ℃, so that enough bainite is obtained, the content of bainite and martensite is ensured to be more than 60%, and the grain refinement in the subsequent continuous annealing process is facilitated. The thickness of the hot rolled steel plate is 3.2-4.0 mm.
3. Acid washing: and (3) removing the oxide scales generated on the surface of the hot-rolled steel plate and ensuring the surface quality of the cold-rolled steel plate.
4. Cold rolling: the cold rolling reduction is 40% -58%, and the cold rolling reduction is more than 40% to promote tissue fibrosis in cold rolling configuration; the cold rolling reduction of less than 58% is to prevent excessive deformation resistance due to excessive cold rolling reduction, and it is difficult to roll to a target thickness.
5. Continuous annealing:
(1) heating isothermal temperature of 740-790 ℃, isothermal time of 80-150 s, slow cooling temperature of 700-750 ℃ and slow cooling speed of 1-3 ℃/s; after slow cooling, cooling to 450-470 ℃ at a cooling rate of not less than 30 ℃/s, isothermal cooling for 20-40 s, and finally cooling to room temperature at a cooling rate of more than 2 ℃/s.
6. And (3) finishing: the steel plate enters a finishing machine for plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.4%.
The action principle of the invention is as follows: firstly, the invention is designed aiming at alloy components, adopts a low-temperature coiling mode in a hot rolling stage, ensures that a hot rolled plate contains enough bainite and martensite with high dislocation density, and easily forms fine and uniform austenite and ferrite on a bainite and martensite matrix in the subsequent annealing process, thereby being beneficial to improving the strength of the steel plate. And secondly, a proper amount of Ti, nb and Cu elements are added into the alloy components, so that grains can be further refined, the nano-grade precipitation content is increased, the tissue deformation coordination capacity is improved, and the carbon equivalent of the steel plate with the same strength grade is reduced. Finally, the epitaxial ferrite with high alloy content and high hardness is obtained by matching with a corresponding slow cooling process, so that the hardness difference of each phase is reduced, and the welding performance and the forming performance of the steel plate are improved.
The following examples are given by way of illustration of detailed embodiments and specific procedures based on the technical scheme of the present invention, but the scope of the present invention is not limited to the following examples.
[ example ]
The chemical compositions of the example steels are shown in Table 1, the continuous casting and hot rolling process parameters of the example steels are shown in Table 2, the cold rolling and continuous annealing process parameters of the example steels are shown in Table 3, and the mechanical properties of the example steels are shown in Table 4.
A typical SEM photograph of the steel sheet produced in example 1 is shown in FIG. 1.
Table 1 chemical composition of steel, wt%
| Examples | C | Mn | Cr | Mo | Si | Cu | Ti | Nb | P | S |
| 1 | 0.10 | 1.7 | 0.4 | 0.4 | 0.4 | 0.6 | 0.02 | 0.025 | 0.010 | 0.005 |
| 2 | 0.08 | 1.9 | 0.4 | 0.5 | 0.2 | 0.4 | 0.01 | 0.03 | 0.012 | 0.005 |
| 3 | 0.05 | 2.0 | 0.6 | 0.4 | 0.5 | 0.5 | 0.015 | 0.04 | 0.010 | 0.003 |
| 4 | 0.09 | 1.8 | 0.7 | 0.4 | 0.4 | 0.5 | 0.01 | 0.025 | 0.008 | 0.003 |
| 5 | 0.07 | 1.9 | 0.4 | 0.6 | 0.5 | 0.4 | 0.01 | 0.035 | 0.009 | 0.005 |
| 6 | 0.08 | 1.9 | 0.5 | 0.5 | 0.2 | 0.5 | 0.015 | 0.025 | 0.007 | 0.005 |
| 7 | 0.09 | 1.7 | 0.5 | 0.4 | 0.4 | 0.7 | 0.015 | 0.05 | 0.01 | 0.004 |
| 8 | 0.1 | 1.6 | 0.6 | 0.4 | 0.2 | 0.4 | 0.01 | 0.03 | 0.013 | 0.005 |
Table 2 continuous casting and hot rolling process parameters of steel
| Examples | Heating temperature/. Degree.C | Initial rolling temperature/DEGC | Finishing temperature/°c | Coiling temperature/. Degree.C |
| 1 | 1175 | 1086 | 911 | 460 |
| 2 | 1294 | 1173 | 1015 | 470 |
| 3 | 1248 | 1154 | 1023 | 480 |
| 4 | 1256 | 1161 | 995 | 470 |
| 5 | 1186 | 1123 | 927 | 480 |
| 6 | 1239 | 1145 | 948 | 490 |
| 7 | 1233 | 1137 | 920 | 480 |
| 8 | 1221 | 1139 | 916 | 460 |
Table 3 galvanization process parameters of steel
Table 4 mechanical properties of steels
| Examples | Rp0.2/MPa | Rm/MPa | A50/％ | λ/％ | Welding current window/kA |
| 1 | 791 | 1021 | 12.4 | 61 | 2.3 |
| 2 | 787 | 1032 | 12.2 | 63 | 2.5 |
| 3 | 823 | 1057 | 12.6 | 66 | 3.5 |
| 4 | 817 | 1048 | 12.5 | 62 | 2.5 |
| 5 | 688 | 997 | 12.8 | 67 | 3.2 |
| 6 | 696 | 1026 | 12.1 | 61 | 3.1 |
| 7 | 754 | 1013 | 12.5 | 62 | 3.8 |
| 8 | 757 | 1025 | 12.5 | 65 | 2.9 |
In table 4, rp is yield strength, rm is tensile strength, a50 is elongation, and λ is hole expansion ratio.
According to the embodiment, the galvanized steel sheet is prepared through low-cost alloy design and ingenious process design, has tensile strength of 980MPa or more, yield strength of 650-850 MPa, elongation of 12% or more, reaming value of 60% or more, welding window of more than 2000mA, and meets the force energy index of combining good weldability and high formability.
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art, who is within the scope of the present invention, should make equivalent substitutions or modifications according to the technical scheme of the present invention and the inventive concept thereof, and should be covered by the scope of the present invention.
Claims (6)
1. The hot dip galvanized composite steel with the ultra-high reaming performance of 980MPa grade is characterized in that the steel comprises the following chemical components in percentage by mass: 0.05 to 0.1 percent of Mn:1.5 to 2.1 percent, si:0.1 to 0.5 percent, cr:0.4 to 1.0 percent of Mo, 0.4 to 1.0 percent of Mo; mn/Cr > 2, mn/Mo > 3; p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, ti:0.005% -0.025%, nb:0.025% -0.05%, cu:0.4 to 0.8 percent, and the balance of Fe and unavoidable impurities.
2. The ultra-high hole expansion 980MPa grade hot dip galvanized complex phase steel according to claim 1, wherein the finished steel sheet structure comprises ferrite, bainite, martensite and carbide precipitates; wherein, the ferrite comprises ferrite in a critical zone and epitaxial ferrite, and the martensite comprises low-carbon martensite and high-carbon martensite; according to the volume percentage, the ferrite content of the critical zone is 5-20%, the ferrite content of the epitaxial zone is 5-10%, and the bainite content of the epitaxial zone is 45-55%; the content of the low-carbon martensite is 10% -15%, and the carbon content in the low-carbon martensite is less than 0.4%; the content of the high-carbon martensite is 2% -8%, and the carbon content in the high-carbon martensite is less than 0.8%; the average grain size of ferrite and prior austenite is 2-4 mu m.
3. The ultra-high hole expansion 980MPa grade hot dip galvanized complex phase steel according to claim 1, wherein the finished steel sheet structure comprises titanium precipitation, niobium precipitation and copper simple substance precipitation, wherein the titanium precipitation size is 30-50 nm, the niobium precipitation size is 20-30 nm, and the copper simple substance precipitation size is 5-15 nm.
4. The ultra-high reaming performance 980MPa grade hot dip galvanized complex phase steel according to claim 1, wherein the tensile strength of the finished steel plate is over 980MPa, the yield strength is 700-850 MPa, the elongation is more than or equal to 12%, the reaming ratio is more than or equal to 60%, the carbon equivalent C+1/6Mn is less than 0.4, and the welding current window is more than 2000mA.
5. The method for preparing the hot dip galvanized complex phase steel with ultra-high reaming performance of 980MPa grade according to any one of claims 1 to 4, which is characterized by comprising the following steps of smelting, hot rolling, pickling, cold rolling, continuous deplating and finishing:
1) Smelting;
2) Hot rolling; the heating temperature is 1150-1300 ℃, the initial rolling temperature is 1080-1180 ℃, the final rolling temperature is 880-1030 ℃, and the coiling temperature is 450-500 ℃;
3) Acid washing;
4) Cold rolling; the cold rolling reduction is 40-58%;
5) Continuous annealing; heating to 740-790 ℃ for 80-150 s; the slow cooling temperature is 700-750 ℃, and the slow cooling speed is controlled to be 1-3 ℃/s; slowly cooling to 450-470 ℃ at a cooling rate of not less than 30 ℃/s, isothermally heating for 20-40 s, and finally cooling to room temperature at a cooling rate of more than 2 ℃/s;
6) Finishing; the finishing elongation is controlled to be 0.1% -0.4%.
6. The method for preparing the hot-dip galvanized complex phase steel with ultra-high reaming performance of 980MPa grade according to claim 5, wherein the thickness of the hot-rolled steel plate is 3.2-4.0 mm.
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