CN117327984A - Low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment - Google Patents

Low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment Download PDF

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CN117327984A
CN117327984A CN202311383537.6A CN202311383537A CN117327984A CN 117327984 A CN117327984 A CN 117327984A CN 202311383537 A CN202311383537 A CN 202311383537A CN 117327984 A CN117327984 A CN 117327984A
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equal
less
steel
strength
percent
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CN202311383537.6A
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Chinese (zh)
Inventor
宿成
刘妍
张智刚
刘广涛
张文录
温新峰
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Baotou Iron and Steel Group Co Ltd
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Baotou Iron and Steel Group Co Ltd
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Priority to CN202311383537.6A priority Critical patent/CN117327984A/en
Publication of CN117327984A publication Critical patent/CN117327984A/en
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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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C22C33/06—Making ferrous alloys by melting using master alloys
    • 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
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/009—Pearlite

Abstract

The invention discloses a low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment, which adopts the design thought of C-Si-Mn-Ti components, and utilizes the synergistic effect of solid solution strengthening elements Mn and Si and fine crystal strengthening and precipitation strengthening elements Ti to jointly improve the toughness of the material so as to avoid heat preservation coverThe mechanical property of the processed low-cost mode is more than or equal to 600MPa, the tensile strength is more than or equal to 700MPa, and the elongation A is obtained 50 More than or equal to 18 percent; impact properties at-20℃satisfy AKv 2 High-strength 700 MPa-grade automobile steel belt with the strength of more than or equal to 100J.

Description

Low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment
Technical Field
The invention belongs to the field of metallurgical materials, and particularly relates to a low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment.
Background
In recent years, with the increasing strength of national energy conservation and emission reduction requirements, the strength requirements of end users in various industries on steel materials are higher and higher to meet the reduction development trend, so that the development and application fields of high-strength steel are wider and wider, the commercial vehicle weight reduction target is clearly proposed by China automobile engineering society in 2016, and the weight is reduced by 35% in 2035. High-strength steel above 700MPa grade is gradually becoming the main material of structural members such as automobile girders, carriage bodies, axles and the like. How to produce high-quality high-strength steel with high efficiency and low cost becomes a research focus and a hot spot of steel materials. The low-alloy high-strength steel for mature research and application mainly adopts solid solution strengthening, fine grain strengthening, tissue strengthening and the like as main means, and the added alloy elements mainly comprise Mn, cr, nb, ti, V, cu, mo and the like and mainly adopt acicular ferrite and low-carbon bainite. The addition of noble alloy elements results in higher product cost, which affects the batch application and popularization of the high-strength steel to a certain extent. How to utilize relatively cheap micro-alloy element Ti, by reasonably controlling the content of key component element C, S, N and the process parameters of controlled rolling and cooling, the precipitation strengthening effect of the alloy Ti is exerted, and the development of low-alloy high-strength steel with tensile strength of more than or equal to 700MPa mainly comprising acicular ferrite and polygonal ferrite is the target of the invention.
The patent document CN1962099A discloses a method for producing 700MPa grade high-strength weathering steel based on a thin slab continuous casting and rolling process by adopting Ti microalloying process, wherein the composition design system is C (0.03% -0.07%) -Si (0.30% -0.50%) -Mn (0.60% -1.60%) -P (.ltoreq.0.040%) -S (.ltoreq.0.008%) -Cu (0.20% -0.50%) -Cr (0.30% -0.70%) -Ni (0.15% -0.35%) -Ti (0.08% -0.14%) -Al (0.025% -0.040%), N is not more than 0.0080 and the balance Fe. The production process adopts a sheet billet continuous casting and rolling process to produce the sheet billet with the thickness of 60mm, the tapping temperature of 1100-1180 ℃, the FDT of 870-920 ℃, and the CT: 550-650 ℃. Belonging to a CSP technique of continuous casting and rolling of sheet billet.
The patent document CN 110616301A discloses a production method for improving the precipitation strengthening effect of Ti microalloyed hot rolled high strength steel on line, mainly discloses the addition amount of Ti as a microalloying element is 0.03-0.10wt%, the set coiling temperature of a steel coil is 500-700 ℃, the method is characterized in that after each hot rolled coil is uncoiled, a heat preservation cover is independently covered on line, the online heat preservation time of the steel coil is more than or equal to 60 minutes, and the precipitation strengthening effect of TiC is improved.
The literature 2050 finishing high-strength steel slow cooling process shallow analysis introduces a method for controlling the cooling process of high-strength steel coils such as BS600MC, BS700MC and the like in a warehouse by adopting a slow cooling wall so as to achieve the purposes of improving precipitation strengthening effect, internal stress distribution and plate shape quality.
The research and implementation of the construction scheme of the 620mm strip steel pit in the literature proposes that the temperature control cooling of the slow cooling pit is utilized to cool the variety steel coil for 48 hours in a slow cooling period, so that the whole temperature of the steel coil is uniform. However, in actual production, the slow cooling process cannot preserve heat of the steel coil in time, and meanwhile, the heat preservation effect is greatly influenced by the environment of a slow cooling area, and particularly, the effect of improving precipitation strengthening is difficult to achieve for Ti microalloyed hot rolled high-strength steel coils.
Disclosure of Invention
Aiming at the problems existing in the prior art, the invention provides a low-cost manufacturing method for developing high-strength steel for automobile structures with the thickness of 2-6 mm and the tensile strength of more than or equal to 700MPa based on 2250mm hot continuous rolling unit (casting blank heating-rough rolling-finish rolling-layer cooling-coiling-stacking slow cooling), which utilizes a controlled rolling and controlled cooling process to exert the functions of refining the structure of microalloy Ti in the casting blank solidification process, precipitation strengthening in the rolling process and precipitation strengthening in the coiling process of steel coil, and cooperates with solid solution strengthening elements Mn and Si to jointly improve the toughness of the material. The method is innovative, and develops the low-cost, easily-formed and high-rigidity high-strength steel for the automobile without heat preservation cover treatment around the material composition design fully playing the reinforcement effect of the low-cost Ti microalloy, the narrow-range control of C, S, N element in the smelting process and the TMCP temperature and deformation control strategy in the hot rolling stage. The material is mainly applied to high-strength structural steel such as commercial vehicle girders, carriage bodies and steam axles.
The invention is realized by the following technical scheme.
The invention provides a low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment, which is characterized by comprising the following chemical components in percentage by mass: 0.04 to 0.08 percent of C; si 0.05-0.20%; mn 1.00-1.50%; p is less than or equal to 0.015 percent; s is less than or equal to 0.005%; al is less than or equal to 0.040%; 0.070 to 0.100 percent of Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is less than or equal to 50ppm; the balance of Fe and unavoidable impurities;
the method comprises the following processes: smelting continuous casting process, rolling process and steel coil storage area stacking slow cooling process; wherein:
the smelting continuous casting process comprises the following steps: molten iron-converter smelting-LF refining-RH degassing-slab continuous casting; the converter smelting adopts KR pre-desulfurized molten iron, ferrosilicon, ferromanganese and ferrotitanium for deoxidization alloying, and argon blowing and stirring are carried out on the molten steel in the whole process; the vacuum degree is less than or equal to 2mbar, the deep vacuum time is more than or equal to 10min, and the superheat degree delta T is less than or equal to 30 ℃;
the rolling process comprises the following steps: slab heating, high-pressure water descaling, fixed-width press rolling, E1R1 roughing mill rolling, E2R2 roughing mill rolling, flying shear, high-pressure water descaling, F1-F7 finishing mill rolling, encryption type laminar cooling and coiling; the heating temperature of the plate blank is 1250+/-20 ℃; heating for 180-240 min; the rough rolling mode adopts 1+5, 3+3 or 3+5; intermediate blank thickness range: 35-45 mm; the initial rolling temperature of the finish rolling is 970-1100 ℃; the finish rolling temperature is 840-890 ℃, the coiling temperature is 560-620 ℃, and the cooling speed is 20-40 ℃/s;
stacking and slow cooling process for steel coil storage area: and (3) intensively stacking steel coils (more than or equal to 10 coils) with the same or similar coiling temperature range to form a slow cooling atmosphere, wherein the steel coils can be arranged into a single layer or a double layer, the interval between the transverse steel coils is controlled to be 50-100 mm, and meanwhile, a ventilation opening of a slow cooling area to be far away from a steel coil storage area is selected, the slow cooling time is kept to be more than or equal to 72 hours, and the slow cooling speed is 5-10 ℃/hour.
In some embodiments, the mechanical properties of the high-strength automotive steel satisfy a yield strength of greater than or equal to 600MPa, a tensile strength of greater than or equal to 700MPa, and an elongation A 50 More than or equal to 18 percent; impact properties at-20℃satisfy AKv 2 Not less than 100J (full size).
In some embodiments, the mechanical properties of the high-strength automotive steel satisfy a yield strength of greater than or equal to 660MPa, a tensile strength of greater than or equal to 730MPa, and an elongation A 50 More than or equal to 19 percent; impact properties at-20℃satisfy AKv 2 Not less than 155J (full size), yield ratio not less than 0.89 and not more than 0.93, and grain size not less than 11 grade.
In some embodiments, the metallographic structure of the high strength automotive steel is granular bainite, polygonal ferrite, and pearlite.
In some embodiments, the high-strength automotive steel comprises the following chemical components in percentage by mass: 0.07% of C; si 0.14%; mn 1.05%; p is 0.012%; s is 0.003%; alt 0.030%; 0.070 percent of Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is 44ppm; the balance of Fe and unavoidable impurities.
In some embodiments, the high-strength automotive steel comprises the following chemical components in percentage by mass: 0.08 percent of C; 0.15% of Si; mn 1.40%; p is 0.010%; s is 0.003%; alt is 0.025%; ti 0.080%; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is 40ppm; the balance of Fe and unavoidable impurities.
In some embodiments, the high-strength automotive steel comprises the following chemical components in percentage by mass: 0.07% of C; 0.18% of Si; mn 1.50%; p is 0.013 percent; s is 0.002%; alt is 0.032; 0.088% of Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is 38ppm; the balance of Fe and unavoidable impurities.
In some embodiments, the high-strength automotive steel comprises the following chemical components in percentage by mass: c0.075%; 0.15% of Si; mn 1.30%; p is 0.012%; s is 0.004%; alt 0.037%; 0.092% Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; 45ppm of N; the balance of Fe and unavoidable impurities.
In another aspect, the present invention provides a high strength automotive steel manufactured by the above method.
The invention has the advantages that: the invention utilizes the synergistic effect of solid solution strengthening elements Mn and Si and fine crystal strengthening and precipitation strengthening elements Ti to jointly improve the toughness of the material through the C-Si-Mn-Ti component design, adopts the controlled cooling process of a 2250mm hot rolling unit (casting blank heating-rough rolling-finish rolling-layer cooling-coiling-stacking slow cooling), designs the control scheme of a warehouse area steel belt slow cooling field, does not need to be specially provided with a heat preservation cover or a heat preservation pit, not only can reduce the manufacturing cost of the product and improve the production efficiency, but also can obtain the product with mechanical properties meeting yield strength of more than or equal to 600MPa, tensile strength of more than or equal to 700MPa and elongation A 50 More than or equal to 18 percent; impact properties at-20℃satisfy AKv 2 The high-strength 700 MPa-grade automobile steel strip with the thickness of more than or equal to 100J (full size) can be used for industrial production of 2250mm hot rolling production line, and has good popularization value. The product can be applied to automobile girders, carriage bodies and transmission shafts.
Drawings
FIG. 1 is a photograph showing a metallographic structure of a 700 MPa-grade high-strength steel for automobiles produced in example 3.
FIG. 2 is a photograph showing a metallographic structure of a 700 MPa-grade high-strength steel for automobiles produced in example 4.
Detailed Description
The following describes the invention in detail by way of specific examples, which are intended to aid in understanding the invention and are not intended to limit the invention.
1. Smelting of materials
1.1 component design: the design of the composition was carried out according to the thickness of the product, as shown in table 1.
Table 1: composition design (mass percent)
1.2 converter smelting: the pretreated molten iron (S is less than or equal to 0.003 percent) enters a converter, oxygen blowing decarburization and heating are carried out, ferrosilicon and ferromanganese are added in the later period of smelting for deoxidization alloying, P, S components are controlled, the peroxidation of molten steel is prevented, the tapping amount is controlled, steel slag is prevented from entering the molten steel, the tapping temperature is 1600-1650 ℃, the tapping P of the converter is less than or equal to 0.015 percent, and the S is less than or equal to 0.008 percent.
1.3 external refining: an LF+RH whole-process argon blowing process is adopted, a good reducing atmosphere is maintained in the refining process, al wires are adopted for deoxidation, ferromanganese is added in the late stage of LF for alloying, ferrotitanium is added in the late stage of RH vacuum treatment (the vacuum degree is less than or equal to 2mbar and the deep vacuum time is more than or equal to 10 min) for alloying, and calcium treatment is carried out after the alloying is finished, so that the molten steel N is ensured to be less than or equal to 50ppm.
1.4 slab continuous casting: the superheat degree delta T of the molten steel is less than or equal to 30 ℃ (20-30 ℃), and the pulling speed is controlled to be 0.90-1.10 m/min. Is matched with a dynamic soft reduction technology, and the straightening temperature is more than or equal to 920 ℃.
1.5 Whole process nitrogen control: the detection of N in molten steel is less than or equal to 50ppm, the scrap steel ratio is less than or equal to 85%, the tapping temperature of the converter is more than or equal to 1600 ℃, and the converter adopts bottom blowing argon stirring and cannot adopt a bottom blowing stirring mode of argon-nitrogen alternating switching. The ladle adopts argon evacuation treatment, argon is used for blowing the tundish for more than or equal to 10min before continuous casting and heat exchange, air in the ladle is discharged, and when the tundish is cast for 30t, the argon blowing pipe is taken out to reduce nitrogen absorption of molten steel, and the whole argon blowing protection casting is adopted in the normal casting process.
2. Controlled rolling and cooling process
The casting blank is heated by adopting a step-type heating furnace (the heating process is shown in table 2), rough rolling adopts single frames R1 and R2 for round trip rolling, rough rolling modes adopted by the rough rolling are 1+5, 3+3 and 3+5, finish rolling adopts F1-F7 continuous rolling processes, and a specific rolling and cooling control process is shown in table 3.
Table 2: casting blank heating system
Table 3: rolling schedule
3. Examples
3.1 according to the above smelting technical requirements, smelting casting blanks of Ti microalloy high-strength steel with the following components, wherein the specific components are shown in the following table 4.
Table 4: chemical composition of each example (mass percent:%)
3.2 design and hot rolling process according to the above components, the product performance index is shown in table 5. Test methods refer to GB/T228 and GB/T229.
Table 5: product Properties of examples
3.3 the metallographic structure of the product is granular bainite, polygonal ferrite and pearlite. The morphology is shown in fig. 1 and 2, wherein fig. 1 shows the metallographic structure of the product manufactured in example 3, and fig. 2 shows the metallographic structure of the product manufactured in example 4.
In conclusion, the product has the performance advantages of low cost control basis and high strength and toughness matching, can be popularized and applied to the field of automobile and engineering machinery light weight in batches, and meets the downstream market demand condition.
Finally, it should be noted that: the foregoing description is only a preferred embodiment of the present invention, and is not intended to limit the present invention, but although the present invention has been described in detail with reference to the foregoing embodiments, it will be apparent to those skilled in the art that modifications may be made to the technical solutions described in the foregoing embodiments, or that equivalents may be substituted for part of the technical features thereof. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.

Claims (9)

1. A low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment is characterized by comprising the following chemical components in percentage by mass: 0.04 to 0.08 percent of C; si 0.05-0.20%; mn 1.00-1.50%; p is less than or equal to 0.015 percent; s is less than or equal to 0.005%; al is less than or equal to 0.040%; 0.070 to 0.100 percent of Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is less than or equal to 50ppm; the balance of Fe and unavoidable impurities;
the method comprises the following processes: smelting continuous casting process, rolling process and steel coil storage area stacking slow cooling process; wherein:
the smelting continuous casting process comprises the following steps: molten iron-converter smelting-LF refining-RH degassing-slab continuous casting; the converter smelting adopts KR pre-desulfurized molten iron, ferrosilicon, ferromanganese and ferrotitanium for deoxidization alloying, and argon blowing and stirring are carried out on the molten steel in the whole process; the vacuum degree is less than or equal to 2mbar, the deep vacuum time is more than or equal to 10min, and the superheat degree delta T is less than or equal to 30 ℃;
the rolling process comprises the following steps: slab heating, high-pressure water descaling, fixed-width press rolling, E1R1 roughing mill rolling, E2R2 roughing mill rolling, flying shear, high-pressure water descaling, F1-F7 finishing mill rolling, encryption type laminar cooling and coiling; the heating temperature of the plate blank is 1250+/-20 ℃; heating for 180-240 min; the rough rolling mode adopts 1+5, 3+3 or 3+5; intermediate blank thickness range: 35-45 mm; the initial rolling temperature of the finish rolling is 970-1100 ℃; the finish rolling temperature is 840-890 ℃, the coiling temperature is 560-620 ℃, and the cooling speed is 20-40 ℃/s;
stacking and slow cooling process for steel coil storage area: and (3) intensively stacking steel coils (more than or equal to 10 coils) with the same or similar coiling temperature range to form a slow cooling atmosphere, wherein the steel coils can be arranged into a single layer or a double layer, the interval between the transverse steel coils is controlled to be 50-100 mm, and meanwhile, a ventilation opening of a slow cooling area to be far away from a steel coil storage area is selected, the slow cooling time is kept to be more than or equal to 72 hours, and the slow cooling speed is 5-10 ℃/hour.
2. The method according to claim 1, wherein the mechanical properties of the high-strength automotive steel satisfy a yield strength of not less than 600MPa, a tensile strength of not less than 700MPa, and an elongation A 50 More than or equal to 18 percent; impact properties at-20℃satisfy AKv 2 Not less than 100J (full size).
3. The method according to claim 2, wherein the mechanical properties of the high-strength automotive steel satisfy a yield strength of not less than 660MPa, a tensile strength of not less than 730MPa, an elongation a 50 More than or equal to 19 percent; impact properties at-20℃satisfy AKv 2 Not less than 155J (full size), yield ratio not less than 0.89 and not more than 0.93, and grain size not less than 11 grade.
4. The method of claim 1, wherein the metallurgical structure of the high strength automotive steel is granular bainite, polygonal ferrite, and pearlite.
5. The method according to any one of claims 1 to 4, wherein the high-strength automotive steel comprises the following chemical components in mass percent: 0.07% of C; si 0.14%; mn 1.05%; p is 0.012%; s is 0.003%; alt 0.030%; 0.070 percent of Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is 44ppm; the balance of Fe and unavoidable impurities.
6. The method according to any one of claims 1 to 4, wherein the high-strength automotive steel comprises the following chemical components in mass percent: 0.08 percent of C; 0.15% of Si; mn 1.40%; p is 0.010%; s is 0.003%; alt is 0.025%; ti 0.080%; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is 40ppm; the balance of Fe and unavoidable impurities.
7. The method according to any one of claims 1 to 4, wherein the high-strength automotive steel comprises the following chemical components in mass percent: 0.07% of C; 0.18% of Si; mn 1.50%; p is 0.013 percent; s is 0.002%; alt is 0.032; 0.088% of Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; n is 38ppm; the balance of Fe and unavoidable impurities.
8. The method according to any one of claims 1 to 4, wherein the high-strength automotive steel comprises the following chemical components in mass percent: c0.075%; 0.15% of Si; mn 1.30%; p is 0.012%; s is 0.004%; alt 0.037%; 0.092% Ti; h is less than or equal to 2.0ppm; o is less than or equal to 30ppm; 45ppm of N; the balance of Fe and unavoidable impurities.
9. A high strength automotive steel made by the method of any one of claims 1-8.
CN202311383537.6A 2023-10-24 2023-10-24 Low-cost method for manufacturing high-strength automobile steel by utilizing Ti microalloy precipitation strengthening without heat preservation cover treatment Pending CN117327984A (en)

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