CN113981319A - Low-alloy-cost high-strength steel for automobile wheels and preparation method thereof - Google Patents
Low-alloy-cost high-strength steel for automobile wheels and preparation method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 67
- 239000010959 steel Substances 0.000 title claims abstract description 67
- 238000002360 preparation method Methods 0.000 title claims abstract description 11
- 238000001816 cooling Methods 0.000 claims abstract description 24
- 238000005452 bending Methods 0.000 claims abstract description 11
- 238000012360 testing method Methods 0.000 claims abstract description 9
- 238000005098 hot rolling Methods 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000005096 rolling process Methods 0.000 claims description 54
- 238000010438 heat treatment Methods 0.000 claims description 21
- 229910045601 alloy Inorganic materials 0.000 claims description 17
- 239000000956 alloy Substances 0.000 claims description 17
- 238000004519 manufacturing process Methods 0.000 claims description 16
- 229910052799 carbon Inorganic materials 0.000 claims description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 9
- 238000003825 pressing Methods 0.000 claims description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims description 6
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 2
- 239000011574 phosphorus Substances 0.000 claims description 2
- 239000000306 component Substances 0.000 description 15
- 238000000034 method Methods 0.000 description 14
- 238000003466 welding Methods 0.000 description 11
- 239000000047 product Substances 0.000 description 10
- 238000005728 strengthening Methods 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000012545 processing Methods 0.000 description 7
- 239000000126 substance Substances 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- MWUXSHHQAYIFBG-UHFFFAOYSA-N Nitric oxide Chemical compound O=[N] MWUXSHHQAYIFBG-UHFFFAOYSA-N 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
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- 238000005204 segregation Methods 0.000 description 3
- 230000002159 abnormal effect Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 241000282414 Homo sapiens Species 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000008358 core component Substances 0.000 description 1
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- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
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- 229910052719 titanium Inorganic materials 0.000 description 1
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Classifications
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/02—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for lubricating, cooling, or cleaning
- B21B45/0203—Cooling
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- 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
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B2015/0057—Coiling the rolled product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2201/00—Special rolling modes
- B21B2201/06—Thermomechanical rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2261/00—Product parameters
- B21B2261/20—Temperature
Abstract
The invention discloses a low-alloy-cost high-strength steel for automobile wheels, which comprises the following components in percentage by weight: 0.15-0.20% of C, 0.20-0.30% of Si, 0.35-0.50% of Mn, less than or equal to 0.025% of P, less than or equal to 0.010% of S, 0.030-0.050% of Ti, 0.015-0.050% of Als, and the balance of Fe and inevitable impurities. The invention also discloses a preparation method of the low-alloy-cost high-strength steel for the automobile wheel, which comprises the steps of smelting the low-alloy-cost high-strength steel for the automobile wheel into a plate blank according to the components of the low-alloy-cost high-strength steel for the automobile wheel, and then sequentially carrying out hot rolling, coiling and cooling to obtain a finished product. The yield strength of the steel for the automobile wheel prepared by the components and the preparation method is more than or equal to 355MPa, the tensile strength is more than or equal to 540MPa, the elongation after fracture is more than or equal to 20 percent, and the 180-degree bending test D is 2a, so that excellent plasticity and bending performance are realized.
Description
Technical Field
The invention relates to the technical field of hot continuous rolling strip production, in particular to high-strength steel for automobile wheels with low alloy cost and a preparation method of the high-strength steel for the automobile wheels with low alloy cost.
Background
With the attention of human beings on the environment and resources, light weight, energy conservation, environmental protection, safety and low cost become new targets of the automobile manufacturing industry. The energy-saving effect brought by the weight reduction of the rotating parts such as the automobile wheels is 1.2-1.3 times that of the non-rotating parts, and meanwhile, the automobile wheels are important safety parts in an automobile running system and play roles in bearing, steering, driving, braking and the like, so that the technical development direction of the automobile wheels is to reduce the cost and the weight as far as possible on the premise of ensuring the reliability and the safety, and the demand on the steel for the automobile wheels with low cost and high strength is increasingly greater.
The Chinese patent application with publication number CN104611626A discloses a low-cost high-strength steel for automobile wheels and a production method thereof, and the steel comprises the following chemical components in percentage by weight: c: 0.07 to 0.10%, Si: 0.146-0.246%, Mn: 0.76 to 0.95 percent of the total weight of the alloy, less than or equal to 0.02 percent of P, less than or equal to 0.015 percent of S, and the balance of Fe and inevitable impurity elements. The product disclosed in the patent can realize the tensile strength of more than 440MPa and has lower strength.
The Chinese patent application with publication number CN107130178A discloses a 500 MPa-grade automobile high-strength wheel steel and a CSP process production method thereof, wherein the steel comprises the following chemical components in percentage by weight: c: 0.04-0.07%, Si is less than or equal to 0.30%, Mn: 0.80-1.00%, P is less than or equal to 0.015%, S is less than or equal to 0.010%, Nb: 0.02-0.03%, Als: 0.020 to 0.045%, and the balance of Fe and inevitable impurity elements. The product disclosed by the patent is added with high content of Mn and a certain amount of Nb, the alloy cost of the material is high, and the CSP production line is adopted for production, so that the production process is not suitable for the conventional hot continuous rolling production line.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: provided is a low-alloy-cost high-strength steel for automobile wheels.
In order to solve the technical problems, the invention adopts the technical scheme that: the high-strength automobile wheel steel with low alloy cost comprises the following components in percentage by weight: 0.15-0.20% of C, 0.20-0.30% of Si, 0.35-0.50% of Mn, less than or equal to 0.025% of P, less than or equal to 0.010% of S, 0.030-0.050% of Ti, 0.015-0.050% of Als, and the balance of Fe and inevitable impurities.
Further, the method comprises the following steps: the carbon equivalent CEV of the steel for the automobile wheel is less than or equal to 0.28 percent.
Further, the method comprises the following steps: the yield strength of the steel for the automobile wheel is more than or equal to 355MPa, the tensile strength is more than or equal to 540MPa, the elongation after fracture is more than or equal to 20 percent, and the 180-degree bending test D is 2 a.
Further, the method comprises the following steps: the thickness of the steel for the automobile wheel is 10.0-16.0 mm.
The invention also discloses a preparation method of the low-alloy-cost high-strength steel for the automobile wheel, which comprises the steps of smelting the components of the low-alloy-cost high-strength steel for the automobile wheel into a plate blank, and then sequentially carrying out hot rolling, coiling and cooling to obtain a finished product.
Further, the method comprises the following steps: the hot rolling step comprises heating, side pressing, rough rolling and finish rolling.
Further, the method comprises the following steps: the heating temperature in the heating step is 1180-1220 ℃, and the heating time is 180-400 min.
Further, the method comprises the following steps: in the rough rolling step, the pass reduction is more than or equal to 18%, the odd pass full length total phosphorus removal is carried out, and the thickness of the intermediate blank is 53-57 mm.
Further, the method comprises the following steps: in the finish rolling step, the start rolling temperature of finish rolling is not more than 1030 ℃, and the finish rolling temperature is 830-870 ℃.
Further, the method comprises the following steps: the coiling temperature in the coiling step is 580-620 ℃; and in the cooling step, laminar cooling is carried out in a two-section cooling mode, the intermediate temperature point is 660-700 ℃, and the isothermal time is 5 s.
The invention has the beneficial effects that: the invention reduces the carbon equivalent of the steel for the automobile wheel by controlling the contents of Si and Mn elements through a high-content cheap strengthening element C, further improves the strength of the steel for the automobile wheel by adding a certain amount of Ti element to exert the effects of fine grain strengthening and precipitation strengthening, simultaneously improves the welding performance of the product by adding Ti element to form precipitates in the welding process to inhibit the microstructure coarsening of a heat affected zone, and realizes the low cost, high strength and excellent welding performance of the steel for the automobile wheel. The yield strength of the steel for the automobile wheel prepared by the components and the preparation method is more than or equal to 355MPa, the tensile strength is more than or equal to 540MPa, the elongation after fracture is more than or equal to 20 percent, and the 180-degree bending test D is 2a, so that excellent plasticity and bending performance are realized.
Detailed Description
In order to facilitate understanding of the present invention, the present invention will be further described with reference to the following examples.
The invention discloses low-alloy-cost high-strength steel for automobile wheels, which comprises the following components in percentage by weight: 0.15-0.20% of C, 0.20-0.30% of Si, 0.35-0.50% of Mn, less than or equal to 0.025% of P, less than or equal to 0.010% of S, 0.030-0.050% of Ti, 0.015-0.050% of Als, and the balance of Fe and inevitable impurities.
The reason why the steel for high-strength automobile wheels with low alloy cost according to the present invention employs the above components and component ratios is as follows:
c is an effective strengthening element in steel, can be dissolved in a matrix to play a role of solid solution strengthening, can be combined with Ti to form carbide precipitated particles to play a role of fine grain strengthening and precipitation strengthening, improves the carbon content, and is favorable for improving the strength, but too high carbon content can form more large and thick brittle carbide particles in the steel, is unfavorable for plasticity and toughness, can form a segregation zone in the center of the steel plate due to too high carbon content, is unfavorable for bending property formability, and increases welding carbon equivalent and welding crack sensitivity index due to too high carbon content, so that welding processing is not facilitated; therefore, the value range of C in the invention is set to be 0.15-0.20%.
Si has higher solid solubility in steel, is beneficial to thinning rust layer tissues, reduces the integral corrosion rate of the steel and improves the toughness, but the scale removal is difficult during rolling due to the over-high content, and the welding performance is reduced. Therefore, the value range of Si in the invention is set to be 0.20-0.30%.
Mn has a strong solid solution strengthening effect, can obviously reduce the phase transition temperature of steel, refines the microstructure of the steel, is an important strengthening and toughening element, but when the content of Mn is excessive, a casting blank crack is easy to generate in the continuous casting process, and simultaneously, the core component segregation of a steel plate can be caused, and the welding performance of the steel can be reduced; therefore, the value range of Mn in the invention is set to be 0.35-0.50%.
P and S elements can generate adverse effects on the structure performance of the steel plate, the plasticity and the low-temperature toughness of the steel can be obviously reduced when the content of P is too high, and sulfide inclusions can be formed by S to deteriorate the performance of the steel; therefore, the value ranges of P and S are set to be less than or equal to 0.025 percent and less than or equal to 0.010 percent.
Ti (C, N) precipitates formed by Ti and C, N can effectively refine austenite grains, inhibit the coarsening of the structure of a coarse grain region in the welding process and simultaneously generate a precipitation strengthening effect, but micron-sized TiN is easily formed due to excessively high Ti content, so that the forming performance and the fatigue performance are reduced; therefore, the value range of Ti in the invention is set to be 0.030-0.050% of Ti.
Al is added into steel to play a role in deoxidation, and the steel quality can be improved, but the content of Al is too high, and nitrogen oxide is easy to precipitate at austenite grain boundaries to cause casting blank cracks to generate; therefore, the value range of Als is set to be 0.015-0.050%.
The thickness of the low-alloy-cost high-strength steel for automobile wheels prepared by adopting the components is 10.0-16.0 mm, the carbon equivalent CEV is less than or equal to 0.28%, the yield strength is greater than or equal to 355MPa, the tensile strength is greater than or equal to 540MPa, the elongation after fracture is greater than or equal to 20%, and the 180-degree bending test D is 2 a; low cost, high strength and excellent welding performance are realized.
The invention also discloses a preparation method of the low-alloy-cost high-strength steel for the automobile wheel, and when the low-alloy-cost high-strength steel for the automobile wheel is prepared, a plate blank is smelted according to the components of the low-alloy-cost high-strength steel for the automobile wheel, and then the steps of hot rolling, coiling and cooling are sequentially carried out to obtain a finished product of the low-alloy-cost high-strength steel for the automobile wheel.
In the step of hot rolling the slab, the hot rolling step includes heating, side pressing, rough rolling and finish rolling.
More specifically, in the heating step, the slab is heated to homogenize the cast structure and component segregation and to dissolve the alloy elements, but the problems of burning loss, overheating, overburning and the like can occur when the heating temperature is too high and the heating time is too long. Therefore, in the heating step, the heating temperature is set to be 1180-1220 ℃, and the heating time is set to be 180-400 min.
In the side pressing step, the side pressing is carried out on the steel billet by using a fixed-width press machine so as to realize the requirement of a user on the width of the steel strip, but the steel billet can form a bone-like shape due to overlarge side pressing amount, and the edge part is thickened too much, so that the pressing amount of the middle part of the plate blank is insufficient during subsequent rough rolling, the austenite in the thickness direction is not completely recrystallized, and a mixed crystal structure is generated; therefore, the side pressure of the fixed width press is set to be less than or equal to 120mm in the side pressure step.
Further specifically, in the rough rolling step, the rough rolling needs to reach enough deformation to ensure austenite recrystallization, refine austenite grains and prevent mixed crystal tissues, and the rough rolling descaling can fully remove iron scales and avoid the surface quality problem caused by pressing of the iron scales; if the intermediate slab thickness is too large, the rough rolling deformation amount may be insufficient and the finish rolling load increases, and if the intermediate slab thickness is too small, the finish rolling deformation amount may be insufficient. Therefore, in the invention, the rough rolling pass reduction in the rough rolling step is set to be more than or equal to 18%, the odd pass full-length descaling is carried out, and the thickness of the intermediate billet is 53-57 mm.
In the finish rolling step, if the start rolling temperature of finish rolling is too high, the deformation of the non-recrystallization region of austenite in the finish rolling process is insufficient, and the structure is not refined; if the finish rolling temperature is too low, the difference between the finish rolling temperature and the initial rolling temperature is too large, so that the cooling speed in the finish rolling process is too high, the risk of rolling of a plurality of racks in a two-phase region after finish rolling exists, and the comprehensive performance of a product is poor; if the finishing temperature is too high, the deformation of the unrecrystallized area is insufficient, which is not beneficial to the refining of the final structure. Therefore, in the invention, the initial rolling temperature of finish rolling in the finish rolling step is set to be less than or equal to 1030 ℃, and the final rolling temperature is set to be 830-870 ℃.
Specifically, in the coiling step, if the coiling temperature is too low, abnormal structures are generated due to too high cooling speed in the subsequent cooling process; if the coiling temperature is too high, the crystal grains become coarse, resulting in deterioration of the overall properties of the finished product. Therefore, the coiling temperature is set to be 580-620 ℃.
In the cooling step, the steel for the high-strength automobile wheel with low alloy cost has larger thickness, so that the abnormal phenomena of structures such as uneven structure in the thickness direction and the like caused by reddening during laminar cooling due to over-high cooling speed are avoided, and a two-section cooling mode is adopted, and an intermediate temperature point and isothermal time are finally set through industrial tests and verification. The method adopts a two-stage cooling mode, sets the intermediate temperature to be 660-700 ℃, and sets the isothermal time to be 5 s.
Examples
To further understand the present invention, three examples of compositions and preparation methods of the steel for high strength automobile wheels using the low alloy cost steel of the present invention are provided, and the specific chemical compositions of the three examples are shown in table 1.
TABLE 1 chemical composition/% of examples
| C | Si | Mn | P | S | Ti | Als | |
| Example 1 | 0.17 | 0.23 | 0.44 | 0.013 | 0.003 | 0.033 | 0.047 |
| Example 2 | 0.18 | 0.22 | 0.41 | 0.013 | 0.002 | 0.040 | 0.028 |
| Example 3 | 0.18 | 0.25 | 0.40 | 0.009 | 0.006 | 0.048 | 0.033 |
The specific processing technology of the embodiment 1 comprises the following steps: processing the plate blank obtained by smelting according to the chemical components in the table 1, wherein the heating temperature is 1210 ℃, and the heating time is 200 min; the side pressure of the fixed width press is 100mm, the reduction of the rough rolling pass is more than or equal to 18 percent, the odd pass full-length scale removal is carried out, and the thickness of the intermediate blank is 56 mm; the initial rolling temperature of finish rolling is 1010-1030 ℃, the finishing temperature is 840-860 ℃, and the coiling temperature is 580-610 ℃; and carrying out laminar cooling after rolling, wherein a two-section cooling mode is adopted, the temperature of the middle point is 660-680 ℃, and the isothermal time is 5 s.
The specific processing technology of the embodiment 2 is as follows: processing the plate blank obtained by smelting according to the chemical components in the table 1, wherein the heating temperature is 1190 ℃, and the heating time is 250 min; the side pressure of the fixed width press is 100mm, the reduction of the rough rolling pass is more than or equal to 18 percent, the odd pass full-length scale removal is carried out, and the thickness of the intermediate blank is 55 mm; the initial rolling temperature of finish rolling is 1000-1020 ℃, the finishing temperature is 830-850 ℃, and the coiling temperature is 590-610 ℃; and carrying out laminar cooling after rolling, wherein a two-section cooling mode is adopted, the temperature of the middle point is 670-680 ℃, and the isothermal time is 5 s.
The specific processing technology of the embodiment 3 is as follows: processing the plate blank obtained by smelting according to the chemical components in the table 1, wherein the heating temperature is 1200 ℃, and the heating time is 230 min; the side pressure of the fixed width press is 110mm, the reduction of the rough rolling pass is more than or equal to 18 percent, the full-length scale removal of the odd pass is carried out, and the thickness of the intermediate blank is 55 mm; the initial rolling temperature of finish rolling is 1000-1030 ℃, the finishing temperature is 850-870 ℃, and the coiling temperature is 590-620 ℃; and carrying out laminar cooling after rolling, wherein a two-section cooling mode is adopted, the temperature of the middle point is 670-690 ℃, and the isothermal time is 5 s.
The finished products prepared by the three groups of examples are subjected to performance tests, and the specific mechanical property and bending property test results are shown in table 2.
Table 2 results of performance testing of examples
| Thickness/mm | Yield strength/MPa | Tensile strength/MPa | Elongation after break/% | 180 degree bend test | |
| Example 1 | 10.0 | 445 | 578 | 26.0 | D is 2a qualified |
| Example 2 | 12.5 | 416 | 562 | 24.0 | D is 2a qualified |
| Example 3 | 16.0 | 396 | 562 | 25.0 | D is 2a qualified |
Note 1: in Table 2, D is the bending indenter diameter and a is the specimen thickness
According to the performance test results of the three groups of embodiments obtained in the table 2, the low-alloy-cost high-strength steel for automobile wheels and the preparation method thereof disclosed by the invention have the advantages that through reasonable alloy components and production process design, the high strength, good plasticity and bending performance and excellent welding performance of the product are realized, the alloy cost is obviously reduced, the production method of the product is simple, the production cost is low, the comprehensive performance is excellent, and the application prospect is good.
Claims (10)
1. The high-strength automobile wheel steel with low alloy cost is characterized in that: comprises the following components in percentage by weight: 0.15-0.20% of C, 0.20-0.30% of Si, 0.35-0.50% of Mn, less than or equal to 0.025% of P, less than or equal to 0.010% of S, 0.030-0.050% of Ti, 0.015-0.050% of Als, and the balance of Fe and inevitable impurities.
2. The steel for a high-strength automobile wheel with low alloy cost according to claim 1, wherein: the carbon equivalent CEV of the steel for the automobile wheel is less than or equal to 0.28 percent.
3. The steel for a high-strength automobile wheel with low alloy cost according to claim 1, wherein: the yield strength of the steel for the automobile wheel is more than or equal to 355MPa, the tensile strength is more than or equal to 540MPa, the elongation after fracture is more than or equal to 20 percent, and the 180-degree bending test D is 2 a.
4. The steel for a high-strength automobile wheel with low alloy cost according to claim 1, wherein: the thickness of the steel for the automobile wheel is 10.0-16.0 mm.
5. The preparation method of the steel for the high-strength automobile wheel with low alloy cost is characterized by comprising the following steps of: the steel for a high-strength automobile wheel having a low alloy cost according to any one of claims 1 to 4, which is produced by smelting a slab, and then subjecting the slab to the steps of hot rolling, coiling and cooling in this order to obtain a finished product.
6. The method for producing a low-alloy-cost high-strength steel for automobile wheels according to claim 5, wherein: the hot rolling step comprises heating, side pressing, rough rolling and finish rolling.
7. The method for producing a low-alloy-cost high-strength steel for automobile wheels according to claim 6, wherein: the heating temperature in the heating step is 1180-1220 ℃, and the heating time is 180-400 min.
8. The method for producing a low-alloy-cost high-strength steel for automobile wheels according to claim 6, wherein: in the rough rolling step, the pass reduction is more than or equal to 18%, the odd pass full length total phosphorus removal is carried out, and the thickness of the intermediate blank is 53-57 mm.
9. The method for producing a low-alloy-cost high-strength steel for automobile wheels according to claim 6, wherein: in the finish rolling step, the start rolling temperature of finish rolling is not more than 1030 ℃, and the finish rolling temperature is 830-870 ℃.
10. The method for producing a low-alloy-cost high-strength steel for automobile wheels according to claim 5, wherein: the coiling temperature in the coiling step is 580-620 ℃; and in the cooling step, laminar cooling is carried out in a two-section cooling mode, the intermediate temperature point is 660-700 ℃, and the isothermal time is 5 s.
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Application publication date: 20220128 |