CN109797336B - Tubeless rim steel with thickness of 9-11 mm and production method thereof - Google Patents
Tubeless rim steel with thickness of 9-11 mm and production method thereof Download PDFInfo
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The tubeless rim steel with the thickness of 9-11 mm comprises the following components in percentage by weight: c: 0.040 to 0.063%, Si: 0.045-0.100%, Mn: 0.35-0.70%, P: less than or equal to 0.006 percent, S: less than or equal to 0.005 percent, O: less than or equal to 0.0020 percent, N: less than or equal to 0.0030 percent, Als: 0.035-0.065%; the production method comprises the following steps: smelting in a converter and then refining in an LF (ladle furnace); RH vacuum treatment; continuously casting and heating the casting blank; rough rolling; fine rolling; carrying out ultra-fast cooling; coiling; and (7) flattening. The invention not only ensures that the thickness specification is 9-11 mm, the yield strength under the material is more than or equal to 275MPa, the tensile strength is 370-470 MPa, and the elongation A50The impact energy Akv is more than or equal to 40 percent, the impact energy Akv is more than or equal to 175J at the temperature of minus 20 ℃, the transverse sample is 180 degrees after the material is flash butt welded, the bending core diameter d is 0a, the material is qualified, the fatigue strength is more than or equal to 140MPa, the cold forming precision is high, and the qualification rate is improved by at least 5 percent.
Description
Technical Field
The invention relates to hot rolled steel and a production method thereof, belongs to tubeless rim steel and a production method thereof, and particularly relates to tubeless rim steel with the thickness of 9-11 mm and a production method thereof.
Background
The structure of the wheel mainly comprises a spoke and a rim, and the spoke is generally produced by mechanical stamping, so that the spoke wheel steel is required to have good deep drawing performance, tensile forming performance and shearing edge tensile performance. The wheel rim is formed by rolling after flash butt welding, so that the wheel steel for the wheel rim is required to have good welding performance and post-welding forming performance, such as cold bending performance, fatigue performance and the like.
At present, the exploitation of various mineral resources and the construction of engineering projects provide a material foundation for the beautiful life of human beings, and greatly stimulate the requirements of engineering machinery vehicles and dump mining vehicles, because of special working environment and working state, the wheels of the engineering machinery vehicles and the wheels of the mining vehicles have the characteristics of large volume, heavy weight, complex forming and the like, and are generally made of thick hot rolled steel. On the other hand, the hot working generates a large amount of iron scale dust and heat radiation phenomena, which bring serious pollution to the environment, which is contrary to the development concept of environmental protection, energy conservation and consumption reduction. Therefore, the production of the hot-rolled wheel steel for cold forming can meet the requirements of the steel for the tubeless wheel rim of the engineering machinery vehicle and the steel for the tubeless wheel rim of the self-discharging mining vehicle, and is the key point for solving the problems.
After retrieval:
the Chinese patent publication No. CN 201711156024.6 discloses a high-strength thin-specification wheel steel with good fatigue resistance, which comprises the following components: 0.05 to 0.07%, Si: 0.15-0.30%, Mn: 1.40-1.60%, P: less than or equal to 0.008 percent, S: less than or equal to 0.002%, Als: 0.020 to 0.060%, Nb: 0.046-0.055%, and the balance of Fe and inevitable impurities. The manufacturing process comprises the steps of refining and Ca treatment in an LF furnace after smelting in a converter, heating and rolling a casting blank after continuous casting and forming, cooling and coiling in a quick-front and slow-rear cooling mode, finishing and post-processing.
Chinese patent publication No. CN 201610392108.9 discloses a thick steel for truck spokes and a preparation method thereof, wherein the steel comprises the following components: 0.07 to 0.10%, Si: 0.01 to 0.20%, Mn: 0.85-1.00%, P: 0.01% -0.025%, S: 0.01% -0.015%, Als: 0.010-0.050%, and the balance of Fe and inevitable impurities. The manufacturing process comprises molten iron desulphurization → converter smelting combined converting → deoxidation, alloying → small platform feeding Al wire behind the converter → LF refining heating → continuous casting → slab heating → high pressure water descaling → rough rolling → hot coil box coiling → finish rolling → laminar cooling → coiling → welding head and tail → acid cleaning → trimming → oil coating → finished product. The steel is special steel for spokes, has relatively high C content and high harmful impurities such as S, P and the like, and has adverse effects on the fatigue performance, the forming performance and other service performances of materials.
The tubeless rim steel produced by the invention has excellent forming performance, impact resistance and fatigue performance, and can be cold-formed aiming at the defect that the large rim with thick specification can only be formed by heating at the present stage, so that the processing energy consumption and cost are greatly reduced, the environmental pollution is reduced, and the tubeless rim steel produced by the invention has good impact resistance and fatigue performance which are necessary conditions for the harsh working condition requirements of the off-road wheels, and the problem that the wheel steel for the road at the present stage can not meet the use requirements of the harsh working condition is solved.
Disclosure of Invention
The invention aims to overcome the defects in the prior art and provide a novel high-strength high-elongation-percentage-A composite material which has the thickness specification of 9-11 mm, the yield strength of the material being more than or equal to 275MPa, the tensile strength of 370-470 MPa and the elongation percentage of A50Not less than 40%, and impact energy A at-20 deg.CkvThe transverse test piece is 180 degrees after flash butt welding, the bending diameter d is 0a, the fatigue strength is larger than or equal to 140MPa, the cold forming precision is high, the qualified rate is improved by at least 5%, and the tubeless rim steel is 9-11 mm thick and the production method thereof.
The measures for realizing the aim are as follows:
the tubeless rim steel with the thickness of 9-11 mm comprises the following components in percentage by weight: c: 0.040 to 0.063%, Si: 0.045-0.100%, Mn: 0.35-0.70%, P: less than or equal to 0.006 percent, S: less than or equal to 0.005 percent, O: less than or equal to 0.0020 percent, N: less than or equal to 0.0030 percent, Als: 0.035 to 0.065%, and the balance of Fe and inevitable impurities.
The method for producing the tubeless rim steel with the thickness of 9-11 mm comprises the following steps:
1) smelting in a converter, and then feeding the smelted product into an LF furnace for external refining;
2) carrying out RH vacuum treatment; controlling P in the molten steel to be less than or equal to 0.008 percent and S to be less than or equal to 0.005 percent when the vacuum treatment is finished, and controlling the vacuum treatment time to be not less than 20 min; (ii) a After the components are finely adjusted, calcium treatment is carried out, Si-Ca wires are fed according to 650-850 g/ton steel,
the feeding rate is controlled to be 260-320 m/min;
3) heating the casting blank by continuous casting blank forming, wherein the heating temperature is controlled to be 1170-1230 ℃;
4) rough rolling is carried out, and the finishing temperature is controlled to be 1040-1080 ℃;
5) carrying out finish rolling, and controlling the finish rolling temperature to be 810-840 ℃;
6) carrying out ultra-fast cooling, and cooling to the coiling temperature at the cooling speed of 160-200 ℃/s;
7) coiling: controlling the coiling temperature to be 510-540 ℃;
8) leveling: the leveling force is set to be 2.0-2.5%.
It is characterized in that: the slag in the LF external refining process comprises the following components in percentage by weight: CaO: 50% -55% of Al2O3：25％～28％、MgO：6％～8％、SiO2: 9-12%, TFe < 0.6%, and controlling the alkalinity R of the slag: 4.0 to 4.5.
The reason for the action and control of the components and the main process in the invention is as follows:
carbon: the steel is a solid solution strengthening element with very good strengthening effect and low price, and is also a main element influencing the toughness of the steel material, and the carbon is increased to improve the strength, but the toughness is reduced, so the steel is also unfavorable for the welding performance of the material. The application range of the steel grade is that parts for the tubeless wheel rim of the engineering machinery vehicle need to be subjected to stamping deformation processing to a greater degree, and in order to save energy and reduce consumption, avoid hot working process procedures and reduce the equipment and energy consumption cost of a heating furnace, the material required by the steel grade has good cold forming performance while meeting the strength requirement. If the carbon content is more than 0.063%, good cold formability of the material cannot be satisfied, and if the carbon content is less than 0.040%, the strength of the material cannot be satisfied. Therefore, the carbon content is limited to the range of 0.040 to 0.063%.
Silicon: the silicon has strong solid solution strengthening effect after being dissolved in ferrite, and the tensile strength of the hot rolled steel can be improved by 8.0-9.0 MPa and the yield strength can be improved by 4.0-5.0 MPa when 0.1 weight percent of silicon is added into the carbon steel. And the addition of trace Si element reduces the melting point of impurities such as alumina and the like when the rim part is subjected to flash butt welding, forms silicate oxide with lower melting point, quickly forms welding slag, and is removed in a slag skimming process, so that the welding seam quality of the rim is improved, the cold forming requirement of the material is ensured, but the adverse effect on the toughness and the surface quality is obviously increased after the silicon content exceeds 0.2%, particularly, a hot-rolled steel plate generates a red iron sheet, and pockmarks are left on the surface of the steel plate after acid cleaning to become a crack source in the wheel fatigue process, so the set Si content of the invention is 0.045-0.100%.
Manganese: manganese is the most effective element for improving the strength and toughness, so that the hardness and strength of ferrite and austenite in the steel are improved; the critical transformation temperature in the steel is reduced, the effect of refining pearlite is achieved, and the effect of indirectly improving the strength of the pearlite steel is also achieved; however, the addition of a large amount of manganese can adversely affect the component segregation of the product; and simultaneously is an element for improving the sensitivity coefficient of the welding crack. Therefore, the manganese content is limited to 0.35 to 0.70%.
Phosphorus: in order to avoid deterioration of cold press formability, toughness and fatigue property of the material due to phosphorus, the upper limit of the content is set to 0.006%, and therefore the content is controlled to 0.006% or less.
Sulfur: sulfur is a very harmful element. The sulfur in steel often exists in the form of manganese sulfide, and the sulfide inclusion is unfavorable for the fatigue property of steel, and the lower the sulfur content in steel, the better. Therefore, the sulfur content in steel is controlled to be less than 0.005%
Aluminum: adding a small amount of aluminum can refine crystal grains and improve impact toughness, and the aluminum can also play a role in deoxidation, and is a strong oxidizing forming element to form Al with oxygen in steel2O3Is removed during steel making. Too high aluminum can form too much Al core inclusion, the Al core inclusion has great damage to the fatigue performance of the steel for the wheel rim, and the steel for the wheel rim has to control the Al core inclusion. Therefore, the content of Als is limited to be 0.035-0.065%.
Oxygen and nitrogen: the elements which have adverse effects on the structure and performance of the hot rolled steel plate coil and the adverse effects on the burst rate and the microcrack rate of the steel for the wheel rim are strictly controlled. The invention therefore defines the oxygen content O: less than or equal to 0.0020 percent, and the nitrogen content N: less than or equal to 0.0030 percent.
According to the characteristic requirements of finished materials, the components and the content of the slag are controlled in the LF external refining process, and the alkalinity of the slag is controlled to be in the range of R: 4.0 to 4.5; in the LF external refining process, the influence of alkalinity on the sulfur content ratio is most obvious, and the influence on the viscosity of slag is great. The control of the alkalinity R value is favorable for improving the desulfurization capacity of the slag, can effectively carry out desulfurization, improves the mechanics of materials, such as application performances of fatigue performance, shock resistance and the like, can ensure that the slag has reasonable viscosity, improves the effective volume of a steel ladle, reduces the damage of scouring action on a steel ladle lining, reduces the production cost and increases the production efficiency and benefit.
And (3) RH furnace vacuum treatment: the vacuum degree is less than or equal to 6.5KPa, the circulating pure degassing time is not less than 12 minutes, and the vacuum time is not less than 20 minutes. After the components are finely adjusted, calcium treatment is carried out, 650-850 g/t of Si-Ca wire is fed into molten steel in each furnace according to weight, the feeding rate is controlled to be 260-320 m/min, because the wire feeding rate of the Si-Ca wire has great influence on the yield of the Si-Ca wire, the calcium treatment can improve the steel quality, and the calcium treatment enables Al to be treated2O3Transformation into low-melting-point substance 12 CaO. Al2O3Accelerating the floating of inclusions and reducing Al2O3Inclusion and removal of Al2O3The aluminum calcium carbonate is changed into spherical from a string shape without deformation and inclusion; calcium treatment converts sulfides (FeS and MnS) into spherical CaS, so that the impact toughness of the steel plate is greatly improved, and the anisotropy is greatly improved; the calcium treatment can also improve the mixed casting performance of molten steel and prevent the tundish stopper rod and the submerged nozzle from being coated with Al2O3And inclusion and blockage. Thereby reducing the production cost and improving the economic benefit.
Slab continuous casting: slab continuous casting: using anti-crack slab covering slag, and adopting a weak cooling mode in a continuous casting secondary cooling system to prevent cracks from being generated during slab casting; the temperature of the tundish is controlled at 1565 +/-30 ℃, the pulling speed is controlled at 1.45 +/-0.3M/min, the plate blank continuous casting adopts a whole-process protective casting process, the crystallizer adopts an electromagnetic stirring (M-EMS) technology, the currently used wheel steel material does not adopt the crystallizer electromagnetic stirring (M-EMS) technology, and a plurality of limitations are placed on the service performance of the material, so that the material cannot meet the use requirements of harsh service conditions, and further popularization and use of the material are limited. Through a large number of research experiments, the invention shows that the superheat degree of molten steel can be greatly reduced and the solidification time can be shortened by adopting a crystallizer electromagnetic stirring (M-EMS) technology, so that a wide and thin equiaxed crystal area is generated, forced convection is carried out at the solidification front, dendrites at the solidification front are broken, fragments of the dendrites are remelted, the temperature of the molten steel is reduced, an equiaxed crystal core is increased, the development of the columnar crystal front is blocked, and the wide equiaxed crystal area is formed. The stirring of the molten steel reduces the temperature gradient of the liquid core from outside to inside, and the surrounding crystallization develops uniformly, thereby improving the equiaxial crystal rate on the section of the casting blank, enabling the segregation elements to be distributed uniformly, avoiding the aggregation of solute elements, finally improving the segregation of the casting blank, and improving the comprehensive service performance such as the shock resistance of the material.
Controlling the heating of the casting blank: charging the cold blank into a furnace, wherein the temperature of a preheating section is 550-700 ℃, the preheating time is 70-100 min, the temperature of a first heating section is 1000-1100 ℃, the temperature of a first adding time is 30-50 min, the temperature of a second heating section is 1120-1230 ℃, the temperature of a second adding time is 40-55 min, and the temperature of a soaking section is 1170-1230 ℃; soaking time is 30-45 min, total heating time is controlled to be 170-250 min, the temperature difference between the same slabs is less than or equal to 30 ℃, the temperature of the slabs is uniform, elements are fully dissolved in solid solution, the thickness and the number of furnace-produced iron oxide scales are effectively controlled, and the product material with good surface quality is obtained.
The invention carries out high-pressure water descaling again after the first pass of finish rolling: is mainly formed by Fe in the tunnel furnace3O4The formed primary scale can be removed by a descaler at the inlet side of the vertical rolling mill in front of the roughing mill, so that the rough rolling descaling is set to be not less than five times, a large amount of secondary scale is still generated in the heat insulation conveying roller way and between the roller way and the descaler of the finishing mill, and the secondary scale is mainly made of Fe2O3、Fe3O4The method is characterized in that the method can be removed by a descaling machine in front of a finishing mill, so that the number of open descaling headers before finishing rolling is set to be not less than two, and the tertiary scale generated between a descaling box of the finishing mill and a finishing rolling stand of the finishing mill is difficult to remove, particularly, the FeO content of the scale generated between a descaling point and an F3 stand is high, so that an F1 stand rear descaling mode is designed, the descaling effect is ensured by F1 stand rear descaling, and the descaling water of the F1 stand is used for controlling the temperature of a finish rolling plate surface and reducing the generation of the tertiary scale, so that the better material surface quality is obtained, and due to the effect of F1 stand rear descaling, the abrasion consumption of the roller surface in the rolling process is reduced, and the surface roughness of a steel plate can be well controlled.
The invention controls the finishing temperature of finish rolling to be 810-840 ℃, because the deformation termination temperature has important influence on the steel structure in the hot working process, the higher the deformation termination temperature is, the stronger the tendency of grain aggregation and growth is, the coarser the obtained austenite grains are, therefore, the deformation termination temperature in the material forming process is reduced as much as possible, but is not lower than Ar3 generally, namely, the grain is refined by controlling the rolling control cooling means to improve the product quality, and the finishing temperature is controlled to be 810-840 ℃, so as to adapt to the rolling rhythm, rapidly roll, reduce the generation of cubic scale and obtain the product with high surface quality.
Laminar cooling adopts the mode of anterior segment ultrafast cooling, and the cooling rate is 160 ~ 200 ℃/s. The increase of the cooling rate can reduce Ar3, increase the phase transformation nucleus and inhibit the grain growth after the phase transformation, so that F grains are refined and the material is strengthened by fine grains.
According to research and analysis, the coiling temperature is controlled to be 520-550 ℃, the iron scale structure is divided into three layers, the layer of ferrous oxide (FeO) is closest to iron, when the temperature is lower than 570 ℃, the ferrous oxide (FeO) is in an unstable state, the content of the ferrous oxide (FeO) is increased along with the increase of the surface temperature of the steel plate, the temperature is higher than 700 ℃, and the content of the ferrous oxide (FeO) in the iron scale reaches 95%; ferroferric oxide (Fe)3O4) Is an intermediate layer of iron scale, and when the temperature is lower than 500 ℃, the iron scale is only made of ferroferric oxide (Fe)3O4) Single phase composition, temperature higher than 700 deg.C, ferroferric oxide (Fe)3O4) Ferrous oxide (FeO) begins to form and at very high temperatures, ferroferric oxide (Fe)3O4) Only accounts for 4 percent of the iron scale. Ferroferric oxide (Fe)3O4) Is a harder, more wear resistant phase; iron oxide (Fe)2O3) The outermost layer on the scale, which is usually present at high temperatures, typically represents only 1% of the thickness of the scale. Therefore, the coiling temperature is determined to be 550-590 ℃ through a large number of experiments and analytical researches, so that the method is favorable for further forming loose iron scale mainly with an FeO structure on the surface of the material, reducing the thickness of the iron scale and being favorable for subsequent processing and utilizationThe scale on the surface of the material is removed, so that the surface quality of the steel plate is improved, the surface quality of the product is improved, and the energy consumption can be reduced. In the prior art, the coiling temperature is controlled to be 630-650 ℃, the thickness of the iron scale is greatly increased due to the higher temperature, the subsequent processing of the material is more difficult, the labor cost, the process cost and the equipment burden are increased, the surface quality of the material is deteriorated along with the increase of the thickness of the iron scale and the difficulty in removal, the surface quality risk is increased, the overhigh coiling temperature and the difficulty in the subsequent process are increased, and the energy consumption is increased.
Leveling: the whole force is set to be 2.0-2.5%, the plastic deformation range of the material can be expanded, the yield platform of the material is eliminated, and the slip line is prevented from being generated during cold forming. Meanwhile, the elongation of the material in the rolling direction is ensured to be uniform, the plate shape and the surface quality of the material are adjusted, and the forming performance of the material is improved.
The metallographic structure of the invention is ferrite plus pearlite, and the grain size of the ferrite is 10.5 grade.
Compared with the prior art, the invention not only ensures that the thickness specification is 9-11 mm, the yield strength under the material is more than or equal to 275MPa, the tensile strength is 370-470 MPa, and the elongation A50Not less than 40%, and impact energy A at-20 deg.CkvThe material is flash butt welded to make the transverse test sample 180 deg. and the bending diameter d 0a qualified, so that the cold forming precision of the tubeless wheel rim with fatigue strength greater than 140MPa is high and the qualified rate is raised by at least 5%.
Drawings
FIG. 1 is a metallographic structure diagram of the present invention.
Detailed Description
The present invention is described in detail below:
table 1 is a list of values for each example and comparative example of the present invention;
table 2 is a table of the main process parameters of each example of the present invention and comparative example;
table 3 is a list of the performance test cases of the examples and comparative examples of the present invention;
table 4 shows the composition and percentage by weight of the slag of each example and comparative example of the present invention.
The embodiments of the invention are produced according to the following steps:
1) smelting in a converter, and then feeding the smelted product into an LF furnace for external refining;
2) carrying out RH vacuum treatment; controlling P in the molten steel to be less than or equal to 0.008 percent and S to be less than or equal to 0.005 percent when the vacuum treatment is finished, and controlling the vacuum treatment time to be not less than 20 min; (ii) a After the components are finely adjusted, calcium treatment is carried out, and Si-Ca wires are fed in per ton of steel according to 650-850 g, and the feeding rate is controlled at 260-320 m/min;
3) heating the casting blank by continuous casting blank forming, wherein the heating temperature is controlled to be 1170-1230 ℃;
4) rough rolling is carried out, and the finishing temperature is controlled to be 1040-1080 ℃;
5) carrying out finish rolling, and controlling the finish rolling temperature to be 810-840 ℃;
6) carrying out ultra-fast cooling, and cooling to the coiling temperature at the cooling speed of 160-200 ℃/s;
7) coiling: controlling the coiling temperature to be 510-540 ℃;
8) leveling: the leveling force is set to be 2.0-2.5%.
TABLE 1 list of chemical compositions (wt%) of inventive and comparative examples
TABLE 2 List of the main process parameters of the examples of the invention and the comparative examples
TABLE 3 Table of the results of mechanical Properties measurements of the examples of the invention and the comparative examples
TABLE 4 tabulated (wt%) list of composition and content of slag of each example of the invention and comparative example
As can be seen from Table 3, the material has good mechanical properties, good low-temperature impact properties and fatigue properties, can completely meet the performance use requirements of wheel steel, and particularly greatly improves the requirements on the material in the face of complex and variable practical working conditions, while the steel material of the invention can completely meet the requirements, in the use field of customers, tracking statistical analysis shows that the wheel rim manufactured by using the material of the invention has high precision of parts after cold forming, and according to statistics, the qualification rate is improved by at least 5% compared with the prior material. All the examples of the present invention were acceptable.
The above examples are merely preferred examples and are not intended to limit the embodiments of the present invention.
Claims (2)
1. The method for producing the tubeless rim steel with the thickness of 9-11 mm comprises the following steps:
1) smelting in a converter, and then feeding the smelted product into an LF furnace for external refining; argon blowing and stirring are adopted in the whole process of external refining in the LF furnace;
2) carrying out RH vacuum treatment; controlling P in the molten steel to be less than or equal to 0.008 percent and S to be less than or equal to 0.005 percent when the vacuum treatment is finished, and controlling the vacuum treatment time to be not less than 20 min; after the components are finely adjusted, calcium treatment is carried out, and Si-Ca wires are fed in per ton of steel according to 650-850 g, and the feeding rate is controlled at 260-320 m/min;
3) heating the casting blank by continuous casting blank forming, wherein the heating temperature is controlled to be 1170-1230 ℃;
4) rough rolling is carried out, and the finishing temperature is controlled to be 1040-1080 ℃;
5) carrying out finish rolling, and controlling the finish rolling temperature to be 810-840 ℃;
6) carrying out ultra-fast cooling, and cooling to the coiling temperature at the cooling speed of 160-200 ℃/s;
7) coiling: controlling the coiling temperature to be 510-540 ℃;
8) leveling: the leveling force is set to be 2.0-2.5%;
the tubeless rim steel with the thickness of 9-11 mm comprises the following components in percentage by weight: c: 0.040-0.059%
Si：0.045～0.100%，Mn：0.35～0.70%，P：≤0.006%，S：≤0.005%，O：≤0.0020%，
N: less than or equal to 0.0030 percent, Als: 0.035 to 0.065%, and the balance of Fe and inevitable impurities.
2. The method for producing the tubeless rim steel with the thickness of 9-11 mm according to claim 1, wherein the method comprises the following steps: the slag in the LF external refining process comprises the following components in percentage by weight: CaO: 50% -55% of Al2O3：25％～28％、MgO：6％～8％、SiO2: 9-12%, TFe < 0.6%, and controlling the alkalinity R of the slag: 4.0 to 4.5.
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| CN112226691B (en) * | 2020-09-30 | 2022-02-15 | 鞍钢股份有限公司 | Hot rolled steel plate for 1800 MPa-grade hot stamping wheel spoke and manufacturing method thereof |
| CN112267067B (en) * | 2020-09-30 | 2022-02-18 | 鞍钢股份有限公司 | Hot rolled steel plate for 2000 MPa-level hot stamping wheel rim and manufacturing method thereof |
| CN112267066B (en) * | 2020-09-30 | 2022-02-15 | 鞍钢股份有限公司 | Hot rolled steel plate for 1800 MPa-grade hot stamping wheel rim and manufacturing method thereof |
| CN112226690B (en) * | 2020-09-30 | 2022-02-15 | 鞍钢股份有限公司 | Pickled steel plate for 1800 MPa-level hot stamping wheel rim and manufacturing method thereof |
| CN112267065B (en) * | 2020-09-30 | 2022-02-15 | 鞍钢股份有限公司 | Pickled steel plate for 2000 MPa-level hot stamping wheel rim and manufacturing method thereof |
| CN112251669B (en) * | 2020-09-30 | 2022-02-18 | 鞍钢股份有限公司 | Hot rolled steel plate for 2000 MPa-level hot stamping wheel spoke and manufacturing method thereof |
| CN114559222A (en) * | 2022-03-21 | 2022-05-31 | 张家港今日精锻有限公司 | Method for manufacturing tubeless multi-piece wheel rim for off-highway automobile |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009280900A (en) * | 2008-04-21 | 2009-12-03 | Jfe Steel Corp | METHOD FOR PRODUCING HIGH-STRENGTH HOT-ROLLED STEEL SHEET HAVING 780 MPa OR MORE OF TENSILE STRENGTH |
| EP2799578A1 (en) * | 2011-12-27 | 2014-11-05 | JFE Steel Corporation | High-strength hot-rolled steel sheet and manufacturing method therefor |
| JP2017166008A (en) * | 2016-03-15 | 2017-09-21 | 新日鐵住金株式会社 | Hot rolled steel sheet and manufacturing method therefor |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102296230B (en) * | 2011-09-07 | 2014-04-30 | 柳州钢铁股份有限公司 | Hot rolled steel for vehicle wheel steel ring, and production process thereof |
| CN102787270B (en) * | 2012-08-22 | 2014-08-27 | 武汉钢铁(集团)公司 | Thin hot-rolled pickled steel with good formability and production method thereof |
| CN104032215B (en) * | 2014-05-30 | 2016-08-17 | 武汉钢铁(集团)公司 | 420MPa level steel for automobile wheel and production method thereof |
| CN104294144B (en) * | 2014-10-10 | 2017-01-18 | 武汉钢铁(集团)公司 | Steel for automobile rim having tensile strength equal to or greater than 380MPa and production method of steel |
| CN106636934A (en) * | 2016-11-17 | 2017-05-10 | 河钢股份有限公司承德分公司 | Wheel steel with tensile strength being at level of 590 MPa and production method |
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2019
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009280900A (en) * | 2008-04-21 | 2009-12-03 | Jfe Steel Corp | METHOD FOR PRODUCING HIGH-STRENGTH HOT-ROLLED STEEL SHEET HAVING 780 MPa OR MORE OF TENSILE STRENGTH |
| EP2799578A1 (en) * | 2011-12-27 | 2014-11-05 | JFE Steel Corporation | High-strength hot-rolled steel sheet and manufacturing method therefor |
| JP2017166008A (en) * | 2016-03-15 | 2017-09-21 | 新日鐵住金株式会社 | Hot rolled steel sheet and manufacturing method therefor |
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