High-surface-quality and high-strength steel plate for passenger car chassis component and production method thereof

Abstract

The invention belongs to the field of metal materials, and particularly relates to a high-surface-quality and high-strength steel plate for a passenger car chassis component and a production method thereof. The steel comprises the following chemical components in percentage by weight: 0.68%-0.76% of Si, 0.68%-1.20% of Al, 1.0%-1.58% of Al / Si, and the balance of Fe and inevitable impurities, and further comprises the following components in percentage by weight: 0.68%-0.76% of Si, 0.68%-1.20% of Al, 1.0%-1.58% of Mo and the balance of Ce. According to the invention, the conventional component with higher Si content is adopted, the Si content does not need to be specially reduced, the smelting is easy, the cost is low, the surface quality is good, oxide scale stripes and chromatic aberration defects are avoided, and the surface roughness Ra is 1.33-1.70 microns.

Description

Technical Field

[0001] This invention belongs to the field of metallic materials, and specifically relates to a high-strength steel plate with high surface quality for passenger vehicle chassis components and its production method. Background Technology

[0002] With the rapid development of the automotive industry, the demands for lightweighting, safety, and cost reduction are increasing. Hot-rolled pickled steel sheet is made from high-quality hot-rolled coils through processes such as uncoiling, pickling, rinsing, drying, edge trimming, and oiling. Hot-rolled pickled steel sheet offers a high cost-performance ratio, falling between cold-rolled and hot-rolled steel sheets. Its surface quality and application requirements are between those of hot-rolled and cold-rolled steel sheets, making it an ideal substitute for some types of both. Hot-rolled pickled steel sheet is widely used in automotive chassis, wheels, and body structural parts. Currently, given the challenging steel market conditions, it is one of the most profitable products for steel companies, effectively reducing procurement costs while meeting user requirements.

[0003] Chinese patent application CN113549823B discloses a 900MPa grade hot-rolled pickled multiphase steel with low yield strength ratio and high porosity, and its production method. Its chemical composition by weight percentage is: C: 0.085%–0.162%, Si: 0.08%–0.85%, Mn: 1.15%–2.50%, Al: 0.10%–0.30%, Cr: 0.10%–0.75%, Mo: 0.08%–0.65%, Nb: 0.025%–0.070%, Ti: 0.030%–0.155%, B: 0.0020%–0.0050%, rare earth elements La+Ce: 0.010%–0.060%, with P ≤ 0.020% and S ≤ 0.007%, the balance being Fe and unavoidable impurities. Yield strength ≥ 590 MPa, tensile strength ≥ 900 MPa, elongation A80 ≥ 14%, yield strength ratio ≤ 0.70, and porosity ≥ 80%; requires special reduction of Si content, is not easy to smelt, has high cost, and is prone to oxidation streaks and color difference defects on the surface. In addition, it has low elongation after fracture, which does not meet the requirements of high surface quality and high strength passenger car chassis structural components.

[0004] Chinese patent application CN119351875A discloses a hot-rolled pickled multiphase steel with a tensile strength of 800 MPa and its manufacturing method. The chemical composition of the multiphase steel is C: 0.030-0.050%, Si: 0.15-0.20%, Mn: 1.30-1.50%, Cr: 1.30-1.50%, Al: 0.15-0.20%, S≤0.005%, P≤0.012%, Ti: 0.020-0.030%, B: 0.0015-0.0025%, N≤0.0040%, with the balance being Fe and unavoidable impurities. The multiphase steel provided by this invention has a yield strength ≥680 MPa, a tensile strength ≥800 MPa, an elongation ≥15%, a porosity ≥70%, and low crack sensitivity. The Si content is 0.15-0.20%, which requires special reduction of Si content. It is not easy to smelt, has high cost, and the surface quality is prone to oxidation streaks and color difference defects. In addition, the elongation after fracture is low, which does not meet the requirements of high surface quality and high strength passenger car chassis structural components. Summary of the Invention

[0005] To address the development needs in the automotive steel industry, this invention provides a high-strength steel plate with high surface quality for passenger vehicle chassis components and its production method. The steel plate has a yield strength of 680~760MPa, a tensile strength of 830~900MPa, a longitudinal elongation A≥24%, and meets the requirements for transverse cold bending at 180° D=a. It uses conventional components with relatively high Si content, eliminating the need for special Si content reduction, making it easy to smelt, low in cost, and with good surface quality, free of iron oxide scale streaks and color difference defects. The surface roughness Ra is 1.33~1.70μm.

[0006] To achieve the above objectives, the present invention employs the following technical solution: A high-strength steel plate with high surface quality for passenger vehicle chassis components, wherein the chemical composition of the steel by weight percentage is: C: 0.060%–0.095%, Si: 0.68%–0.76%, Mn: 1.55%–1.90%, Al: 0.68%–1.20%, Nb: 0.040%–0.060%, Ti: 0.090%–0.140%, Cr: 0.30%–0.45%, Mo: 0.10%–0.40%, Ce: 0.0070%–0.0150%, and Al / Si: 1.0–1.58, and P ≤ 0.010%, S ≤ 0.004%, N ≤ 0.003%, with the balance being Fe and unavoidable impurities.

[0007] The microstructure of the finished steel plate is 5%–10% ferrite, 83%–90% bainite, 1%–5% martensite, and 1%–2% retained austenite.

[0008] The steel plate has a yield strength of 680-760 MPa, a tensile strength of 830-900 MPa, a longitudinal elongation A ≥ 24%, and a transverse cold bend of 180° D = a (the diameter of the bending mandrel is equal to the thickness of the steel plate).

[0009] The surface roughness Ra of the steel plate is 1.33–1.70 μm. The roughness of the steel plate in this invention, while meeting the surface quality requirements for steel plates, can increase the frictional resistance during welding, which is beneficial for heat transfer and fusion during welding, improving weld quality. During spot welding, it can keep the contact resistance within a reasonable range, avoiding incomplete welds or burn-through due to poor contact, and improving weld strength and stability. It can also increase the friction coefficient of the friction surface, improving the anti-slip ability of the connection, thereby enhancing the overall stability of the structure.

[0010] The main function of the high surface quality, high strength steel plate composition for passenger vehicle chassis components in this invention is as follows: C: Carbon is a common strengthening element in steel. Interstitial solid-solution carbon atoms cause certain lattice distortions in the matrix, playing a role in solid-solution strengthening. It also combines with Ti or Nb to form submicron or nano-sized fine spherical TiC or NbC particles for dispersed precipitation strengthening, refining the grains and strengthening the matrix. In this invention, carbon ensures the strength and formability of the steel plate. Too low a carbon content will not achieve the mechanical properties of the steel plate described in this invention, while too high a content will cause the steel plate to become brittle, posing a risk of delayed fracture and hot-rolling edge cracking, and also negatively impacting the weldability, plasticity, and toughness of the steel plate. In this invention, the overall carbon content is required to be within a low range, which helps reduce the risk of delayed fracture and hot-rolling edge cracking, and is also beneficial to the weldability of the steel plate. Therefore, the optimal range of carbon in this invention is 0.060% to 0.095%.

[0011] Si: Silicon is one of the key elements in this invention. Silicon dissolves in the crystal lattice, producing a solid solution strengthening effect, increasing the strength and yield point of the steel sheet, while maintaining good ductility, which is particularly important for high-strength passenger vehicle chassis components. It can also refine the grains, improving the uniform and local elongation of the steel sheet, making it less prone to cracking and wrinkling during stamping, which is beneficial for manufacturing complex passenger vehicle chassis components. Therefore, the silicon content in this invention is 0.68% to 0.76%.

[0012] Mn: Manganese strengthens the solid solution in steel by inducing lattice distortion through substitution solid solution. It is also an austenite stabilizing element in steel, expanding the austenite region, reducing the critical quenching rate of steel, and delaying the transformation of austenite to pearlite. However, excessive Mn content leads to Mn segregation, which can reduce the plasticity of steel, worsen the uniformity of steel sheet structure during hot rolling, and easily cause severe banded structural defects in the structure, which is not conducive to the formability. Therefore, after comprehensive consideration, the present invention selects a manganese content of 1.55% to 1.90%.

[0013] P: Phosphorus is an impurity element in steel. It tends to agglomerate at grain boundaries. When the phosphorus content in steel is high, Fe2P particles are easily formed, which reduces the plasticity, toughness and porosity of the steel. Therefore, the lower its content, the better. In order to obtain a higher elongation, its upper limit is set at 0.010%.

[0014] S: Sulfur is an impurity element in steel. It easily combines with Mn to form MnS inclusions, which become the starting point of cracks and deteriorate the processing performance. It seriously affects the plasticity, formability and hole expansion performance of steel plates. Therefore, the lower the content, the better. The upper limit is set at 0.004%.

[0015] Al: When the Si content in steel is high, a red iron oxide scale, mainly composed of Fe2O3, will form on the surface of the steel plate during rolling. This is because Si promotes the formation of Fe-Si-O composite oxides, such as Fe2SiO4, at the interface between the iron oxide scale and the matrix. Fe2SiO4 will penetrate into the space between FeO and the matrix in a liquid state, and after solidification, it will exhibit an anchor-like morphology, firmly anchoring the FeO layer and making the iron oxide scale difficult to remove. The unremoved FeO layer will be crushed during subsequent hot rolling, increasing the contact area with air and accelerating the transformation process of FeO→Fe3O4→Fe2O3, ultimately forming a red iron oxide scale mainly composed of Fe2O3. Furthermore, during subsequent pickling, the steel plate surface will have iron oxide scale streaks and color difference defects. The role of adding Al in this invention is that Al's oxidation activity (i.e., its affinity for oxygen) is much higher than that of Si. Al is a strong deoxidizing element, and its ability to combine with oxygen is stronger at high temperatures. It will preferentially react with oxygen in the steel or in the air to first generate Al2O3. Si has relatively low oxidizing activity. Only after the oxidation reaction of Al is basically completed (or the oxygen supply is sufficient) will Si gradually combine with oxygen to form iron-silicon composite oxides (such as Fe2SiO4). Therefore, in the process of iron oxide scale formation, the oxidation reaction of Al occurs before Si, and Al2O3 is formed before the oxide of Si, avoiding the formation of Fe2SiO4. Furthermore, this invention contains Cr, and in the process of iron oxide scale formation, the oxidation reaction of Al occurs before Cr, and Al2O3 is formed before the oxide of Cr, avoiding the formation of FeCr2O4. This is beneficial for the absence of iron oxide scale streaks and color difference defects on the steel plate surface during subsequent pickling. Therefore, in this invention, the Al content is limited to 0.68% to 1.20%, and the Al / Si ratio is satisfied as 1.0 to 1.58.

[0016] Niobium (Nb) effectively delays the recrystallization of deformed austenite, inhibits austenite grain growth, increases the austenite recrystallization temperature, refines the grain size, and improves the strength and toughness of steel. Nb combines with carbon (C) to form NbC, which provides grain refinement and precipitation strengthening. It can also strengthen ferrite and bainite; however, excessive Nb content will lead to excessively large NbC sizes, deteriorating the steel plate's properties and reducing the toughness of the weld heat-affected zone. To achieve excellent mechanical properties, the optimal Nb content in this invention is between 0.040% and 0.060%.

[0017] Ti: Titanium can effectively delay the recrystallization of deformed austenite, prevent austenite grain growth, increase the austenite recrystallization temperature, refine grains, and improve the strength and toughness of steel. Since free N atoms in steel deteriorate the toughness of steel plates, Ti combines with impurity elements N in steel to form blocky or angular TiN. Therefore, the formation of TiN has a solidifying effect on N. However, if the N content is too high, the size of the blocky or angular TiN will be too large, which will deteriorate the performance of the steel plate and make the toughness of the weld heat-affected zone and the fatigue performance of the steel plate worse. Therefore, this invention limits N to ≤0.003% to avoid the formation of too much blocky or angular TiN. Furthermore, the purpose of Ti microalloying in this invention is to enable Ti and C to form submicron or nano-sized fine spherical TiC particles for dispersed precipitation strengthening, refining the grains, strengthening the matrix, and playing the role of grain refinement strengthening and precipitation strengthening. It can also strengthen ferrite, which is beneficial to obtaining excellent mechanical properties and fatigue properties, thereby improving the service life of steel in the manufacture of passenger car chassis structural parts. Therefore, the titanium content of this invention is selected from 0.090% to 0.140%.

[0018] Cr: Chromium can effectively improve the hardenability and strength of steel. In addition, chromium can form a relatively dense protective layer on the surface of steel in corrosive environments, protecting the substrate and effectively improving the corrosion resistance of the steel. However, excessive chromium content in steel can deteriorate the toughness of the steel plate. Therefore, the optimal range of Cr content in this invention is between 0.30% and 0.45%.

[0019] Mo: Molybdenum is a carbide-forming element that can improve the strength and toughness of steel plates. Mo can significantly improve the stability of austenite, increase the hardenability of steel, and is conducive to the formation of martensite. Therefore, the Mo content in this invention is selected from 0.10% to 0.40%.

[0020] Ce: Cerium has a strong affinity for harmful elements such as oxygen and sulfur in steel, forming stable oxides (e.g., Ce₂O₃) and sulfides (e.g., CeS). These compounds have high melting points and are easily removed from molten steel by flotation, reducing non-metallic inclusions and improving steel purity. For inclusions that cannot be completely removed, cerium can alter their morphology and distribution, transforming brittle, elongated sulfides into spherical or dot-shaped cerium sulfides, reducing the adverse effects of inclusions on the mechanical properties of steel, especially improving toughness and fatigue strength. The addition of cerium can inhibit grain growth during heating or cooling, refining austenite or ferrite grains, thereby improving the strength and toughness of the steel. Through purification and modification, it enhances the plasticity and toughness of steel and reduces the risk of cracking during hot and cold working. It can also improve the weldability and oxidation resistance of steel, thus increasing its service life at high temperatures. Therefore, this invention limits the Ce content to 0.0070%–0.0150%.

[0021] N: For the nitrogen content in steel, the lower the nitrogen content, the better. However, excessively low nitrogen content can lead to production difficulties and increased costs. This invention, however, requires ensuring a certain amount of AlN formation to refine the grains and improve the strength and elongation of the steel plate. Therefore, the nitrogen content in this invention is ≤0.003%. A method for producing high-strength steel plates with high surface quality for passenger vehicle chassis components includes smelting and continuous casting, hot rolling, bell-type furnace heating and cooling, and pickling processes. Specific details include: (1) Smelting process: The raw materials are pretreated by KR hot metal to control the S content to be less than 0.004%. After slag removal, they enter the converter. In the converter smelting, the double slag method is used to remove P, and the P content is controlled to be ≤0.010%. At the end of the converter smelting, the C content is controlled to be 0.060~0.095%. Argon gas is blown for more than 5 minutes when tapping the steel (the argon blowing and sedation before continuous casting can promote the removal of inclusions in the molten steel and improve the uniformity of the molten steel composition). Then, the LF+RH process is carried out, and the H and O contents are strictly controlled. H≤0.0002% and O≤0.0015%. The RH vacuum degassing is maintained for more than 17 minutes. Calcium treatment is carried out in the refining LF process. After that, the slab is continuously cast. The superheat of continuous casting is ≤20℃ and the continuous casting drawing speed is 0.7~1.0m / min. Reducing superheat and casting speed can improve macroscopic segregation of the billet, decrease the spacing of secondary dendrite arms in the solidification structure of the billet, and help reduce billet segregation and internal structural defects. Controlling the electromagnetic stirring current intensity in the secondary cooling zone during continuous casting to 170-250A and the secondary cooling water volume to 0.75-1.25L / kg (reducing the average carbon segregation index, suppressing segregation, and limiting the intensity of secondary cooling to suppress the tendency of central cracks in the billet to worsen) and applying light pressure in the horizontal section of the secondary cooling zone, i.e., at the end of solidification, the billet reduction is 4.0-5.5mm (reducing the central porosity and segregation of the billet). The billets are stacked for more than 48 hours after casting (reducing the accumulation of residual H, suppressing the generation of microcracks inside the billet, and ensuring the toughness of the steel plate).

[0022] (2) Hot rolling process: The continuously cast slab with a thickness of (170~230) mm × a width of (1060~2100) mm is loaded into a walking beam furnace for heating. The heating temperature is 1212~1252℃ and the holding time is 120~180 min. The rough rolling adopts the 3+3 rolling process (R1 is rolled in 3 passes and R2 is rolled in 3 passes) for a total of 6 passes. The exit temperature of the rough rolling is 1060~1100℃ and the thickness of the intermediate slab is 36 mm. The intermediate billet has a diameter of 0-45.0 mm and a width of 1060-2100 mm. Before entering the hot-rolling finishing mill, an insulation cover is used to reduce the temperature drop of the intermediate billet on the delay roller table and the temperature difference between the head and tail and the width direction. Finishing is a 7-stand continuous rolling process. High-pressure water descaling is performed before finishing. The entry temperature of the finishing mill is 1050-1080℃, and the final rolling temperature is 860-920℃. The rapid cooling rate is greater than 30℃ / s. After rapid cooling to 560-632℃, the billet is coiled. Rapid cooling to 560-632℃ aims to rapidly generate bainite, inhibiting grain growth while ensuring the bainite content, thus refining the bainite grains. The final microstructure of the rolled steel plate has a ferrite volume percentage of 5%-10%, a bainite volume percentage of 83%-90%, a martensite volume percentage of 1%-5%, and a retained austenite volume percentage of 1%-2%.

[0023] (3) After coiling, heat to 305-408℃ in a bell-type furnace, hold for 5.0-8.0 min, and then cool with the furnace. The purpose is to release residual stress. During hot rolling, uneven temperature and plastic deformation will cause residual stress inside the steel plate. At 305-408℃, atoms gain a small amount of energy and can release stress through dislocation movement, avoiding warping due to stress release when the steel plate is uncoiled and cut, thus optimizing the plate shape. It can also reduce the wear of shearing tools during processing, indirectly improving processing efficiency and reducing production material costs. In addition, the reaction rate of iron and oxygen is extremely slow in this temperature range. Combined with the nitrogen protective atmosphere commonly used in bell-type furnaces, it can minimize the formation of iron oxide scale, preserve the original surface state of the steel plate, and reduce the difficulty and cost of subsequent pickling surface treatment.

[0024] (4) Pickling process: Hydrochloric acid is used for continuous cleaning of iron oxide scale on the steel plate through the coil. After hot rolling, the steel plate is uncoiled and pickled on the pickling line. Before pickling, the steel plate is tension leveled with an elongation of 0.8% to 1.5%. The pickling solution is hydrochloric acid. The pickling tank is divided into 3 tanks. The concentration of pickling solution in tank 1 is 80 to 90 g / L, and the temperature of pickling solution in tank 1 is 80.0 to 85.0℃. The concentration of pickling solution in tank 2 is 100 to 110 g / L, and the temperature of pickling solution in tank 2 is 75.0 to 80.0℃. The concentration of pickling solution in tank 3 is 120 to 130 g / L. The pickling solution in tank 3 is maintained at a concentration of g / L and a temperature of 60.0–65.0℃. During pickling, a corrosion inhibitor is added to the acid solution, with the inhibitor accounting for 0.08–0.13% of the pickling solution by weight. The rinsing water temperature is 50–55℃, and the pickling and rinsing speeds are controlled at 70–100 m / min. The pickling process is carried out under tension, with a tension of 40–50 kN. Finally, the product is coated with oil and rolled up to obtain the finished product, which has a thickness of 1.50–6.00 mm and a surface roughness Ra of 1.33–1.70 μm.

[0025] Compared with the prior art, the beneficial effects of the present invention are: 1. The purpose of adding Al in this invention is that Al's oxidation activity (i.e., its affinity for oxygen) is much higher than that of Si. Al is a strong deoxidizing element, and its ability to combine with oxygen is even stronger at high temperatures. It will preferentially react with oxygen in steel or air to first generate Al2O3. Si, on the other hand, has relatively low oxidation activity. Only after the oxidation reaction of Al is basically complete (or the oxygen supply is sufficient) will it gradually combine with oxygen to form iron-silicon composite oxides (such as Fe2SiO4). Therefore, in the process of iron oxide scale formation, the oxidation reaction of Al occurs before Si, and Al2O3 will be generated before the oxide of Si, avoiding the formation of Fe2SiO4. Furthermore, this invention contains Cr. In the process of iron oxide scale formation, the oxidation reaction of Al occurs before Cr, and Al2O3 will be generated before the oxide of Cr, avoiding the formation of FeCr2O4. This is beneficial for the steel plate surface to be free of iron oxide scale streaks and color difference defects during subsequent pickling.

[0026] 2. Titanium can effectively delay the recrystallization of deformed austenite, prevent austenite grain growth, increase the austenite recrystallization temperature, refine the grains, and improve the strength and toughness of steel. Since the presence of free N atoms in steel deteriorates the toughness of the steel plate, Ti combines with the impurity element N in the steel to form blocky or angular TiN. Therefore, the formation of TiN has a solidifying effect on N. Furthermore, the purpose of the Ti microalloying in this invention is to enable Ti and C to form submicron or nanoscale fine spherical TiC particles for dispersion precipitation strengthening, grain refinement, and matrix strengthening. This achieves both grain refinement strengthening and precipitation strengthening, and can also strengthen ferrite. This is beneficial for obtaining excellent mechanical properties and fatigue properties, thereby improving the service life of steel in the manufacture of passenger car chassis structural components.

[0027] 3. Chromium can effectively improve the hardenability and strength of steel. In corrosive environments, chromium can form a relatively dense protective layer on the surface of steel, protecting the substrate and effectively improving the corrosion resistance of the steel.

[0028] 4. Molybdenum can improve the strength and toughness of steel plates, significantly improve the stability of austenite, increase the hardenability of steel, and facilitate the formation of martensite.

[0029] 5. Cerium has a strong affinity for harmful elements such as oxygen and sulfur in steel, forming stable oxides (e.g., Ce₂O₃) and sulfides (e.g., CeS). These compounds have high melting points and are easily removed from molten steel by flotation, reducing non-metallic inclusions and improving steel purity. For inclusions that cannot be completely removed, cerium can alter their morphology and distribution, transforming brittle, elongated sulfides into spherical or dot-shaped cerium sulfides, reducing the adverse effects of inclusions on the mechanical properties of steel, especially improving toughness and fatigue strength. The addition of cerium can inhibit grain growth during heating or cooling, refining austenite or ferrite grains, thereby improving the strength and toughness of the steel. Through purification and modification, it enhances the plasticity and toughness of steel and reduces the risk of cracking during hot and cold working. It can also improve the weldability and oxidation resistance of steel, thus extending its service life at high temperatures.

[0030] 6. After coiling, the steel is heated and cooled in a bell-type furnace. This releases residual stress. During hot rolling, uneven temperature and plastic deformation leave residual stress inside the steel plate. At 305–408℃, atoms gain a small amount of energy and can release stress through dislocation movement, preventing warping during uncoiling and cutting due to stress release and optimizing the plate shape. It also reduces the wear of shearing tools during processing, indirectly improving processing efficiency and reducing production material costs. Furthermore, the reaction rate between iron and oxygen is extremely slow in this temperature range. Combined with the nitrogen protective atmosphere commonly used in bell-type furnaces, this minimizes the formation of iron oxide scale, preserving the original surface condition of the steel plate and reducing the difficulty and cost of subsequent pickling surface treatment.

[0031] 7. The microstructure of the steel of this invention consists of ferrite, bainite, martensite and retained austenite, which significantly improves the comprehensive mechanical properties of the steel plate during the forming process.

[0032] 8. This invention has excellent mechanical properties, with a yield strength of 680-760 MPa, a tensile strength of 830-900 MPa, a longitudinal elongation A≥24%, and a qualified transverse cold bending of 180° D=a. It uses conventional components with high Si content, so there is no need to specially reduce the Si content. It is easy to smelt, has low cost, and has good surface quality, with no iron oxide scale streaks and color difference defects. The surface roughness Ra is 1.33-1.70 μm. Detailed Implementation

[0033] To make the objectives, technical solutions, and advantages of this invention clearer, the specific implementation methods of this invention will be further described below in conjunction with the embodiments. The following embodiments are used to specifically illustrate the content of this invention. These embodiments are only general descriptions of the content of this invention and do not limit the content of this invention.

[0034] The specific embodiments of the present invention are as follows: The smelting raw materials undergo KR hot metal pretreatment to control the sulfur content below 0.004%. After slag removal, they enter the converter. In the converter smelting, a double-slag method is used to remove phosphorus (P), controlling the P content to ≤0.010%. At the end of the converter smelting, the carbon content is controlled between 0.060% and 0.095%. Argon gas is blown for at least 5 minutes during tapping, followed by the LF+RH process. The H and O contents are strictly controlled: H ≤0.0002%, O ≤0.0015%. RH vacuum degassing is maintained for at least 17 minutes. The LF is then refined. The process involves calcium treatment followed by slab continuous casting. The superheat during continuous casting is ≤20℃, and the casting speed is 0.7~1.0m / min. The electromagnetic stirring current intensity in the secondary cooling zone during continuous casting is controlled at 170A~250A, and the secondary cooling water volume is 0.75L / kg~1.25L / kg. Light pressure is applied in the horizontal section of the secondary cooling zone, i.e., at the end of solidification, and the reduction of the continuous casting billet is 4.0~5.5mm (to reduce the central porosity and segregation of the billet). The billets are stacked for more than 48 hours after being taken off the line. A continuously cast slab with a thickness of (170–230) mm and a width of (1060–2100) mm is loaded into a walking beam furnace for heating at a temperature of 1212–1252℃ and a holding time of 120–180 min. The roughing rolling process employs a 3+3 rolling pattern (R1 is rolled in 3 passes, and R2 is rolled in 3 passes), for a total of 6 passes. The roughing mill exit temperature is 1060–1100℃, and the intermediate slab thickness is 36.0–45 mm. The intermediate billet is 0.0 mm thick and 1060–2100 mm wide. Before entering the hot rolling mill, it is insulated with a heat-insulating cover to reduce the temperature drop on the delay roller table and the temperature difference between the head and tail and the width direction. The finishing mill is a 7-stand continuous rolling process. High-pressure water descaling is performed before finishing. The entry temperature is 1050–1080℃, and the final rolling temperature is 860–920℃. The rapid cooling rate is greater than 30℃ / s. After rapid cooling to 560–632℃, it is coiled. After hot rolling and coiling, it is heated to 305–408℃ in a bell-type furnace, held for 5.0–8.0 min, and then cooled in the furnace. After cooling, the steel plate is uncoiled on the pickling line and pickled with hydrochloric acid. Before pickling, the steel plate is tension-straightened with an elongation of 0.8%~1.5%. The pickling solution is hydrochloric acid, and the pickling tank is divided into three tanks: Tank 1 has a concentration of 80~90 g / L and a pickling solution temperature of 80.0~85.0℃; Tank 2 has a concentration of 100~110 g / L and a pickling solution temperature of 75.0~80.0℃; Tank 3 has a concentration of 120~130 g / L and a pickling solution temperature of 6℃. During pickling at 0.0~65.0℃, a corrosion inhibitor is added to the acid solution, with the corrosion inhibitor accounting for 0.08~0.13% of the weight of the pickling solution; the rinsing water temperature is 50~55℃, and the pickling and rinsing speed is controlled at 70~100m / min; the pickling process is under tension, with a tension of 40~50KN; finally, oiling and winding are performed to obtain the finished product, with a thickness of 1.50~6.00mm and a surface roughness Ra of 1.33~1.70μm.

[0035] The specific components, smelting process, hot rolling process, bell-type furnace heating process, pickling process, steel plate properties, and volume percentage of the six embodiments of the present invention are shown in Tables 1-6.

[0036] Table 1 Chemical composition (wt, %) of the embodiments of the present invention: Table 2 Smelting process of the present invention embodiment: Table 3 Hot rolling process and bell-type furnace heating process of the present invention: Table 4. Pickling process parameters of the present invention embodiments: Table 5 Mechanical performance parameters of embodiments of the present invention: Table 6. Tissue volume percentage in the embodiments of the present invention:

Claims

1. A high-surface-quality, high-strength steel plate for passenger vehicle chassis components, characterized in that, The chemical composition of the steel, by weight percentage, is as follows: C: 0.060%–0.095%, Si: 0.68%–0.76%, Mn: 1.55%–1.90%, Al: 0.68%–1.20%, Nb: 0.040%–0.060%, Ti: 0.090%–0.140%, Cr: 0.30%–0.45%, Mo: 0.10%–0.40%, Ce: 0.0070%–0.0150%, and Al / Si: 1.0–1.58, with P ≤ 0.010%, S ≤ 0.004%, N ≤ 0.003%, and the balance being Fe and unavoidable impurities. The production method of high-strength steel plates with high surface quality for passenger vehicle chassis components includes smelting and continuous casting, hot rolling, bell-type furnace heating and cooling, and pickling processes, specifically including: The hot rolling process includes: a finishing mill inlet temperature of 1050-1080℃, a finishing mill temperature of 860-920℃, a rapid cooling rate of more than 30℃ / s, and coiling after rapid cooling to 560-632℃. After winding, the product is heated to 305–408°C in a bell-type furnace, held for 5.0–8.0 minutes, and then cooled with the furnace.

2. The high-surface-quality, high-strength steel plate for passenger vehicle chassis components according to claim 1, characterized in that, The microstructure of the finished steel plate is 5%–10% ferrite, 83%–90% bainite, 1%–5% martensite, and 1%–2% retained austenite.

3. The high surface quality, high-strength steel plate for passenger vehicle chassis components according to claim 1, characterized in that, The steel plate has a yield strength of 680-760 MPa, a tensile strength of 830-900 MPa, a longitudinal elongation A ≥ 24%, and a transverse cold bending of 180° D = a is qualified.

4. The high surface quality, high-strength steel plate for passenger vehicle chassis components according to claim 1, characterized in that, The surface roughness Ra of the steel plate is 1.33 to 1.70 μm.

5. A method for producing high-surface-quality, high-strength steel sheet for passenger vehicle chassis components as described in any one of claims 1-4, characterized in that, This includes smelting and continuous casting, hot rolling, bell-type furnace heating and cooling, and pickling processes. Specific details include: The hot rolling process includes: a finishing mill inlet temperature of 1050-1080℃, a finishing mill temperature of 860-920℃, a rapid cooling rate of more than 30℃ / s, and coiling after rapid cooling to 560-632℃. After winding, the product is heated to 305–408°C in a bell-type furnace, held for 5.0–8.0 minutes, and then cooled with the furnace.

6. The method for producing high-surface-quality, high-strength steel plates for passenger vehicle chassis components according to claim 5, characterized in that, In the smelting and continuous casting process: argon gas is blown for more than 5 minutes when tapping steel from the converter, RH vacuum degassing is maintained for more than 17 minutes, the superheat of continuous casting is ≤20℃, the continuous casting billet pulling speed is 0.7~1.0m / min, the electromagnetic stirring current intensity in the secondary cooling zone of the continuous casting stage is controlled at 170~250A, the secondary cooling water volume is 0.75~1.25L / kg, light pressure is applied at the end of solidification, the reduction of the continuous casting billet is 4.0~5.5mm, and the billets are stacked for more than 48 hours after leaving the line.

7. The method for producing high-surface-quality, high-strength steel plates for passenger vehicle chassis components according to claim 5, characterized in that, The hot rolling process also includes: heating temperature of 1212~1252℃, holding time of 120~180min, roughing mill exit temperature of 1060~1100℃, intermediate billet thickness of 36.0~45.0mm, width of 1060~2100mm, and the intermediate billet is insulated with a heat preservation cover before entering the hot rolling finishing mill.

8. The method for producing high-surface-quality, high-strength steel sheet for passenger vehicle chassis components according to claim 5, characterized in that, The pickling process includes: a tensile elongation rate of 0.8%–1.5%; the pickling tank is divided into three tanks: tank 1 has a concentration of 80–90 g / L and a pickling solution temperature of 80.0–85.0℃; tank 2 has a concentration of 100–110 g / L and a pickling solution temperature of 75.0–80.0℃; tank 3 has a concentration of 120–130 g / L and a pickling solution temperature of 60.0–65.0℃; during pickling, a corrosion inhibitor is added to the acid solution, with the corrosion inhibitor accounting for 0.08%–0.13% of the weight of the pickling solution; the rinsing water temperature is 50–55℃; the pickling and rinsing speeds are controlled at 70–100 m / min; the pickling process is under tension, with a tension of 40–50 kN.

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