EP4527963A1 - Acier à haute plasticité et son procédé de fabrication - Google Patents

Acier à haute plasticité et son procédé de fabrication Download PDF

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EP4527963A1
EP4527963A1 EP23826543.3A EP23826543A EP4527963A1 EP 4527963 A1 EP4527963 A1 EP 4527963A1 EP 23826543 A EP23826543 A EP 23826543A EP 4527963 A1 EP4527963 A1 EP 4527963A1
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Prior art keywords
steel
content
less
equal
mpa
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EP23826543.3A
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German (de)
English (en)
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EP4527963A4 (fr
Inventor
Huanrong WANG
Chen Zhang
Ana YANG
Houjun PANG
Jiajie FAN
Min Lu
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority claimed from CN202210714634.8A external-priority patent/CN117305690A/zh
Priority claimed from CN202210713392.0A external-priority patent/CN117305685A/zh
Application filed by Baoshan Iron and Steel Co Ltd filed Critical Baoshan Iron and Steel Co Ltd
Publication of EP4527963A1 publication Critical patent/EP4527963A1/fr
Publication of EP4527963A4 publication Critical patent/EP4527963A4/fr
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
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Definitions

  • the present invention belongs to the field of steel and manufacturing method therefor, and particularly relates to a high-plasticity steel and a manufacturing method therefor.
  • Chinese Patent Application CN104233092A discloses a 780 MPa grade steel with ultra-high plasticity, whose composition is designed to have a low carbon content and a high silicon content, and a certain amount of precious alloy elements such as Cr, Mo and Nb, resulting in relatively high alloy costs.
  • Chinese Patent Application CN107815593A discloses a steel with low silicon content and high aluminum content and with ultra-high plasticity, whose composition has low silicon content and high aluminum content, and a certain amount of precious element Cu.
  • the production process mainly includes heat treatment in the two-phase zone for 1-3 minutes and then phase transformation in the bainite zone, to obtain 780 MPa grade heat-treated steel with ultra-high plasticity.
  • the heat treatment process cannot be applied to existing hot rolling production lines.
  • the objective of the present invention is to provide a high plasticity steel and a manufacturing method therefor.
  • the high plasticity steel has good mechanical properties and can achieve good matching among a low yield strength, a low yield ratio, a high tensile strength and an ultra-high elongation rate.
  • the steel can be widely applied to components with complex shape requirements, or other parts that require thinning while maintaining high strength, such as those in commercial or passenger vehicles.
  • the present invention provides a steel comprising the following components in percentage by mass: C: 0.10-0.35%, Si: 0.8-2.0%, Mn: 1.0-3.0%, P: ⁇ 0.02%, S ⁇ 0.005%, Al: 0.1-2.0%, N: ⁇ 0.005%, with the balance being Fe and other inevitable impurities.
  • the above-mentioned steel also comprises Ti, and, in percentage by mass, the content of Ti is less than or equal to 0.2%, preferably 0.05-0.2%, more preferably 0.05-0.1%.
  • the above-mentioned steel also comprises one or more selected from the group consisting of Mo, Nb, V, Cu, Ni, Cr and B; wherein, in percentage by mass, the content of Mo is less than or equal to 0.5%, preferably less than or equal to 0.3%; the content of Nb is less than or equal to 0.1%, preferably less than or equal to 0.06%; the content of V is less than or equal to 0.1%, preferably less than or equal to 0.06%; the content of Cu is less than or equal to 0.5%, preferably less than or equal to 0.3%; the content of Ni is less than or equal to 0.5%, preferably less than or equal to 0.3%; the content of Cr is less than or equal to 0.5%, preferably less than or equal to 0.3%; the content of B is less than or equal to 0.001%, preferably less than or equal to 0.0005%.
  • Mo is less than or equal to 0.5%, preferably less than or equal to 0.3%
  • the content of Nb is less than or equal to 0.1%, preferably less than or equal to
  • the inevitable impurities of the above-mentioned steel include, in percentage by mass, O ⁇ 0.003%, preferably O ⁇ 0.002%; S ⁇ 0.003%; and/or N ⁇ 0.004%.
  • the composition in percentage by mass of the above-mentioned steel satisfies one or more of the following: C: 0.15 ⁇ 0.25%, Si: 1.0 ⁇ 1.6%, Mn: 1.5 ⁇ 2.5%, Al: 0.3 ⁇ 1.0%.
  • Carbon is a basic element in steel, and is also one of the important elements in the present invention. Carbon expands the austenite phase region and stabilizes austenite. Carbon, as a gap atom in steel, plays a very important role in improving the strength of steel, and has the greatest impact on the yield strength and tensile strength of steel. Additionally, as an effective element for stabilizing residual austenite, carbon usually has a relatively high concentration in steel. In the present invention, in order to obtain high-strength steel having different levels of tensile strength and having a relatively stable residual austenite in the steel microstructure, the content of carbon must be greater than or equal 0.10%. However, the content of carbon cannot exceed 0.35%. Excessive content of carbon can easily lead to higher strength, reduction of elongation rate, and deterioration of welding performance. Therefore, the content of carbon is between 0.10-0.35%.
  • Silicon is a basic element in steel, and is also one of the important elements in the present invention.
  • the addition of silicon to steel can lower the non-recrystallization temperature of austenite, expanding the rolling process window of austenite. This allows dynamic recrystallization of the steel to be completed during the finish rolling stage, which is beneficial for improving the differences in transverse and longitudinal properties of the steel.
  • Another function of adding silicon into steel is the inhibition of the formation of the cementite. In the present invention, to ensure that the steel microstructure contains a large amount of residual austenite, it is necessary to add a relatively high amount of silicon to inhibit the formation of the cementite. This inhibitory effect of silicon on carbide formation is evident when the silicon content reaches 0.8% or more.
  • the content of silicon should not be too high; otherwise, the rolling force load during actual rolling process will be too large, and there will be a significant amount of red scale on the surface of steel plate, which is not conducive to stable production during rolling. Therefore, the silicon content in the steel should be 0.8-2.0%, preferably 1.0-1.6%.
  • Manganese is the most fundamental elements in steel, and is also one of the most important elements in the present invention. Mn expands the austenite phase region, reduces the critical quenching rate of the steel, stabilizes austenite, refines grains, and delays the transition of austenite to pearlite. Additionally, during heat treatment process, Mn undergoes partition and diffuses from bainite into residual austenite, further stabilizing the residual austenite and increasing its content. A manganese content of at least 1.0% is required to achieve these effects. However, the content of manganese should not be too high. If the content of manganese exceeds 3.0%, it may lead to segregation in the continuous casting slab and the formation of a large amount of MnS inclusions. Therefore, the manganese content in the steel should be 1.0-3.0%, preferably 1.5-2.5%.
  • Phosphorus is an impurity element in steel. P tends to segregate easily at grain boundaries. When the content of P in steel is relatively high ( ⁇ 0.1%), Fe 2 P is formed and precipitated around the grain, reducing the plasticity and toughness of the steel. Thus, the lower the content of P, the better. It is generally preferable to control the content of P to 0.02% or less, as this level does not increase the cost of steel-making.
  • Sulfur is an impurity element in steel.
  • S typically combines with Mn to form MnS inclusions, especially when the contents of S and Mn are both relatively high, a significant amount of MnS will be formed in the steel.
  • MnS itself has a certain degree of plasticity. MnS deforms along the rolling direction during subsequent rolling process, which not only reduces the transverse plasticity of the steel, but also increases structure anisotropy, adversely affecting hole expansion performance. Therefore, the lower the content of S in steel, the better.
  • the S content is required to be controlled to 0.005% or less, preferably 0.003% or less.
  • Aluminum is one of the important elements in the present invention. In addition to its basic roles of deoxidation and nitrogen fixation, aluminum also has two other important functions in the present invention.
  • the content of austenite-stabilizing elements such as carbon and manganese is relatively high, so that austenite has strong stability.
  • austenite-stabilizing elements such as carbon and manganese
  • additional aluminum is also necessary. Aluminum is added into steel for accelerating the transformation of ferrite.
  • Al can not only play a role in inhibiting the formation of cementite, but also promote the diffusion of carbon atoms from bainite ferrite to residual austenite, thereby accelerating the diffusion of carbon atoms in residual austenite, increasing the carbon concentration in residual austenite, and obtaining highly stable residual austenite.
  • the content of aluminum is ⁇ 0.1%, the above-mentioned various beneficial effects can be achieved.
  • the content of aluminum exceeds 2.0%, its effect of promoting diffusion and enrichment of carbon becomes saturated, and the viscosity of the molten steel increases, which can easily clog the casting nozzle. Therefore, the aluminum content in the steel of the present invention should be 0.1-2.0%, preferably 0.3%-1.0%.
  • Nitrogen is an impurity element in the present invention. The lower the N content, the better. However, nitrogen is an inevitable element in the steelmaking process. Although present in small amounts, nitrogen can combines with strong carbide-forming elements such as Ti to form TiN particles, which are detrimental to the performances of steel. Therefore, the content of nitrogen in the present invention is controlled to be 0.005% or less, preferably 0.004% or less.
  • Titanium is one of the optional additive elements in the present invention.
  • Steel with ultra-high plasticity and high-strength comprises a large amount of residual austenite, which is a soft phase with relatively low yield strength. Therefore, to improve the yield strength of the steel, microalloying elements such as titanium can be added under certain conditions. Titanium enhances yield strength through its precipitation strengthening effect in the proeutectoid ferrite. As the titanium content increases, the precipitation strengthening effect is gradually enhanced. When the titanium content reaches 0.20%, the precipitation strengthening effect of titanium becomes saturated. Therefore, the amount of titanium added can be adjusted as needed.
  • the titanium content in the steel of the present invention is controlled to be 0.20% or less, preferably 0.05-0.2%, more preferably 0.05-0.1%.
  • Molybdenum is one of the optional additive elements in the present invention.
  • the addition of molybdenum to steel can greatly delay the phase transition of ferrite and pearlite, which is conducive to obtaining bainite structure.
  • molybdenum has a strong resistance to welding softening. Since the primary objective of the present invention is to obtain a microstructure mainly consisting of ferrite, bainite, and residual austenite, and since ferrite and bainite are prone to softening after welding, the addition of an appropriate amount of molybdenum can effectively reduce the degree of welding softening. Considering that molybdenum is a precious metal, adding too much would increase the cost of the alloy. Therefore, the content of molybdenum in the present invention is 0.5% or less, preferably 0.3% or less.
  • Oxygen is an inevitable element in the steelmaking process.
  • the content of O in steel can generally be reduced to 0.003% or less, which does not cause any significant adverse effects on the performance of the steel plate. Therefore, in the present invention, the O content in the steel is controlled to be 0.003% or less, preferably 0.002% or less.
  • Copper is one of the optional additive elements in the present invention.
  • the addition of copper to steel can improve the corrosion resistance of the steel, and when combined with phosphorus, the corrosion resistance effect is even better.
  • an ⁇ -Cu precipitation phase may be formed under certain conditions, which has a relatively strong precipitation strengthening effect.
  • the addition of Cu tends to result in "Cu-brittleness” phenomenon during the rolling process.
  • the content of Cu in the present invention is controlled to be 0.5% or less, preferably 0.3% or less.
  • Nickel is one of the optional additive elements in the present invention.
  • the addition of nickel to steel provides a certain level of corrosion resistance, though its corrosion resistance effect is weaker than copper.
  • the addition of nickel in steel has little effect on the tensile properties of the steel, but can refine the structure and precipitation phases of steel and greatly improve the low-temperature toughness of steel.
  • the addition of a small amount of nickel can inhibit the occurrence of "Cu-brittleness".
  • the addition of relatively high amount of nickel does not have any significant adverse effect on the properties of the steel itself.
  • both copper and nickel are added, they not only improve corrosion resistance, but also refine the structure and precipitate phases of the steel, greatly improving the low-temperature toughness.
  • both copper and nickel are relatively valuable alloying elements. Therefore, to minimize the cost of alloy design, the amount of nickel added in the present invention is 0.5% or less, preferably 0.3% or less.
  • Chromium is one of the optional additive elements in the present invention.
  • the addition of chromium to steel can improves its strength mainly through mechanisms such as solid solution strengthening or microstructure refinement. Chromium easily dissolves into ferrite, and plays a role in strengthening ferrite. Additionally, the addition of a small amount of chromium element can also improve corrosion resistance. Therefore, the amount of chromium added in the present invention is 0.5% or less, preferably 0.3% or less.
  • Niobium is one of the optional additive elements in the present invention. Similar to titanium, niobium is a strong carbide-forming element in steel. The addition of niobium to steel can greatly increase the non-recrystallization temperature of steel, allowing the formation of deformation austenite with higher dislocation density during the finish rolling stage, and refine the final phase transition structure during the subsequent transformation process. However, the amount of niobium added should not be too much. On one hand, when the amount of niobium added exceeds 0.01%, it is prone to form a relatively coarse niobium-carbonitride in the structure, which is not conducive to the low-temperature impact toughness of the steel.
  • the niobium content in the steel of the present invention is 0.10% or less, preferably 0.06% or less.
  • Vanadium is one of the optional additive elements in the present invention. Similar to Ti and Nb, vanadium is also a strong carbide-forming element. However, vanadium carbides have a low solubility or precipitation temperature and are typically fully solid dissolved in austenite during the finish rolling stage. Carbides of vanadium begins to form in ferrite only when the temperature decreases and phase transition starts. Since vanadium carbides have a high solid solubility in ferrite compared to niobium and titanium carbides, the size of vanadium carbides formed in ferrite is larger and vanadium carbides are prone to form at grain boundaries, which is not conducive to the toughness of steel. Therefore, the amount of vanadium added in the steel of the present invention is 0.10% or less, preferably 0.06% or less.
  • Boron is one of the optional additive elements in the present invention. Boron is an element that is prone to segregation. During rolling in the austenite region, B element can segregate to the austenite grain boundaries, reducing the interfacial energy at the austenite grain boundaries and inhibiting the formation of ferrite during subsequent cooling and phase transformation. Since the desired microstructure of the present invention includes ferrite, bainite and stable residual austenite, it is necessary to strictly control the content of boron element in the steel to prevent the inhibition of ferrite formation due to excessive addition of boron. Therefore, the amount of boron added in the steel of the present invention is 0.001% or less, preferably 0.0005% or less.
  • the content of elements in the steel of the present invention refer to mass fractions.
  • the steel of the present invention has a microstructure includes ferrite, bainite, and residual austenite, wherein the residual austenite content is 5% or more.
  • the volume fraction of ferrite in steel is between 30-50%, preferably between 35-45%; the volume fraction of bainite is between 40-60%, preferably between 45-55%; and the volume fraction of residual austenite is between 5-15%, preferably between 10-15%.
  • the above-mentioned steel has a yield strength of 500 MPa or more, preferably 600 MPa or more, more preferably 700 MPa or more; a tensile strength of 780 MPa or more, preferably 980MPa or more; an elongation rate of 25% or more, preferably 30% or more.
  • the above-mentioned steel has a hole expansion of 30% or more, preferably 50% or more.
  • the yield strength of the steel is ⁇ 600MPa
  • the tensile strength is ⁇ 780MPa
  • the elongation rate is ⁇ 30%
  • the hole expansion rate is ⁇ 50%
  • the yield strength of the steel is ⁇ 700MPa
  • the tensile strength is ⁇ 980MPa
  • the elongation rate is ⁇ 25%
  • the hole expansion rate is ⁇ 30%.
  • the existing 780 MPa grade steel with ultra-high plasticity comprises C-Si-Mn as the main elements, with microalloying elements such as Nb and Ti added when necessary to refine the grains.
  • the content of Al is 0.1% or less, mainly to utilize the deoxidation and nitrogen fixation function of Al element.
  • the present invention adopts a composition design of high content Al, with the Al content of 0.1% or more.
  • the main purposes of adding high content of Al are to promote transformation of ferrite and to further improve the stability of residual austenite.
  • the existing 780 MPa grade steels with ultra-high plasticity have low yield strength or low yield ratio, and the residual austenite is not sufficiently stable. In case of deformation, the residual austenite in the microstructure easily transforms into martensite.
  • the ultra-high plasticity steel of the present invention can have tensile properties with varying yield strengths and yield ratios. Moreover, the residual austenite in the structure is more stable, and the content of residual austenite is 5% or more. Despite the varying yield strengths, the tensile strength and elongation rate remain at a high level, making the steel more favorable for downstream processing and use. Moreover, the steel of the present invention can also have a relatively high hole expansion rate, making it particularly suitable for stamping processes involving parts with higher requirements for drawing and flanging forming.
  • the method for manufacturing the aforementioned steel comprises the following steps:
  • the above-mentioned method further includes step 4) pickling, wherein the hot-rolled strip steel is pickled at a running speed of 30 ⁇ 120 m/min, with a pickling temperature of 75 ⁇ 85 °C and a straightening rate of 2% or less, and then rinsed at a temperature in the range of 35 ⁇ 50 °C, and the surface of the hot-rolled strip steel is dried at a temperature of 120 ⁇ 140 °C, and oiled, to obtain a pickled steel with high-strength and ultra-high plasticity.
  • the primary purpose of setting the initial rolling temperature of hot rolling at 1000 °C or higher, and performing 5-7 passes of rolling with a relatively large deformation rate of 50% or more at 1000°C or higher, is to refine the austenite grains.
  • a staged cooling process is used to control the content of ferrite, bainite and residual austenite in the steel.
  • the water-cooling stop temperature and air-cooling duration in the first stage cooling after rolling determine the content of ferrite, while the coiling temperature after the second cooling stage determines the contents of bainite and residual austenite.
  • the content of ferrite, bainite and residual austenite can be quantitatively controlled.
  • This combination of the innovative composition design and process can obtain ultra-high plasticity steel with exceptionally stable residual austenite.
  • the innovation of the present invention are as follows.
  • the present invention obtains hot-rolled or pickled ultra-high plasticity high-strength steel with low yield strength by a composition design of medium-to-low carbon, high silicon and high aluminum, combined with an innovative staged cooling process during hot rolling, a medium-temperature coiling process, and pickling process.
  • the relatively high content of carbon is beneficial for obtaining high strength, and provides a large amount of available carbon atoms that can diffuse into the residual austenite, resulting in highly stable residual austenite.
  • the main purpose of adding a relatively high silicon content is to inhibit the formation of carbides and extend the temperature range for ferrite formation.
  • the addition of relatively high content of aluminum promotes the diffusion of carbon atoms from bainite ferrite to residual austenite, further improving the stability of the residual austenite.
  • the present invention adds high content Ti into the steel.
  • nano-sized TiC precipitates are formed within the ferrite grains during the ferrite transformation process, thereby improving the strength of ferrite, reducing the performance differences between ferrite and bainite, and increasing the hole expansion rate of steel.
  • the relatively high manganese content in the steel of the present invention further improves the stability of the residual austenite.
  • the microstructure of the steel of the present invention with a high hole expansion rate and ultra-high plasticity consists of ferrite, bainite and residual austenite. Bainite provides the steel with high tensile strength. Ferrite and the relatively high content of metastable residual austenite provide the steel plate with ultra-high elongation rate through the TRIP effect, with the content of residual austenite being ⁇ 5%.
  • the ferrite containing nano-sized precipitates has improved yield strength through precipitation strengthening, which reduces the hardness difference between ferrite and bainite, and greatly increases its hole expansion rate while achieving ultra-high plasticity.
  • the main purpose of coiling at 350-550 °C after hot rolling is to obtain bainite and highly stable residual austenite.
  • the microstructure of the ultra-high plasticity steel of the present invention primarily consists of ferrite, bainite and stable residual austenite, with a content of residual austenite content of ⁇ 5%. Ferrite endows the steel plate with low yield strength, bainite endows the steel plate with high tensile strength, and stable residual austenite endows the steel plate with ultra-high elongation.
  • the present invention can obtain hot-rolled or pickled ultra-high plasticity high-strength steel with low yield strength.
  • the steel has a yield strength of 500MPa or more, preferably 600MPa or more, more preferably 700MPa or more, a tensile strength of 780MPa or more, preferably 980MPa or more.
  • the elongation rate of the hot-rolled or pickled steel coils is greater than or equal 25%, preferably greater than or equal 30%.
  • the present invention adopts a composition design of medium-to-low carbon, high silicon, and high aluminum, which is completely different from the traditional low-carbon, high-silicon or low-silicon, high-aluminum designs of conventional hot-rolled ultra-high plasticity steels.
  • the present invention adopts an innovative composition design concept of medium-to-low carbon and high aluminum, which is matched with the innovative staged cooling and medium-temperature coiling processes.
  • Hot-rolled and pickled ultra-high plasticity steels with high tensile strength, ultra-high elongation, and high hole expansion rate can be obtained using an existing continuous hot rolling production line.
  • the high-strength and ultra-high plasticity steel manufactured by using the technology provided by the present invention has a yield strength of ⁇ 500MPa, a tensile strength of ⁇ 780MPa, a low yield ratio, and ultra-high elongation (A reaching 30% or more), exhibiting excellent combination of low yield strength, low yield ratio, high tensile strength, ultra-high plasticity, and high hole expansion rate. It can be applied to the manufacturing of various complex parts of passenger or commercial vehicles and has promising application prospects.
  • compositions of the steels in the examples and comparative examples of the present invention are shown in Table 1.
  • the balance in the table is Fe and other inevitable impurities.
  • the cooling was staged cooling. After the final rolling, the steel strip was water-cooled to a temperature between 600 ⁇ 750 °C at a cooling rate of 30 °C/s or more. After air cooling for 1 ⁇ 10 seconds, the steel strip was then cooled to a temperature between 350 ⁇ 550 °C at a cooling rate of 10 °C/s or more and coiled, and then cooled to room temperature at a cooling rate of 50 °C/h or less, to obtain a hot-rolled strip steel.
  • the specific process for the pickling step is as follows. 4) Pickling: The hot-rolled strip steel was pickled at a running speed of 30 ⁇ 120 m/min, with a pickling temperature of 75 ⁇ 85 °C and a straightening rate of 2% or less, and then rinsed at a temperature in the range of 35 ⁇ 50 °C, and the surface of the hot-rolled strip steel was dried at a temperature of 120 ⁇ 140 °C, and oiled.
  • the steels of Comparative Example 1-3 are from CN 104233092 A .
  • Table 2 shows the specific production process parameters of the steel in the examples of the present invention, and the specific process parameters for pickling are not shown.
  • Table 3 shows the performance parameters of the hot-rolled steels of Examples 1-8 and 17-24 of the present invention.
  • Table 4 shows the performance parameters of the pickled steels of Examples 9-16 of the present invention.
  • composition design of the comparative examples is low-carbon, high silicon and low aluminum, while the composition design of the examples of the present invention is medium-to-low carbon, high silicon and high aluminum.
  • the two have completely different composition designs in terms of carbon content and aluminum content.
  • the hole elongation rate of comparative examples is around 20%, while the hole elongation rate of the examples of the present invention reaches around 30%, indicating that the ultra-high plasticity steel of the present invention has a better matching of strength and ultra-high plasticity.
  • the ferrite content in the microstructure of the comparative examples is 15% or less, while the ferrite content in the steel microstructure of the examples is 25% to 45%. Additionally, the bainite content in the microstructure of the comparative examples is 70% or more, while the bainite content in the microstructure of the examples is 44% to 53%, demonstrating a significant difference in microstructural design between the two.
  • the hot-rolled or pickled high-strength ultra-high plasticity steel coils or plates according to the present invention have a yield strength of 500 MPa or more, up to 600 MPa or more, and even up to 700 MPa or more; a tensile strength of 780 MPa or more, up to 980 MPa or more; an elongation rate of 25% or more, up to 30% or more; and a hole expansion rate of 30% or more, and even up to 50% or more.
  • the steel has good matching of yield strength, tensile strength, ultra-high plasticity and high hole expansion rate, and is especially suitable for complex forming and cold stretching parts such as automotive chassis structures and has broad application prospects.
  • Figures 3 to 6 show the metallographic photographs of Examples 1, 6, 10, and 14, respectively. These figures demonstrate that the composition and process design according to the present invention achieve a microstructure mainly composed of carbide-free lath bainite and retained austenite between bainitic laths.
  • Figures 7 to 10 show typical metallographic photographs of Examples 17, 19, 21, and 23, respectively. These figures clearly demonstrate that the composition and process design according to the present invention achieve a microstructure mainly composed of ferrite with intragranular nanoprecipitates, bainite and retained austenite. This microstructure provides a good match of low yield strength, high tensile strength, ultra-high plasticity and high hole expansion rate, resulting in excellent overall performance.
  • the steel of the present invention has a good match of strength, ultra-high plasticity, and high hole expansion, making it particularly suitable for complex forming parts such as automotive chassis structures and has broad application prospects.
  • Table 1 (Unit: mass percentage) C Si Mn P S Al N O Ti Mo Cu Ni Cr Nb V B Example 1, 9 0.27 1.54 2.03 0.013 0.0022 0.75 0.0025 0.0023 - 0.2 - - - 0.03 0.08 0.0005
  • Example 2 10 0.16 0.81 1.03 0.009 0.0025 0.33 0.0028 0.0022 0.20 - 0.2 - 0.5 - 0.04 0.0002
  • Example 3 11 0.35 1.75 1.82 0.016 0.0030 1.96 0.0022 0.0021 0.10 - - 0.1 - - - 0.0008
  • 12 0.21 1.86 1.27 0.019 0.0027 0.45 0.0046 0.0030 - 0.4 - - - - - 0.0003
  • Example 5 13 0.33 1.44 1.55 0.011 0.00

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