WO2022042728A1 - 一种980MPa级全贝氏体型超高扩孔钢及其制造方法 - Google Patents
一种980MPa级全贝氏体型超高扩孔钢及其制造方法 Download PDFInfo
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- WO2022042728A1 WO2022042728A1 PCT/CN2021/115419 CN2021115419W WO2022042728A1 WO 2022042728 A1 WO2022042728 A1 WO 2022042728A1 CN 2021115419 W CN2021115419 W CN 2021115419W WO 2022042728 A1 WO2022042728 A1 WO 2022042728A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 140
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- ZLANVVMKMCTKMT-UHFFFAOYSA-N methanidylidynevanadium(1+) Chemical class [V+]#[C-] ZLANVVMKMCTKMT-UHFFFAOYSA-N 0.000 description 3
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- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
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- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
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- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G3/00—Apparatus for cleaning or pickling metallic material
- C23G3/02—Apparatus for cleaning or pickling metallic material for cleaning wires, strips, filaments continuously
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2261/00—Product parameters
- B21B2261/20—Temperature
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Definitions
- the invention belongs to the field of high-strength steel, and in particular relates to a 980MPa grade full-bainite ultra-high hole-expanding steel and a manufacturing method thereof.
- the lightweight of passenger cars is not only the development trend of the automobile industry, but also the requirements of laws and regulations.
- the fuel consumption is stipulated in the laws and regulations, in fact, it is a disguised requirement to reduce the weight of the body, which is reflected in the requirement of high strength, thinning and light weight.
- High-strength weight reduction is an inevitable requirement for subsequent new models, which will inevitably lead to higher steel grades and changes in the chassis structure.
- the requirements for material properties, surface, and molding technology will be improved, such as Hydroforming, hot stamping, laser welding, etc., and then transform the material's high strength, stamping, flanging, springback and fatigue properties.
- the development of domestic high-strength and high-hole-expanding steel not only has a relatively low strength level, but also has poor performance stability.
- the high-hole-expansion steel used by domestic auto parts companies is basically high-strength steel with a tensile strength below 600MPa, and the competition for high-hole-expansion steel below 440MPa is fierce.
- the high hole-expanding steel with a tensile strength of 780MPa is gradually being used in batches, but higher requirements are also put forward for the two important indicators of elongation and hole expansion.
- the 980MPa-level high hole-expanding steel is still in the stage of R&D and certification, and has not yet reached the stage of mass use.
- the hole expansion ratio of a material is closely related to many factors, the most important factors include the uniformity of the structure, the level of inclusion and segregation control, the different structure types, and the measurement of the hole expansion ratio.
- a single homogeneous structure is beneficial to obtain a higher hole expansion ratio, while a dual-phase or multi-phase structure is usually not conducive to the improvement of the hole expansion ratio.
- the purpose of the present invention is to provide a 980MPa grade full bainitic ultra-high hole expanding steel and a manufacturing method thereof.
- the yield strength of the high hole expanding steel is ⁇ 800MPa
- the tensile strength is ⁇ 980MPa
- the hole expansion rate can reach more than 60%. It can be used in parts of passenger car chassis such as control arms and subframes that require high strength, thinning and complex forming.
- the technical scheme of the present invention is:
- composition design of the present invention adopts a lower C content, which can ensure that the user has excellent weldability during use, and ensures that the obtained bainite structure has excellent matching of strength and hole expansion ratio.
- the 980MPa grade full-bainite ultra-high hole-expanding steel described in the present invention has the following chemical composition weight percentages: C 0.05-0.10%, Si ⁇ 2.0%, Mn 1.0-2.0%, P ⁇ 0.02%, S ⁇ 0.003%, Al 0.02 ⁇ 0.08%, N ⁇ 0.004%, Mo 0.1 ⁇ 0.5%, Ti 0.01 ⁇ 0.05%, the rest are Fe and other inevitable impurities.
- the 980MPa grade fully bainitic ultra-high hole-expanding steel according to the present invention contains Cr and/or B, and the content of Cr is preferably 0.20-0.50%, and the content of B is preferably 0.0005-0.002%.
- the Cu and Ni contents are respectively preferably ⁇ 0.3%; the Cr content is preferably 0.2-0.4%; the B content is preferably 0.0005-0.0015%, and the Ca content is preferably ⁇ 0.002%.
- the 980MPa grade full bainitic ultra-high hole-expanding steel according to the present invention has the following chemical composition weight percentages: C 0.05-0.10%, Si ⁇ 2.0%, Mn 1.0-2.0%, P ⁇ 0.02 %, S ⁇ 0.003%, Al 0.02 ⁇ 0.08%, N ⁇ 0.004%, Mo 0.1 ⁇ 0.5%, Ti 0.01 ⁇ 0.05%, Cr ⁇ 0.5%, B ⁇ 0.002%, Ca ⁇ 0.005%, Nb ⁇ 0.06%, V ⁇ 0.05%, Cu ⁇ 0.5%, Ni ⁇ 0.5%, the rest are Fe and other inevitable impurities, and the fully bainitic ultra-high hole expanding steel contains at least Cr, B, Ca, Nb, V, Cu and one or more elements of Ni, preferably at least Cr and/or B.
- the C content is 0.06-0.09%.
- the Mn content is 1.4-1.8%.
- the S content is controlled below 0.0015%.
- the Al content is 0.02-0.05%.
- the N content is controlled below 0.003%.
- the Ti content is 0.01-0.03%.
- the Mo content is 0.15-0.35%.
- the O content is controlled within 30 ppm.
- the Si content is 0.05-2.0%.
- the microstructure of the ultra-high hole-expanding steel of the present invention is full bainite.
- the ultra-high hole-expanding steel of the present invention has a yield strength ⁇ 800MPa, preferably ⁇ 830MPa, more preferably ⁇ 850MPa, more preferably ⁇ 880MPa, tensile strength ⁇ 980MPa, preferably ⁇ 1000MPa, more preferably ⁇ 1020MPa, and transverse elongation A 50 ⁇ 10%, hole expansion ratio ⁇ 60%, preferably ⁇ 70%, through the cold bending performance test (d ⁇ 4a, 180°).
- the impact toughness at -40°C of the ultra-high hole-expanding steel of the present invention is ⁇ 40J, preferably ⁇ 50J, more preferably ⁇ 60J.
- the impact toughness at -40°C of the ultra-high hole-expanding steel of the present invention is greater than or equal to 70J.
- the ultra-high hole-expanding steel of the present invention has a yield strength of ⁇ 850 MPa, a tensile strength of ⁇ 1020 MPa, a transverse elongation A 50 ⁇ 10%, a hole expansion rate of ⁇ 70%, and an impact toughness at -40°C ⁇ 50J, passed the cold bending performance test (d ⁇ 4a, 180°).
- the ultra-high hole-expanding steel of the present invention has a yield strength of ⁇ 830 MPa, a tensile strength of ⁇ 1000 MPa, a transverse elongation A 50 ⁇ 10%, a hole expansion rate of ⁇ 70%, and impact at -40°C Toughness ⁇ 60J, passed the cold bending performance test (d ⁇ 4a, 180°).
- the ultra-high hole-expanding steel of the present invention has a yield strength ⁇ 900 MPa, a tensile strength ⁇ 1040 MPa, an elongation transverse A 50 ⁇ 10%, a hole expansion rate ⁇ 65%, and the impact at -40 ° C Toughness ⁇ 40J, passed the cold bending performance test (d ⁇ 4a, 180°).
- Carbon the basic element in steel, is also one of the important elements in the present invention. Carbon expands the austenite phase region and stabilizes the austenite. As an interstitial atom in steel, carbon 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. In the present invention, in order to obtain ultra-high strength and ultra-high hole expansion ratio, it is necessary to obtain a single-phase uniform low-carbon bainite structure.
- Silicon the basic element in steel, is also one of the important elements in the present invention.
- the difference in silicon content has an important influence on the properties of steel, especially elongation and hole expansion.
- the silicon content is low, the retained austenite in the structure is less, and the elongation is relatively low; when the silicon content reaches more than 0.8%, the retained austenite content in the structure increases under the same process, which is conducive to improving the elongation.
- the difference in silicon content mainly affects the elongation index, and has little effect on the hole expansion ratio. Since more silicon is added to the steel, it is easy to increase the load of the rolling mill, and it is also unfavorable for the surface of the steel.
- the Si content in the steel should not be too high, usually not more than 2.0%. According to the different needs of actual users, two ideas of low silicon and high silicon can be adopted respectively in the composition design.
- Mn is an important element to expand the austenite phase region, which can reduce the critical quenching rate of steel, stabilize austenite, refine grains, and delay the transformation of austenite to pearlite.
- the Mn content should generally be controlled at more than 1.0%; at the same time, the Mn content should generally not exceed 2.0%, otherwise Mn segregation is likely to occur during steelmaking, and slab continuous casting is also prone to Thermal cracking occurs. Therefore, the content of Mn in the steel is generally controlled at 1.0-2.0%, preferably in the range of 1.4-1.8%.
- Phosphorus is an impurity element in steel. P is easy to segregate on the grain boundary. When the content of P in the steel is high ( ⁇ 0.1%), Fe 2 P is formed to precipitate around the grain, reducing the plasticity and toughness of the steel, so the lower the content, the better. It is better to control within 0.02% without increasing the cost of steelmaking.
- Sulfur is an impurity element in steel.
- S in steel usually combines with Mn to form MnS inclusions, especially when the content of S and Mn is high, more MnS will be formed in the steel, and MnS itself has a certain plasticity.
- the deformation in the rolling direction not only reduces the transverse plasticity of the steel, but also increases the anisotropy of the structure, which is unfavorable for the hole expansion performance. Therefore, the lower the S content in the steel, the better.
- the Mn content in the present invention must be at a higher level, in order to reduce the MnS content, the S content should be strictly controlled, and the S content should be controlled within 0.003%.
- the preferable range is 0.0015% or less.
- the role of aluminum in steel is mainly deoxidation and nitrogen fixation.
- the main role of Al is to deoxidize and refine grains.
- the content of Al is usually controlled at 0.02-0.08%; if the content of Al is less than 0.02%, it cannot achieve the effect of refining grains; similarly, When the Al content is higher than 0.08%, the grain refinement effect is saturated. Therefore, the content of Al in the steel can be controlled between 0.02-0.08%, and the preferred range is between 0.02-0.05%.
- Nitrogen is an impurity element in the present invention, and the lower the content, the better. But nitrogen is an inevitable element in the steelmaking process. Although its content is small, when combined with strong carbide forming elements such as Ti, the formed TiN particles have a very adverse effect on the properties of the steel, especially on the hole expansion performance. Due to the square shape of TiN, there is a large stress concentration between its sharp corners and the matrix. During the process of hole expansion and deformation, the stress concentration between TiN and the matrix is easy to form cracks, thereby greatly reducing the hole expansion performance of the material. Under the premise of controlling the nitrogen content as much as possible, the lower the content of strong carbide-forming elements such as Ti, the better. In the present invention, a trace amount of Ti is added to fix nitrogen, so as to minimize the adverse effects brought by TiN. Therefore, the nitrogen content should be controlled below 0.004%, preferably below 0.003%.
- Titanium is one of the important elements in the present invention. Ti mainly plays two roles in the present invention: one is to combine with the impurity element N in the steel to form TiN, which plays a part of "fixing nitrogen”; the other is to form a certain amount of finely dispersed TiN in the subsequent welding process of the material , suppress the austenite grain size, refine the structure and improve the low temperature toughness. Therefore, the content of Ti in the steel is controlled in the range of 0.01-0.05%, preferably in the range of 0.01-0.03%.
- Molybdenum is one of the important elements in the present invention.
- the addition of molybdenum to steel can greatly delay the transformation of ferrite and pearlite. This effect of molybdenum is beneficial to the adjustment of various processes in the actual rolling process. For example, after the end of the final rolling, it can be cooled in stages, or it can be air-cooled first and then water-cooled. In the present invention, the process of air cooling and then water cooling or direct water cooling after rolling is adopted.
- the addition of molybdenum can ensure that structures such as ferrite or pearlite will not be formed during the air cooling process.
- the deformed austenite during the air cooling process can Dynamic recovery occurs, which is beneficial to improve the uniformity of the structure; molybdenum has strong resistance to welding softening. Since the main purpose of the present invention is to obtain a single low-carbon martensite and a small amount of retained austenite, and the low-carbon martensite is prone to softening after welding, adding a certain amount of molybdenum can effectively reduce welding softening degree. Therefore, the content of molybdenum should be controlled between 0.1-0.5%, preferably in the range of 0.15-0.35%.
- Chromium is one of the elements that can be added in the present invention.
- the addition of a small amount of chromium element is not to improve the hardenability of steel, but to combine with B, which is conducive to the formation of acicular ferrite structure in the welding heat-affected zone after welding, which can greatly improve the low-temperature toughness of the welding heat-affected zone.
- the final application parts involved in the present invention are passenger car chassis products, the low temperature toughness of the welded heat affected zone is an important indicator. In addition to ensuring that the strength of the welding heat-affected zone cannot be reduced too much, the low-temperature toughness of the welding heat-affected zone must also meet certain requirements.
- chromium itself also has a certain resistance to welding softening. Therefore, the addition amount of chromium element in steel is generally ⁇ 0.5%, and the preferred range is 0.2-0.4%.
- Boron is one of the elements that can be added in the present invention.
- the role of boron in steel is mainly to segregate at the original austenite grain boundaries to inhibit the formation of pro-eutectoid ferrite; the addition of boron to steel can also greatly improve the hardenability of steel.
- the main purpose of adding trace boron is not to improve the hardenability, but to combine with chromium to improve the structure of the welding heat-affected zone and obtain acicular ferrite structure with good toughness.
- the addition of boron element in steel is generally controlled below 0.002%, and the preferred range is between 0.0005-0.0015%.
- Calcium is an addable element in the present invention.
- Calcium can improve the morphology of sulfides such as MnS, so that elongated sulfides such as MnS become spherical CaS, which is beneficial to improve the morphology of inclusions, thereby reducing the adverse effect of elongated sulfides on hole expansion performance.
- the addition of calcium oxide will increase the amount of calcium oxide, which is detrimental to the hole expansion performance. Therefore, the addition amount of steel grade calcium is usually ⁇ 0.005%, and the preferred range is ⁇ 0.002%.
- Oxygen is an unavoidable element in the steelmaking process.
- the content of O in the steel can generally reach below 30 ppm after deoxidation, which will not cause obvious adverse effects on the performance of the steel plate. Therefore, it is sufficient to control the O content in the steel within 30 ppm.
- Niobium is one of the elements that can be added in the present invention. Similar to titanium, niobium is a strong carbide element in steel. The addition of niobium to steel can greatly increase the unrecrystallized temperature of steel. In the finishing rolling stage, deformed austenite with higher dislocation density can be obtained. In the subsequent transformation process The final phase transition structure can be refined. However, the addition amount of niobium should not be too much. On the one hand, the addition amount of niobium exceeds 0.06%, which is easy to form relatively coarse carbonitrides of niobium in the structure, which consumes some carbon atoms and reduces the precipitation strengthening effect of carbides.
- the high content of niobium also easily causes the anisotropy of the hot-rolled austenite structure, which is inherited to the final structure in the subsequent cooling transformation process, which is detrimental to the hole expansion performance. Therefore, the niobium content in the steel is usually controlled to be ⁇ 0.06%, and the preferred range is ⁇ 0.03%.
- Vanadium is an addable element in the present invention. Like titanium and niobium, vanadium is also a strong carbide former. However, the carbides of vanadium have a low solid solution or precipitation temperature, and are usually all dissolved in austenite in the finishing rolling stage. Vanadium begins to form in ferrite only when the temperature is lowered to start the phase transformation. Since the solid solubility of vanadium carbides in ferrite is greater than that of niobium and titanium, the size of vanadium carbides formed in ferrite is relatively large, which is not conducive to precipitation strengthening and contributes far to the strength of steel.
- the addition amount of vanadium in steel is usually ⁇ 0.05%, and the preferred range is ⁇ 0.03%.
- Copper is an additive element in the present invention. Adding copper to steel can improve the corrosion resistance of steel. When it is added together with P element, the corrosion resistance effect is better; to a strong precipitation strengthening effect. However, the addition of Cu is easy to form the phenomenon of "Cu embrittlement" during the rolling process. In order to make full use of the effect of improving the corrosion resistance of Cu in some applications, and at the same time not cause significant "Cu embrittlement" phenomenon, usually Cu The content of the element is controlled within 0.5%, preferably within 0.3%.
- Nickel is an additive element in the present invention.
- the addition of nickel to steel has certain corrosion resistance, but the corrosion resistance effect is weaker than that of copper.
- the addition of nickel to steel has little effect on the tensile properties of steel, but it can refine the structure and precipitation of steel, and greatly improve the low temperature toughness of steel. ; At the same time, adding a small amount of nickel can inhibit the occurrence of "Cu brittleness" in the steel added with copper.
- the addition of higher nickel has no obvious adverse effect on the properties of the steel itself. If copper and nickel are added at the same time, it can not only improve the corrosion resistance, but also refine the structure and precipitation of the steel, greatly improving the low temperature toughness. But since copper and nickel are both relatively precious alloying elements. Therefore, in order to minimize the cost of alloy design, the addition amount of nickel is usually ⁇ 0.5%, and the preferred range is ⁇ 0.3%.
- the manufacturing method of the 980MPa grade full bainitic ultra-high hole expanding steel according to the present invention comprises the following steps:
- Rolling temperature 950 ⁇ 1100°C, under 3-5 passes above 950°C and the accumulated deformation is ⁇ 50%, preferably ⁇ 70%, the main purpose is to refine the austenite grains; to 930-950 °C, and then carry out 5-7 passes of finishing rolling and the cumulative deformation is ⁇ 70%, preferably ⁇ 80%; the final rolling temperature is 800-930 °C;
- the strip After 0-10 seconds of air cooling for dynamic recovery and dynamic recrystallization, and then water cooling, the strip is water-cooled to the bainite transformation temperature range at a cooling rate of ⁇ 10°C/s, preferably 10-60°C/s. Between B s and B f , use air cooling (cooling speed > 20°C/h) to accelerate the cooling of the steel coil to room temperature after coiling; the preferred coiling temperature is 410-550°C;
- the strip pickling speed is adjusted within the interval of 30-100m/min, the pickling temperature is controlled between 75-85°C, and the tensile correction rate is controlled at ⁇ 2% to reduce the loss of strip elongation; at 35- Rinse in the temperature range of 50°C, and dry the surface of the strip between 120-140°C and apply oil.
- rinsing is performed at a temperature range of 35-50° C., and the surface of the strip is dried and oiled at a temperature of 120-140° C.
- the innovation of the present invention is:
- the invention adopts the design idea of single-phase low-carbon bainite, adopts suitable finishing rolling temperature and air cooling or direct water cooling after rolling, and adopts air cooling or other modes that can accelerate the cooling of the steel coil after coiling.
- the temperature of the steel coil is cooled down to room temperature as soon as possible, and a single-phase bainite with a uniform and fine structure is finally obtained, which shows high plasticity, toughness, good cold bending performance and ultra-high hole expansion rate.
- the rhythm of the rolling process should be completed as quickly as possible.
- air cooling for different times is performed first, or laminar cooling can be performed directly after finishing rolling.
- the main purpose of air cooling is as follows: Due to the high content of manganese and molybdenum in the composition design, manganese is an element that stabilizes austenite, while molybdenum greatly delays ferrite and pearlite transformation. Therefore, in the process of air cooling for a certain period of time, the rolled deformed austenite will not undergo phase transformation, that is, the ferrite structure will not be formed, but dynamic recrystallization and relaxation process will occur.
- the dynamic recrystallization of deformed austenite can form nearly equiaxed austenite with a uniform structure, and the dislocation inside the austenite grains will be greatly reduced after relaxation.
- the combination of the two can be used in the subsequent water cooling laminar cooling In the process, single-phase bainite with uniform and fine structure is obtained.
- the water cooling rate of the strip is required to be ⁇ 10°C/s.
- the microstructure involved in the present invention is low-carbon bainite, as long as the strip steel is cooled to the bainite transformation temperature range, that is, between B s ⁇ B f , at a cooling rate of ⁇ 10°C/s after finishing rolling Can be rolled between. Due to the long bainite transformation time, the coil still undergoes transformation after coiling. Therefore, in order to obtain high-strength steel with excellent strength, plasticity and hole expansion ratio, it is necessary to pass the coiled steel coil through air cooling or other forced cooling modes (cooling rate>20°C/h, preferably ⁇ 25°C/h) as soon as possible to reduce the temperature of the steel coil to room temperature, so as to obtain a single-phase uniform and fine bainite structure. Based on this innovative composition and process design idea, the present invention can obtain 980MPa grade full bainitic ultra-high hole-expanding steel with excellent strength, plasticity, toughness, cold-bending and hole-expanding properties.
- the steel coil or steel plate has excellent matching of strength, plasticity, toughness and hole expansion ratio, and also has good cold bending performance and hole expansion and flanging performance. Its yield strength is ⁇ 800MPa, tensile strength is ⁇ 980MPa, and Hot-rolled or pickled ultra-high hole-expanding steel with a thickness of 2-6mm, with good elongation (transverse A 50 ⁇ 8%), impact toughness and hole-expanding performance (hole-expansion rate ⁇ 60%), can be applied It has a very broad application prospect in the manufacture of parts and components that require complex forming such as automobile chassis and sub-frames that require high-strength thinning, reaming and flanging.
- Fig. 1 is a process flow diagram of the method for manufacturing the 980MPa grade fully bainitic ultra-high hole-expanding steel according to the present invention.
- FIG. 2 is a schematic diagram of the rolling process in the manufacturing method of the 980MPa grade fully bainitic ultra-high hole-expanding steel according to the present invention.
- FIG. 3 is a schematic diagram of the cooling process in the manufacturing method of the 980MPa grade fully bainitic ultra-high hole-expanding steel according to the present invention.
- FIG. 4 is a typical metallographic photograph of Example 3 of the ultra-high hole-expanding steel according to the present invention.
- FIG. 5 is a typical metallographic photograph of Example 5 of the ultra-high hole-expanding steel according to the present invention.
- FIG. 6 is a typical metallographic photograph of Example 7 of the ultra-high hole-expanding steel according to the present invention.
- the manufacturing method of 980MPa grade full bainitic ultra-high hole expanding steel according to the present invention includes the following steps:
- Rolling temperature 950 ⁇ 1100°C, under 3-5 passes above 950°C, and the accumulated deformation is ⁇ 50%; then the intermediate billet is warmed to 930-950°C, and then 5-7 passes of finishing rolling are carried out And the accumulated deformation is ⁇ 70%; the final rolling temperature is 800-930°C;
- the strip After 0-10 seconds of air cooling for dynamic recovery and dynamic recrystallization, and then water cooling, the strip is water-cooled to the bainite transformation temperature range between B s and B f at a cooling rate of ⁇ 10°C/s. After coiling, use air cooling (cooling speed > 20°C/h) to accelerate the cooling of the steel coil until it reaches room temperature;
- the operating speed of strip pickling is adjusted within the range of 30-100m/min, the pickling temperature is controlled between 75-85°C, the pull-straightening rate is controlled within ⁇ 2%, the rinsing is carried out in the temperature range of 35-50°C, and the Dry the surface between 120-140°C and apply oil.
- Tables 2 and 3 are the production process parameters of the steel examples of the present invention, wherein the thickness of the billet in the rolling process is 230 mm; Table 4 is the embodiment of the present invention.
- Mechanical properties of steel plates Tensile properties (yield strength, tensile strength, elongation) are tested according to ISO6892-2-2018 international standard; hole expansion rate is tested according to ISO16630-2017 international standard; impact energy is tested according to ISO14556-2015 international standard.
- the yield strength of the steel coil is ⁇ 800MPa, while the tensile strength is ⁇ 980MPa, the elongation is usually ⁇ 10%, the impact energy is relatively stable, the low temperature impact energy at -40°C is ⁇ 40J, and the hole expansion ratio is ⁇ 60%.
- the 980MPa high-strength steel involved in the present invention has excellent matching of strength, plasticity, toughness and hole expansion performance, and is especially suitable for parts such as automobile chassis structures that require high-strength thinning and hole expansion and flanging. Arms, etc., can also be used for complex forming parts such as wheels, etc. that need to be turned, and has broad application prospects.
- the impact energy is measured by the actual thickness, which is equivalently converted into the impact energy of a standard sample of 10*10*55mm in proportion.
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Abstract
Description
实施例 | C | Si | Mn | P | S | Al | N | Mo | Ti | Cr | B | Ca | Nb | V | Cu | Ni | O |
1 | 0.055 | 0.08 | 1.48 | 0.013 | 0.0028 | 0.055 | 0.0029 | 0.35 | 0.030 | 0.28 | 0.0010 | 0.002 | / | / | 0.20 | 0.10 | 0.0028 |
2 | 0.084 | 1.55 | 1.77 | 0.009 | 0.0010 | 0.040 | 0.0038 | 0.18 | 0.049 | 0.36 | 0.0012 | / | 0.060 | / | / | / | 0.0025 |
3 | 0.073 | 0.66 | 1.02 | 0.014 | 0.0020 | 0.079 | 0.0033 | 0.26 | 0.020 | / | 0.0020 | / | / | 0.04 | 0.30 | 0.20 | 0.0022 |
4 | 0.090 | 1.08 | 1.67 | 0.010 | 0.0027 | 0.025 | 0.0025 | 0.44 | 0.046 | 0.31 | 0.0015 | 0.001 | / | 0.03 | / | 0.50 | 0.0027 |
5 | 0.060 | 0.38 | 1.26 | 0.008 | 0.0012 | 0.052 | 0.0036 | 0.12 | 0.018 | 0.50 | 0.0018 | 0.003 | / | / | / | 0.30 | 0.0026 |
6 | 0.098 | 0.22 | 1.83 | 0.011 | 0.0024 | 0.033 | 0.0030 | 0.49 | 0.028 | 0.30 | 0.0005 | / | 0.030 | / | 0.50 | / | 0.0029 |
7 | 0.051 | 1.88 | 1.39 | 0.015 | 0.0009 | 0.022 | 0.0034 | 0.25 | 0.035 | 0.32 | 0.0018 | 0.005 | 0.015 | 0.02 | / | / | 0.0021 |
8 | 0.077 | 1.24 | 1.99 | 0.009 | 0.0025 | 0.057 | 0.0022 | 0.31 | 0.010 | 0.20 | / | / | / | 0.05 | / | / | 0.0024 |
Claims (15)
- 一种980MPa级全贝氏体型超高扩孔钢,其化学成分重量百分比为:C 0.05~0.10%,Si≤2.0%,Mn 1.0~2.0%,P≤0.02%,S≤0.003%,Al 0.02~0.08%,N≤0.004%,Mo 0.1~0.5%,Ti 0.01~0.05%,O≤0.0030%,其余为Fe以及其它不可避免的杂质。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,还包括Cr≤0.5%,B≤0.002%,Ca≤0.005%,Nb≤0.06%,V≤0.05%,Cu≤0.5%,Ni≤0.5%中的一种或一种以上元素;其中,所述Nb、V含量分别优选为≤0.03%;所述Cu、Ni含量分别优选为≤0.3%;所述Cr含量优选为0.2-0.4%;B含量优选为0.0005-0.0015%;所述Ca含量优选为≤0.002%。
- 如权利要求2所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,还包括Cr≤0.5%和/或B≤0.002%。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述C含量为0.06-0.09%。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述Mn含量为1.4-1.8%。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述S含量控制在0.0015%以下,和/或所述N含量控制在0.003%以下。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述Al含量为0.02-0.05%。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述Ti含量为0.01-0.03%,和/或所述Mo含量为0.15-0.35%。
- 如权利要求1所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述超高扩孔钢的显微组织为全贝氏体。
- 如权利要求1或9所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述超高扩孔钢的屈服强度≥800MPa,抗拉强度≥980MPa,延伸率横向A 50≥10%,扩孔率≥60%,通过冷弯性能测试(d≤4a,180°);优选地,-40℃的冲击韧性≥40J。
- 如权利要求10所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述超高扩孔钢的屈服强度≥850MPa,抗拉强度≥1020MPa,延伸率横向A 50≥10%, 扩孔率≥70%,,通过冷弯性能测试(d≤4a,180°),-40℃的冲击韧性≥50J。
- 如权利要求10所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述超高扩孔钢的屈服强度≥830MPa,抗拉强度≥1000MPa,延伸率横向A 50≥10%,扩孔率≥70%,,通过冷弯性能测试(d≤4a,180°),-40℃的冲击韧性≥60J。
- 如权利要求10所述的980MPa级全贝氏体型超高扩孔钢,其特征在于,所述超高扩孔钢的屈服强度≥900MPa,抗拉强度≥1040MPa,延伸率横向A 50≥10%,扩孔率≥65%,,通过冷弯性能测试(d≤4a,180°),-40℃的冲击韧性≥40J。
- 如权利要求1~13中任何一项所述的的980MPa级全贝氏体型超高扩孔钢的制造方法,其特征是:包括如下步骤:1)冶炼、浇铸按权利要求1~8所述成分采用转炉或电炉冶炼、真空炉二次精炼后浇铸成铸坯或铸锭;2)铸坯或铸锭再加热,加热温度1100-1200℃,保温时间1~2小时;3)热轧开轧温度:950~1100℃,在950℃以上3-5道次大压下且累计变形量≥50%、优选≥70%;随后中间坯待温至930-950℃,然后进行5-7个道次精轧且累计变形量≥70%、优选≥80%;终轧温度800-930℃;4)冷却先经过0-10秒空冷以进行动态回复和动态再结晶,然后进行水冷,以≥10℃/s、优选10-60℃/s的冷速将带钢水冷至贝氏体相变温度范围即B s~B f之间,卷取后采用风冷将钢卷温度冷却至室温;优选卷取温度为410-550℃;5)酸洗带钢酸洗运行速度在30~100m/min的区间内调整,酸洗温度控制在75~85℃之间,拉矫率控制在≤2%,然后漂洗、带钢表面烘干,涂油。
- 如权利要求14所述的980MPa级全贝氏体型超高扩孔钢的制造方法,其特征是,步骤5)酸洗后,在35-50℃温度区间进行漂洗,并在120-140℃之间进行带钢表面烘干,涂油。
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US18/043,100 US20230323502A1 (en) | 2020-08-31 | 2021-08-30 | 980 mpa-grade full-bainite ultra-high hole expansion steel and manufacturing method therefor |
EP21860560.8A EP4206349A4 (en) | 2020-08-31 | 2021-08-30 | ULTRA-HIGH HOLE EXPANSION STEEL, 980 MPA QUALITY, FULLY BAINITE, AND METHOD FOR MANUFACTURING SAME |
JP2023513796A JP2023539648A (ja) | 2020-08-31 | 2021-08-30 | 980MPaレベルの全ベイナイト型超高穴拡げ性鋼及びその製造方法 |
KR1020237009593A KR20230059806A (ko) | 2020-08-31 | 2021-08-30 | 980 MPa급 풀-베이나이트형의 구멍 확장성이 매우 높은 철강 및 이의 제조 방법 |
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WO2024111527A1 (ja) * | 2022-11-22 | 2024-05-30 | Jfeスチール株式会社 | 高強度熱延鋼板及びその製造方法 |
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