WO2023246904A1 - Acier d'alésage ultra-haute qualité et son procédé de fabrication - Google Patents

Acier d'alésage ultra-haute qualité et son procédé de fabrication Download PDF

Info

Publication number
WO2023246904A1
WO2023246904A1 PCT/CN2023/101852 CN2023101852W WO2023246904A1 WO 2023246904 A1 WO2023246904 A1 WO 2023246904A1 CN 2023101852 W CN2023101852 W CN 2023101852W WO 2023246904 A1 WO2023246904 A1 WO 2023246904A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel
present
rolling
strength
cooling
Prior art date
Application number
PCT/CN2023/101852
Other languages
English (en)
Chinese (zh)
Inventor
王焕荣
张晨
杨阿娜
庞厚君
范佳杰
Original Assignee
宝山钢铁股份有限公司
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 宝山钢铁股份有限公司 filed Critical 宝山钢铁股份有限公司
Publication of WO2023246904A1 publication Critical patent/WO2023246904A1/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • 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
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • 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
    • C23G3/021—Apparatus for cleaning or pickling metallic material for cleaning wires, strips, filaments continuously by dipping
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the invention belongs to the field of steel and its manufacturing method, and particularly relates to an ultra-high hole expansion steel and its manufacturing method.
  • Pickling products are commonly used for many parts in passenger cars, especially chassis and body parts. Lightweighting of passenger cars is the development trend of the automotive industry. High-strength and weight reduction is an inevitable requirement for subsequent new models. This will inevitably lead to a higher grade of steel and will also bring about changes in the chassis structure: if the parts are more complex, the materials will be required. Performance, surface and forming technologies such as hydroforming, hot stamping, laser welding, etc. have put forward higher requirements, which in turn have higher requirements for material strength, stamping, flanging, springback and fatigue properties.
  • the high-expansion steel commonly used by domestic auto parts companies is high-strength steel with a tensile strength of less than 600MPa and less than 400MPa.
  • High-expansion steel with a tensile strength of 780MPa is gradually being used in batches in China. Due to the increase in steel strength, higher requirements have been placed on the elongation and hole expansion rate of steel, two important indicators in the forming process.
  • some passenger car companies have further improved the performance requirements of materials. For example, when producing structural parts such as automobile chassis control arms, in order to reduce the stamping process and reduce costs, it is required to have high strength and high plasticity while further improving the hole expansion rate index.
  • 780MPa high-pore expansion steel mostly adopts the design idea of high silicon composition system.
  • the structure is mainly bainite.
  • some trace elements are added to the steel to provide a certain precipitation strengthening effect.
  • the surface of the pickled steel strip not only has obvious red iron scale, but also the hole expansion rate is basically between 50-65%, and the elongation rate of the bainite structure is low. None of these can meet the higher hole expansion rate proposed by the user. performance requirements.
  • Chinese patent CN103602895A provides a low-carbon Nb-Ti micro-alloyed high hole expansion steel. Its composition design features low carbon and high silicon combined with Nb-Ti micro-alloying. The hole expansion rate of the steel is ⁇ 50%. but The design of high silicon content usually results in red iron scale on the surface of the steel plate. In addition, the coiling temperature range required to form bainite is around 500°C. It is difficult to control the temperature of the entire length of the steel coil, which can easily cause large fluctuations in the performance of the entire length.
  • Chinese patent CN105821301A provides an 800MPa grade hot-rolled high-strength and high-pore-expanding steel. Its composition design feature is also low carbon and high silicon combined with Nb-Ti microalloying. The Ti content in the steel is very high, ranging from 0.15 to 0.18%. Therefore, in the actual production process, the surface of strip steel with this composition will have defects such as red iron scale, and ultra-high Ti content will easily form coarse TiN in the steel, which is very detrimental to the stability of the hole expansion rate.
  • Chinese patent CN108570604A provides a 780MPa grade hot-rolled, pickled, high-pore-expanding steel whose composition design features are low carbon, high aluminum and high chromium.
  • the process design adopts a three-stage cooling process. However, this three-stage cooling process is very difficult to control, and the actual hole expansion rate is not high.
  • Chinese patent CN114107792A provides a 780MPa grade hot-rolled, pickled, high-pore-expanding steel. Its composition is characterized by low carbon and high titanium with an appropriate amount of molybdenum added. Since the phase transformation process of molybdenum-containing steel is relatively slow, the phase transformation process mainly occurs after coiling. Therefore, in the actual production process of this steel, there are problems such as low strength of the inner and outer rings of the steel coil.
  • the object of the present invention is to provide an ultra-high hole expansion steel and a manufacturing method thereof.
  • the steel of the present invention has good surface quality, excellent and stable mechanical properties, and can be used in passenger car chassis parts such as control arms and subframes that require high strength and thinning.
  • the elongation of a material is inversely proportional to the hole expansion rate, that is, the higher the elongation, the lower the hole expansion rate; conversely, the lower the elongation, the higher the hole expansion rate. Therefore, it is very difficult to achieve high elongation and ultra-high hole expansion rate at the same time, and it is even more difficult to ensure uniform performance across the entire length of the strip. Under the same or similar strengthening mechanism, the higher the strength of the material, the lower the hole expansion rate. In order to obtain steel with good plasticity and expansion and flanging properties, a better balance between the two is needed.
  • the addition of more silicon elements seems to be indispensable for high strength, high plasticity and high hole expansion steel.
  • the high silicon composition design brings poor steel plate surface, that is, when hot The red iron scale defects formed in the rolling process are difficult to completely remove in the subsequent pickling process, causing striped red iron scale to appear on the surface of the pickled high-strength steel, seriously affecting the surface quality.
  • the invention adopts the composition design of low silicon (or even no Si), low carbon and high aluminum to avoid the appearance of red iron scale on the surface of strip steel, thereby improving the surface quality of pickling high-strength steel.
  • the first aspect of the invention provides a steel whose composition in weight percentage is: C 0.03 ⁇ 0.09%, Si ⁇ 0.2%, Mn 0.5 ⁇ 2.0%, P ⁇ 0.02%, S ⁇ 0.003%, Al 0.2 ⁇ 1.2%, N ⁇ 0.004%, Ti 0.05 ⁇ 0.20%, Mo 0.05 ⁇ 0.5%, Mg ⁇ 0.005%, O ⁇ 0.003%, B ⁇ 0.001%, the balance is Fe and other inevitable impurities, so
  • the relationship between C, Mn, Mo and B in the above steel satisfies: 0.25 ⁇ 2 ⁇ C+Mn/3+Mo+150 ⁇ B ⁇ 1.5,
  • the value before the percent sign is entered into the weight percentage of the corresponding element when calculating. For example, when the C content in steel is 0.05%, substitute the value 0.05 for calculation.
  • the content of chemical elements in steel refers to the weight fraction of the element.
  • the steel of the present invention also contains one or more selected from the group consisting of Nb, V, Cu, Ni and Cr, wherein, in terms of weight percentage, Nb ⁇ 0.06%, V ⁇ 0.10%, preferably ⁇ 0.05wt%, Cu ⁇ 0.5%, preferably ⁇ 0.3%, Ni ⁇ 0.5%, preferably ⁇ 0.3%, Cr ⁇ 0.5%, preferably ⁇ 0.3%.
  • the composition of the above-mentioned steel also satisfies at least one of the following: Si ⁇ 0.15wt%, Mn 1.0 ⁇ 1.6wt%, S ⁇ 0.0015wt%, Al 0.5 ⁇ 1.0wt%, N ⁇ 0.003wt%, Ti 0.07 ⁇ 0.11wt%, Mo 0.15 ⁇ 0.45wt%, Ni ⁇ 0.03wt%, B ⁇ 0.0005wt%.
  • Carbon is a basic element in steel and one of the important elements in the present invention. Carbon can expand the austenite phase area and stabilize austenite. As an interstitial atom in steel, carbon plays a very important role in improving the strength of steel, among which it has the greatest impact on the yield strength and tensile strength of steel.
  • the carbon content since the structure to be obtained is close to full ferrite, in order to obtain high-strength steel with a tensile strength of 780 MPa, the carbon content must be ensured to be above 0.03%. When the carbon content is below 0.03%, the tensile strength of the ferrite structure is difficult to reach 780MPa; but the carbon content cannot be higher than 0.09%. If the carbon content is too high, pearlite structure is easily formed during the phase change process, which is detrimental to the hole expansion performance. Therefore, the carbon content should be controlled between 0.03-0.09%.
  • Silicon is a basic element in steel, but it is an impurity element in the present invention. As mentioned before, in order to meet the user's requirements for high strength, high plasticity and ultra-high hole expansion rate, it is usually added during component design. Add more silicon. However, the high-silicon composition design brings about a reduction in the surface quality of the steel plate and more red iron sheet defects. In the present invention, in order to ensure good surface quality, the silicon content in the steel is strictly controlled. According to a large amount of statistical data in actual production, when the silicon content is below 0.2%, surface red iron scale defects can be avoided during the hot rolling process. Generally, when the silicon content is below 0.15%, it is guaranteed that no red scale will appear. Therefore, the silicon content in steel is within 0.2%, preferably within 0.15%.
  • Manganese is the most basic element in steel and one of the most important elements in the present invention.
  • Mn is an important element in expanding the austenite phase area. It can stabilize austenite, refine grains and delay the transformation of austenite to pearlite.
  • the Mn content is usually above 0.5%.
  • the Mn content generally should not exceed 2.0%, otherwise Mn segregation will easily occur during steelmaking and hot cracking will easily occur during slab continuous casting. Therefore, the Mn content in steel is 0.5-2.0%, preferably 1.0-1.6%.
  • Phosphorus is an impurity element in steel. P is easily segregated to the grain boundaries. When the content of P in the steel is high ( ⁇ 0.1%), Fe 2 P is formed and precipitates around the grains, reducing the plasticity and toughness of the steel. Therefore, the lower the content, the better. Generally, when the P content is within 0.02%, the performance of the steel is better and the cost of steelmaking will not be increased.
  • Sulfur is an impurity element in steel.
  • S in steel usually combines with Mn to form MnS inclusions. Especially when the contents of S and Mn are both high, more MnS will be formed in the steel. MnS itself has a certain degree of plasticity. During the subsequent rolling process, MnS deforms along the rolling direction, which not only reduces the transverse plasticity of the steel, but also increases the anisotropy of the structure, which is detrimental to the hole expansion performance. Therefore, the lower the S content in steel, the better. In order to reduce the MnS content, the S content needs to be strictly controlled. In the present invention, the content of S is within 0.003%, preferably below 0.0015%.
  • Aluminum is one of the most important elements in this invention.
  • the addition of aluminum into steel also plays an important role in the present invention, which is to accelerate the phase change process, so that the phase change of the strip steel is completed on the laminar cooling roller table and before coiling, so as to avoid strip coiling. After removal, due to the different cooling rates of the inner and outer rings of the steel coil, uneven precipitation of nanoscale carbides results in large fluctuations in the performance of the entire length of the strip.
  • the amount of aluminum added to steel is closely related to the austenite stabilizing elements carbon and manganese, as well as the key elements molybdenum and boron that inhibit ferrite phase transformation.
  • Nitrogen is an impurity element in the present invention, and the lower its content, the better. But nitrogen is an inevitable element in the steelmaking process. Although its content is small, it is closely related to strong carbide-forming elements such as Ti The TiN particles formed by these combinations have a very negative impact on the properties of 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 deformation, the stress concentration between TiN and the matrix can easily form a crack source, thus greatly reducing the hole expansion performance of the material. Since the present invention adopts a high titanium design in the component system, in order to minimize the adverse impact of TiN on hole expansion. Therefore, the nitrogen content in the present invention is 0.004% or less, preferably 0.003% or less.
  • Titanium is one of the important elements in the present invention.
  • Ti mainly plays two roles in the present invention: first, it combines with the impurity element N in the steel to form TiN, which plays a part of the role of "nitrogen fixation"; second, it forms a uniform dispersion from the ferrite during the coiling phase transformation process. Fine nanoscale carbides improve strength, plasticity and hole expansion rate.
  • the titanium content in the steel of the present invention is between 0.05-0.20%, preferably between 0.07-0.11%.
  • Molybdenum is one of the important elements in the present invention.
  • the addition of molybdenum to steel can greatly delay the phase transformation of ferrite and pearlite, which is beneficial to obtaining an irregular ferrite structure.
  • Molybdenum and titanium are added to the steel at the same time, and the nanoscale titanium carbide molybdenum precipitate formed has the effect of resisting high-temperature coarsening, which can ensure that no coarsening occurs for a long time after coiling and the strength is reduced.
  • molybdenum has strong resistance to welding softening. Since the main purpose of the present invention is to obtain ferrite plus nano-precipitation structure, adding a certain amount of molybdenum can effectively reduce the degree of welding softening. Therefore, the content of molybdenum in the present invention is between 0.1-0.5%, preferably between 0.15-0.45%.
  • Magnesium is one of the important elements in the present invention. Magnesium added to steel can preferentially form dispersed fine MgO during the steelmaking stage. These fine MgO can serve as nucleation points for TiN. In the subsequent continuous casting process, it can effectively increase the nucleation points of TiN and reduce the size of TiN. Since TiN has a great influence on the hole expansion rate of the final steel plate, it can easily cause the hole expansion rate to be unstable. Therefore, the Mg content in the steel of the present invention is within 0.005%.
  • Oxygen is an unavoidable element in the steelmaking process.
  • the oxygen content in the steel can generally reach less than 30 ppm after deoxidation, which will not cause obvious adverse effects on the performance of the steel plate. Therefore, the O content in the steel of the present invention is within 30 ppm.
  • Niobium is one of the additive elements in the present invention. Niobium is similar to titanium and is a strong carbide element in steel. Adding niobium to steel can greatly increase the non-recrystallization temperature of the steel. During the finishing rolling stage, deformed austenite with a higher dislocation density can be obtained. During subsequent phase transformation, The final tissue can be refined. However, the amount of niobium added cannot be Too much. On the one hand, if the amount of niobium added exceeds 0.06%, it is easy to form relatively coarse niobium carbonitrides in the structure, consuming part of the carbon atoms, thereby reducing the precipitation strengthening effect of carbides.
  • the high content of niobium can easily cause anisotropy of the hot-rolled austenite structure, which is inherited to the final structure during the subsequent cooling phase transformation process, which is detrimental to the hole expansion performance. Therefore, the niobium content in steel is usually ⁇ 0.06%, preferably ⁇ 0.03%.
  • Vanadium is an additive element in the present invention. Similar to titanium and niobium, vanadium is also a strong carbide-forming element. However, the solid solution or precipitation temperature of vanadium carbide is low, and it is usually completely dissolved in austenite during the finishing rolling stage. Only when the temperature is lowered and phase transformation begins, vanadium begins to form in the ferrite. Since the solid solubility of vanadium carbide in ferrite is greater than the solid solubility of niobium and titanium, the size of vanadium carbide formed in ferrite is larger, which is not conducive to precipitation strengthening and contributes far to the strength of steel. Less than titanium carbide or titanium molybdenum carbide. However, the formation of vanadium carbide also consumes a certain amount of carbon atoms, which is detrimental to the improvement of the strength of steel. Therefore, the added amount of vanadium in steel is usually ⁇ 0.10%, preferably ⁇ 0.05%.
  • 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 the P element, the corrosion resistance effect is better; when the amount of Cu added exceeds 1%, under certain conditions, an ⁇ -Cu precipitation phase can be formed, causing A strong precipitation strengthening effect is achieved. However, the addition of Cu can easily cause "Cu embrittlement" during the rolling process. In order to make full use of Cu's corrosion resistance improvement effect in certain applications without causing significant "Cu embrittlement", Cu is usually added. The content of elements is controlled within 0.5%, preferably within 0.3%.
  • Nickel is an additive element in the present invention. Nickel added to steel has certain corrosion resistance, but the corrosion resistance effect is weaker than that of copper. Nickel added to steel has little effect on the tensile properties of the steel, but it can refine the structure and precipitated phases of the steel, greatly improving the low-temperature toughness of the steel. ;At the same time, in steel with added copper element, adding a small amount of nickel can inhibit the occurrence of "Cu embrittlement". Adding higher nickel has no significant 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 precipitated phases of the steel, thereby greatly improving the low-temperature toughness of the steel. But both copper and nickel are relatively expensive alloy elements. Therefore, in order to reduce the cost of alloy design as much as possible, the addition amount of nickel is usually ⁇ 0.5%, preferably ⁇ 0.3%.
  • Chromium is an additive element in the present invention. Chromium is added to steel mainly to improve the strength of steel through solid solution strengthening or structure refinement. Since the structure in the present invention is fine bainitic ferrite plus nano-precipitated carbides, and after the high-temperature hooding process, the movable dislocations in the structure are reduced, making the yield strength and tensile strength of the steel better. The ratio of strength to strength is relatively high, usually reaching above 0.90. add Adding a small amount of chromium element can appropriately reduce the yield strength of steel, thereby reducing the yield-strength ratio. In addition, the addition of a small amount of chromium can also play a role in improving corrosion resistance. Usually the addition amount of chromium is ⁇ 0.5%, preferably ⁇ 0.3%.
  • Boron is an impurity element in the present invention. Since boron can quickly segregate to the austenite grain boundary during the finishing rolling stage, it strongly inhibits the ferrite phase transformation. Considering the present invention, it is expected to obtain the entire ferrite structure as ferrite before hot rolling and coiling. Therefore, the boron element content must be strictly limited.
  • the amount of boron added to steel is usually ⁇ 0.001%, preferably ⁇ 0.0005%.
  • the steel of the present invention has a yield strength of ⁇ 700MPa, a tensile strength of ⁇ 780MPa, an elongation in the transverse direction A50 of ⁇ 17%, and a hole expansion rate of ⁇ 80%.
  • the yield strength of the steel is below 850MPa
  • the tensile strength is below 900MPa
  • the transverse elongation A50 is below 25%
  • the hole expansion rate is below 115%.
  • the structure of the steel of the present invention is more than 95% by volume, preferably more than 97% by volume, of ferrite and less than 5% by volume, preferably less than 3% by volume of pearlite, and the ferrite contains dispersed nanoscale carbonization. things.
  • the present invention adds more Al in the composition design, and at the same time controls the contents of C, Mn, Mo, and B elements that have an important impact on the ferrite phase transformation, so that the strip steel can
  • the air cooling stage of the laminar cooling roller table before coiling completes the phase change process, thereby obtaining a strip with good uniformity of structure and precipitation, and improving the performance stability of the entire length of the strip.
  • Another aspect of the present invention provides a method for manufacturing the above-mentioned steel, comprising the following steps:
  • the molten steel is smelted in a converter or electric furnace, then refined in a vacuum furnace, and then cast into a slab or ingot;
  • Opening rolling temperature 1050 ⁇ 1150°C, 3 ⁇ 5 passes of rough rolling at high pressure above 1050°C and cumulative deformation ⁇ 50% to obtain an intermediate billet, and then air-cooling or water-cooling the intermediate billet to 950 ⁇ 1000°C. Then perform 5 to 7 passes of finishing rolling with the cumulative deformation ⁇ 70%, and the final rolling temperature is 850 to 950°C to obtain a steel strip;
  • Laminar flow cooling is used for cooling. After final rolling, the above steel strip is water-cooled to 550 ⁇ 650°C at a cooling rate of ⁇ 10°C/s for coiling. After coiling, it is cooled to room temperature at a cooling rate of ⁇ 50°C/h to obtain heat.
  • Rolld strip steel After final rolling, the above steel strip is water-cooled to 550 ⁇ 650°C at a cooling rate of ⁇ 10°C/s for coiling. After coiling, it is cooled to room temperature at a cooling rate of ⁇ 50°C/h to obtain heat.
  • the above method also includes step 4) pickling, wherein the pickling speed of the hot-rolled strip is 30-140m/min, the pickling temperature is controlled at 75-85°C, and the tensile straightening rate is controlled at ⁇ 3%. , rinse at a temperature range of 35 to 50°C, dry and oil the surface at a temperature of 120 to 140°C.
  • the present invention adopts specially controlled low-carbon and high-aluminum composition design, and can obtain a high-surface ultra-high hole expansion steel with excellent performance stability through high-temperature coiling process on the hot continuous rolling production line. Due to the innovative design of the component system, the strip steel can complete the phase transformation before coiling, avoiding the structural uniformity problems caused by different cooling rates in the inner, middle and outer rings of the steel coil after coiling, making the steel coil performance uniform Greatly improve.
  • the present invention uses Mg deoxidation to preferentially form dispersed and fine MgO in the molten steel, creating more nucleation points for the formation of TiN in the subsequent continuous casting process, which can effectively refine TiN particles and improve Hole expansion rate stability.
  • the rolling opening temperature of the present invention is 1050-1150°C, and 3-5 passes of rough rolling are performed under high pressure and the cumulative deformation is ⁇ 50% above 1050°C.
  • the main purpose is to refine the austenite grains while retaining more More solid solution titanium.
  • the intermediate billet is then air-cooled or water-cooled to 950-1000°C, and then subjected to 5 to 7 passes of finish rolling with a cumulative deformation of ⁇ 70%.
  • the steel plate is water-cooled to 550-650°C at a cooling rate of ⁇ 10°C/s, and then slowly cooled to room temperature after coiling.
  • the specific manufacturing process is shown in Figure 2.
  • the rolling rhythm should be completed as quickly as possible to ensure that more titanium is solidly dissolved in austenite.
  • the strip is cooled online to 550-650°C at a cooling rate of ⁇ 10°C/s to obtain ferrite and nano-precipitation structures.
  • the strip steel completes the entire phase transformation process within 5-20 seconds on the layer-cooled roller table, thereby obtaining a more uniform structure and precipitation.
  • the thermal stress unevenness generated inside the high-temperature coiled steel coil will be reduced and homogenized during pickling and straightening, which further improves the structural uniformity of the steel and is conducive to obtaining high-quality Pickled ultra-high hole expansion steel with surface, high plasticity, ultra-high hole expansion rate and good performance stability.
  • the solution of the present invention has the following advantages:
  • Chinese patents CN103602895A and CN105821301A adopt high-silicon composition designs, but the present invention adopts a unique composition design of low silicon or even no silicon, low carbon and high aluminum, which can avoid the appearance of red iron scale on the surface of the strip and improve the pickling strength. Surface quality of steel.
  • the present invention adopts a new low-carbon and high-aluminum composition design idea.
  • By accurately controlling the content of carbon, manganese, molybdenum and boron, high strength, high plasticity and ultra-high hole expansion can be obtained by using a simple rolling process. Hot-rolled steel coils with good matching rate and full-length performance stability.
  • the internal stress in the ferrite structure is reduced and homogenized.
  • the uniformly fine and dispersed nano-scale carbides in the ferrite give the steel plate high strength and high plasticity on the one hand, and at the same time, the good structure and uniform distribution of internal stress give the steel plate an ultra-high hole expansion rate.
  • the method of the present invention can be used to produce ultra-high hole expansion steel with yield strength ⁇ 700MPa and tensile strength ⁇ 780MPa, but with good elongation (transverse A50 ⁇ 17%) and high hole expansion performance (hole expansion rate ⁇ 80% ), shows good performance stability, can achieve excellent surface, strength, plasticity and hole expansion performance matching, and is suitable for the manufacturing of complex parts such as automobile chassis and subframes that require high-strength thinning and hole expansion flanging.
  • Figure 1 is a schematic diagram of the rolling and cooling process of steel according to the present invention.
  • Figure 2 is a typical metallographic photograph of the steel in Example 2 of the present invention.
  • Figure 3 is a typical metallographic photograph of the steel in Example 4 of the present invention.
  • Figure 4 is a typical metallographic photograph of the steel in Example 6 of the present invention.
  • the components of the steels in the examples and comparative examples of the present invention are shown in Table 1.
  • the balance of the components in Table 1 is Fe and inevitable impurities.
  • composition shown in Table 1 it is smelted in a converter or electric furnace, then secondary refined in a vacuum furnace, and then cast into a slab or ingot.
  • Opening rolling temperature 1050 ⁇ 1150°C, 3 ⁇ 5 passes of rough rolling at high pressure above 1050°C and cumulative deformation ⁇ 50% to obtain an intermediate billet, and then air-cooling or water-cooling the intermediate billet to 950 ⁇ 1000°C. Then perform 5 to 7 passes of finishing rolling with the cumulative deformation ⁇ 70%, and the final rolling temperature is 850 to 950°C to obtain strip steel;
  • Laminar flow cooling is used for cooling. After final rolling, the strip is water-cooled to 550-650°C at a cooling rate of ⁇ 10°C/s for coiling. After coiling, it is cooled to room temperature at a cooling rate of ⁇ 50°C/h.
  • Table 2 shows the production process parameters of steel according to the embodiment of the present invention.
  • Table 3 shows the performance parameters of the steels in the examples and comparative examples of the present invention.
  • the steel in Comparative Examples 1-3 is selected from CN103602895A, and the steel in Comparative Example 4 is selected from CN114107792A.
  • Table 1 gives the ingredient differences between Examples and Comparative Examples. It can be seen from Table 1 that the composition designs of the comparative examples are all low-aluminum designs, and the composition designs of comparative examples 1-3 also include high-silicon designs, while the composition designs of the present invention are silicon-free and high-aluminum. The two are completely different in composition design. different.
  • the yield strength of the steel coil obtained according to the composition and process of the present invention ⁇ 700MPa, tensile strength ⁇ 780MPa, elongation transverse A50 ⁇ 17%, hole expansion rate ⁇ 80%.
  • Comparative Examples 1 to 3 are similar to the present invention in terms of yield strength, tensile strength and elongation, the hole expansion rate index of Comparative Examples 1 to 3 is significantly lower than that of the embodiments of the present invention.
  • Figures 2 to 4 respectively show typical metallographic photos of the steels in Examples 2, 4 and 6 of the present invention.
  • the composition and process path designed in the present invention a structure mainly composed of ferrite and containing a very small amount of pearlite can be obtained.
  • the ferrite content in the steel is more than 97% by volume
  • the pearlite content is less than 3% by volume
  • the ferrite contains dispersed nanoscale carbides.
  • the steel in the embodiment of the present invention shows a good match of high strength, high plasticity and ultra-high hole expansion rate, and has excellent comprehensive performance.
  • the 780MPa high-strength steel involved in the present invention has high strength, high plasticity and ultra-high hole expansion rate, and is particularly suitable for automobile chassis structures that require high strength thinning and hole expansion flanging forming. It can also be used for the manufacture of parts such as control arms, etc., and can also be used for complex parts such as wheels that require drilling, and has broad application prospects.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

La présente invention concerne un acier d'alésage ultra-haute qualité et son procédé de fabrication. L'acier comprend les composants suivants comme exprimé en pourcentage en poids : C : 0,03-0,09 %, Si : ≤ 0,2 % ; Mn : 0,5-2,0 % ; P : ≤ 0,02 %, S : ≤ 0,003 % ; Al : 0,2-1,2 %, N : ≤ 0,004 % ; Ti : 0,05-0,20 %, Mo : 0,05-0,5 % ; Mg : ≤ 0,005 % ; O : ≤ 0,003 % ; B : ≤ 0,001 %, le reste étant constitué de Fe et d'autres impuretés inévitables. C, Mn, Mo et B dans l'acier satisfont la relation suivante : 0,25 ≤ 2 × C + Mn/3 + Mo +150 × B ≤ 1,5 ; lors du calcul, la valeur numérique présente avant le symbole de pourcentage pour le pourcentage en masse de l'élément correspondant est substituée. L'acier selon la présente invention présente une excellente combinaison de résistance, de plasticité et de performances d'alésage, et peut être utilisé dans des pièces de châssis de voitures de tourisme nécessitant une résistance et un amincissement élevés, telles qu'un bras de commande et un sous-châssis.
PCT/CN2023/101852 2022-06-22 2023-06-21 Acier d'alésage ultra-haute qualité et son procédé de fabrication WO2023246904A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN202210714704.XA CN117305693A (zh) 2022-06-22 2022-06-22 一种超高扩孔钢及其制造方法
CN202210714704.X 2022-06-22

Publications (1)

Publication Number Publication Date
WO2023246904A1 true WO2023246904A1 (fr) 2023-12-28

Family

ID=89279929

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2023/101852 WO2023246904A1 (fr) 2022-06-22 2023-06-21 Acier d'alésage ultra-haute qualité et son procédé de fabrication

Country Status (2)

Country Link
CN (1) CN117305693A (fr)
WO (1) WO2023246904A1 (fr)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1987001735A1 (fr) * 1985-09-19 1987-03-26 Sherby Oleg D Aciers a teneur extremement elevee en carbone et contenant de l'aluminium, ainsi que le traitement de ces aciers
CN108441763A (zh) * 2018-03-23 2018-08-24 马钢(集团)控股有限公司 一种抗拉强度1000MPa级冷轧热浸镀锌高强钢及其制备方法
CN110512146A (zh) * 2019-09-05 2019-11-29 首钢集团有限公司 一种具有优异综合性能的超高强度热轧酸洗扩孔钢及其生产方法
CN114107789A (zh) * 2020-08-31 2022-03-01 宝山钢铁股份有限公司 一种780MPa级高表面高性能稳定性超高扩孔钢及其制造方法
CN114107792A (zh) * 2020-08-31 2022-03-01 宝山钢铁股份有限公司 一种780MPa级高表面超高扩孔钢及其制造方法
CN114107791A (zh) * 2020-08-31 2022-03-01 宝山钢铁股份有限公司 一种980MPa级全贝氏体型超高扩孔钢及其制造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1987001735A1 (fr) * 1985-09-19 1987-03-26 Sherby Oleg D Aciers a teneur extremement elevee en carbone et contenant de l'aluminium, ainsi que le traitement de ces aciers
CN108441763A (zh) * 2018-03-23 2018-08-24 马钢(集团)控股有限公司 一种抗拉强度1000MPa级冷轧热浸镀锌高强钢及其制备方法
CN110512146A (zh) * 2019-09-05 2019-11-29 首钢集团有限公司 一种具有优异综合性能的超高强度热轧酸洗扩孔钢及其生产方法
CN114107789A (zh) * 2020-08-31 2022-03-01 宝山钢铁股份有限公司 一种780MPa级高表面高性能稳定性超高扩孔钢及其制造方法
CN114107792A (zh) * 2020-08-31 2022-03-01 宝山钢铁股份有限公司 一种780MPa级高表面超高扩孔钢及其制造方法
CN114107791A (zh) * 2020-08-31 2022-03-01 宝山钢铁股份有限公司 一种980MPa级全贝氏体型超高扩孔钢及其制造方法

Also Published As

Publication number Publication date
CN117305693A (zh) 2023-12-29

Similar Documents

Publication Publication Date Title
WO2022042733A1 (fr) Acier d'alésage hautement résistant à grande surface de qualité 780 mpa et son procédé de fabrication
WO2022042727A1 (fr) Acier à expansion ultra-élevée de qualité 780 mpa ayant une qualité de surface élevée et une stabilité de performance élevée, et son procédé de fabrication
CN102618790B (zh) 一种高强度低铬铁素体不锈钢及其制造方法
CN110129673B (zh) 一种800MPa级高强塑积Q＆P钢板及其制备方法
WO2022042731A1 (fr) Acier à forte expansion de trou en bainite de qualité 980 mpa et procédé de fabrication de celui-ci
CN109943765B (zh) 一种800MPa级高屈强比冷轧双相钢及其制备方法
WO2021078111A1 (fr) Acier à haute ténacité ayant une bonne ductilité et son procédé de fabrication
KR20230059806A (ko) 980 MPa급 풀-베이나이트형의 구멍 확장성이 매우 높은 철강 및 이의 제조 방법
CN113403550A (zh) 高塑性耐疲劳的冷轧热镀锌dh1180钢板及制备方法
WO2020108595A1 (fr) Plaque d'acier à haute résistance laminée à chaud ayant une qualité de surface élevée et un faible rapport de rendement et son procédé de fabrication
WO2023246904A1 (fr) Acier d'alésage ultra-haute qualité et son procédé de fabrication
CN111440991B (zh) 一种屈服强度800MPa级热轧钢板及其制造方法
CN110669990B (zh) 一种高性能铬钼钢板及其生产方法
WO2023246899A1 (fr) Acier à haute aptitude à l'alésage et son procédé de fabrication
CN111440984A (zh) 一种屈服强度700MPa级热轧钢板及其制造方法
WO2023246898A1 (fr) Acier à haute plasticité et son procédé de fabrication
WO2023246905A1 (fr) Acier à rapport d'expansion de trous élevé et d'une ultra-haute plasticité et son procédé de fabrication
CN114774788B (zh) 一种900MPa级高表面质量的酸洗汽车用钢及其制造方法和应用
WO2022042729A1 (fr) Acier à expansion de trou ultra-élevée, à martensite à très faible teneur en carbone et à austénite résiduelle de qualité 980 mpa, et son procédé de fabrication
WO2024002043A1 (fr) Acier à phase complexe laminé à chaud ayant une résistance à la traction de catégorie 800 mpa et procédé de fabrication pour celui-ci
WO2023241545A1 (fr) Tôle d'acier à phase complexe, laminée à chaud, à expansion élevée de trous, de qualité 1000 mpa, et son procédé de fabrication
WO2023241546A1 (fr) Tôle d'acier laminée à froid à haute teneur en manganèse hautement formable et facilement phosphatée ayant une résistance à la traction de 1 000 à 1 600 mpa, et son procédé de fabrication
CN117305730A (zh) 一种高表面高扩孔钢及其制造方法
CN117305692A (zh) 一种高扩孔钢及其制造方法
CN117305691A (zh) 一种析出强化型回火贝氏体高扩孔钢及其制造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 23826549

Country of ref document: EP

Kind code of ref document: A1