WO2015077934A1 - Acier à plasticité induite par maclage et son procédé de production - Google Patents

Acier à plasticité induite par maclage et son procédé de production Download PDF

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Publication number
WO2015077934A1
WO2015077934A1 PCT/CN2013/087919 CN2013087919W WO2015077934A1 WO 2015077934 A1 WO2015077934 A1 WO 2015077934A1 CN 2013087919 W CN2013087919 W CN 2013087919W WO 2015077934 A1 WO2015077934 A1 WO 2015077934A1
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Prior art keywords
production method
steel
phosphorus
sulfur
casting
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PCT/CN2013/087919
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English (en)
Chinese (zh)
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何丽丽
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何丽丽
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Priority to CN201380030717.4A priority Critical patent/CN104379277B/zh
Priority to PCT/CN2013/087919 priority patent/WO2015077934A1/fr
Publication of WO2015077934A1 publication Critical patent/WO2015077934A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/16—Controlling or regulating processes or operations
    • B22D11/18—Controlling or regulating processes or operations for pouring
    • 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
    • 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
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C22C38/12—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
    • 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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to steel metallurgy and metal materials, and more particularly to a twin induced plasticity steel and a method of producing the same. Background technique
  • Steelmaking is a process of decarburization, temperature rise and alloying by oxidation. Its main tasks are decarburization, deoxidation, temperature rise, gas removal and non-metallic inclusions, alloying, mainly including hot metal pretreatment, converter blowing, alloying, Refining, continuous casting, rolling and other steps.
  • the resistance to deformation is re-increased due to the rearrangement of the internal grains.
  • the deformation develops rapidly, it can only increase with the increase of the stress until the stress reaches the maximum value. Since then, the ability of the steel to resist deformation has been significantly reduced, and large plastic deformation occurs at the weakest point.
  • the cross section of the test piece is rapidly reduced, and necking occurs until the fracture is broken.
  • the maximum stress value of a steel before it is subjected to tensile fracture is called the strength limit or tensile strength.
  • Tensile strength is the stress value at which the material produces the most uniform plastic deformation under tensile stress.
  • TWIP steel which has a TWIP effect during deformation, produces good crystallization.
  • Mechanical properties such as high tensile strength and high plasticity at the same time.
  • the international development of TWIP steel includes the first generation Fe-25Mn-Al-3Si-0.03C series, and the second generation Fe-23Mn-0.6C series.
  • TWIP steel has broad application prospects in vehicle weight reduction.
  • TWIP steel has high strength and high plasticity, compared with other advanced high-strength steels, TWIP steel has a lower yield strength of about 200-400 MPa, which limits its commercial application in the automotive industry. .
  • the technical problem to be solved by the present invention is to provide a novel twinned inducing plastic steel and a method for producing the same.
  • a method for producing twinned inducing plastic steel comprising the steps of: a steel making step, a continuous casting step and a rolling step; and performing the continuous casting step under the condition of protective casting;
  • the conditions of the protective casting are: using a mold flux, casting at a low superheat of 5 ° C to 10 ° C, a drawing speed of 0.5 to 1.5 m / min; in the rolling step, using cold rolling pre-deformation, and Annealing is performed at a temperature close to the full recrystallization temperature.
  • pre-deformed cold rolling is performed using a deformation amount of 10% to 60%.
  • the rolling step includes a recovery and a partial recrystallization annealing process, and the processing temperature is between 550 and 700 degrees Celsius, and the processing time is 100 to 1000 seconds.
  • the steelmaking step comprises a sulfur reduction phosphorus-oxygen process, wherein at the end of the steelmaking step, the sulfur is less than 0.0025%, the phosphorus is less than 0.0025%, and the total oxygen content is less than 0.0015%.
  • the steelmaking step includes an alloying process, and the total addition thereof
  • the percentage by mass is 0.01-2% of at least one transition metal element: titanium, niobium, vanadium.
  • the rolling step includes a metal precipitation process, and at the end of the rolling step, the volume fraction of the transition metal precipitate phase is 1% to 2%, and the size is 15 nm to 150 nm; and, metal precipitation
  • the volume fraction of the phase Al (C, N) is 0.2%-0.5%, and the size is 15 ⁇ to 150 ⁇ .
  • the protective casting is realized by using a protective slag, and the mass percentage of the components of the protective slag is: calcium oxide 30%-40%, silica 30%-40%, aluminum oxide 5% -10%, magnesium oxide 5%-10%, and the balance being sodium oxide and fluorine.
  • the electromagnetic stirring control of the crystallizer is used to reduce the columnar crystal ratio and increase the equiaxed crystal ratio, and the equiaxed crystal ratio of the billet is 70% or more, and the solidification end is electromagnetic stirring.
  • the carbon center segregation degree is controlled between 1.0 and 1.1
  • the phosphorus and sulfur center segregation degrees are controlled between 1.0-1.15
  • the manganese center segregation degree is controlled at 1.0-. Between 1.2.
  • a further technical solution of the present invention is a twin-induced plastic steel prepared by any of the above production methods, which comprises carbon 0.2-1.0%, manganese 10-25%, aluminum 0.02-1.0%, phosphorus ⁇ 0.0025% , sulfur ⁇ 0.0025%, nitrogen ⁇ 0.003%, and a total mass percentage of 0.01-2% of the following at least one transition metal element: titanium, tantalum, vanadium, the balance is iron.
  • the twinned inducing plastic steel comprises at least one of the following elements and an amount thereof: titanium 0.01-1.2%, 43 ⁇ 4 0.01-1.2%, vanadium 0.01-1.2%.
  • the present invention can provide a TWIP steel having a yield strength exceeding 100 MPa and a uniform elongation of more than 10%, and is particularly suitable for special steel applications such as automobiles, and has a market value of 4 ⁇ .
  • Figure 1 is a schematic illustration of one embodiment of a method of production of the present invention. detailed description
  • the invention belongs to the field of steel metallurgy and metal materials, and provides a TWIP steel production method with a yield strength exceeding 1000 MPa and a uniform elongation exceeding 10%, in particular, a process for improving the traditional TWIP steel, which can increase the yield strength to more than 1000 MPa. At the same time, the uniform elongation exceeds 10% of the production method.
  • An embodiment of the present invention is a method for producing twinned inducing plastic steel, comprising the steps of: a steel making step, a continuous casting step and a rolling step; and performing the continuous casting step under conditions of protective casting;
  • the condition of the protective casting is: using a mold flux, casting at a low superheat of 5 ° C to 10 ° C, a drawing speed of 0.5 to 1.5 m / min; and, in the step of rolling, using a cold rolling pre Deformation.
  • the steelmaking step selects conventional TWIP steel, conventional TWIP scrap or other materials.
  • an embodiment of the present invention is a method for producing twinned inducing plastic steel, which comprises the following steps: a steel making step, a continuous casting step and a rolling step; the continuous casting step is continuous Casting step; performing the continuous casting step under the condition of protective casting; wherein, the condition of the protective casting is: using a protective slag, performing low superheat casting at 5 ° C - 10 ° C, the pulling speed is 0.5 Up to 1.5 m/min; in the rolling step, cold rolling pre-deformation is employed, and annealing treatment is performed at a temperature close to the complete recrystallization temperature.
  • the steelmaking material comprises carbon ⁇ 1.0%, manganese ⁇ 25%, aluminum ⁇ 1.0%, phosphorus ⁇ 0.0025%, sulfur ⁇ 0.0025%, nitrogen ⁇ 0.003%, and total mass percentage ⁇ 2% or less.
  • a transition metal element titanium, tantalum, vanadium, the balance of iron and other materials involved in steelmaking.
  • steelmaking materials are set according to the following steelmaking targets.
  • the steelmaking targets include carbon 0.2-1.0%, manganese 10-25%, aluminum 0.02-1.0%, phosphorus ⁇ 0.0025%, sulfur ⁇ 0.0025%, and nitrogen ⁇ 0.003%.
  • the steelmaking process reduces the total oxygen content, thereby reducing the amount of steel inclusions, while controlling the S and P mass percentages of the steel species below 0.0025% and the total oxygen content below 0.0015%.
  • the continuous casting process should be carried out with low superheat and low drawing speed.
  • the superheat degree is controlled between 5 °C and 10 °C
  • the pulling speed is controlled at 0.5/min-1.2 m/min
  • the casting process uses the electromagnetic stirring method of the crystallizer.
  • the slab is uniformly organized, the center defect of the slab is controlled at 0-2, and the equiaxed crystal ratio is above 70%.
  • the solidification end electromagnetic stirring method makes the material structure more uniform, the center segregation degree of C element is controlled between 1.0-1.1, the center segregation degree of P and S elements is controlled between 1.0-1.15, and the center segregation degree control of Mn element Between 1.0 and 1.2.
  • the process of achieving low superheat casting includes: controlling inclusions in steel to prevent nozzle nodulation in low superheat casting process; accurately controlling temperature stability of tundish steel in continuous casting process; stable control of steelmaking continuous casting production rhythm .
  • the conditions for protective casting include the use of an immersion protection tube and the blowing of argon.
  • the steelmaking step comprises a sulfur reduction phosphorus-oxygen process, and at the end of the steelmaking step, the sulfur is less than 0.0025%, the phosphorus is less than 0.0025%, and the total oxygen content is less than 0.0015%.
  • the steelmaking step comprises an alloying process, and the alloying process of the steelmaking step is added with titanium (Ti), milling (Nb), vanadium (V) or one or more transition metal elements. , The three transition elements are precipitate forming elements, form carbonitride precipitates with carbon and nitrogen elements, refine grains, and increase the yield strength of the material.
  • the alloying process adds at least one transition metal element in a total mass percentage of from 0.01 to 2%: titanium, niobium, vanadium.
  • the rolling step includes a metal precipitation process, and at the end of the rolling step, the volume fraction of the transition metal precipitate phase is 1% to 2%, and the size is 15 nm to 150 nm; and, the metal precipitate phase Al (C, N)
  • the volume fraction is from 0.2% to 0.5% and the size is from 15 nm to 150 nm.
  • Carbon, nitrogen and aluminum form an intermetallic compound Al (C, N) to refine grains and improve the strength and plasticity of the material.
  • the mass fraction of aluminum should be controlled at 0.01-1% to control intermetallic compound precipitates in steel.
  • the volume fraction is 0.2%-0.5%, the size is 15nm-100nm, and when the aluminum content exceeds 1%, a large number of large-sized inclusions are deteriorated to deteriorate the physical properties such as formability and elongation of the material.
  • the continuous casting process uses a CaO/SiO2 type protective slag to maintain a certain thickness of the liquid slag layer thickness, and timely add the protective slag to maintain good lubricity of the slab and the mold wall to prevent steel leakage and surface cracks.
  • the phenomenon of slag inclusion occurs, and the weight percentage of the specific components of the protective slag is: calcium oxide (CaO) 30%-40%, silicon dioxide (Si0 2 ) 30%-40%, aluminum oxide (A1 2 0 3 , Alumina) 5%-10%, magnesium oxide (MgO) 5%-10%, and the rest are disodium nitrite (Na 2 0, sodium oxide) and fluorine (F).
  • the protective casting is realized by using a protective slag
  • the mass percentage of the components of the protective slag is: calcium oxide 30%-40%, silica 30%-40%, aluminum oxide 5% -10%, magnesium oxide 5%-10%, and the balance being sodium oxide and fluorine.
  • the mass percentage of the components of the flux is: calcium oxide 32%, silica 38%, aluminum oxide 8%, magnesium oxide 10%, and sodium oxide 10% and fluorine 2%.
  • the mass percentage of the components of the flux is: calcium oxide 39%, silica 34%, aluminum oxide 5%, magnesium oxide 9%, and sodium oxide 4% and fluorine 9%.
  • the crystallizer is used Stirring control reduces the columnar crystal ratio and increases the equiaxed crystal ratio.
  • the equiaxed crystal ratio of the billet is above 70%.
  • the solidification end uses electromagnetic stirring to reduce the carbon and phosphorus and sulfur segregation and carbon center segregation.
  • the control is between 1.0 and 1.1, the phosphorus and sulfur center segregation degrees are controlled between 1.0-1.15, and the manganese center segregation degree is controlled between 1.0 and 1.2.
  • pre-deformed cold rolling is performed using a deformation amount of 10% to 60%. Due to the ultra-high plasticity of TWIP steel, increasing the pre-strain and sacrificing a certain amount of plasticity to improve the yield strength of TWIP steel is an effective strengthening method.
  • the pre-strain of 10%-60% cold rolling will significantly improve the yield strength of the material, exceeding When 60% pre-straining, two problems are caused. First, the work hardening rate of the material is drastically reduced, the plasticity of the material such as elongation is lowered, and the second is that the anisotropy of the material is increased, so that the forming property of the material is weakened.
  • pre-deformed cold rolling is performed using a deformation amount of 50%.
  • the rolling step includes a recovery and a partial recrystallization annealing process
  • the treatment temperature is between 550 and 700 degrees Celsius
  • the treatment time is from 100 to 1000 seconds.
  • the recovery and partial recrystallization annealing temperature is between 550 ° C and 700 ° C, close to the steel.
  • the lower limit of complete recrystallization temperature, the treatment time is 100s-1000s. After the treatment, the grain portion is recrystallized, and the dislocation density in the crystal drops sharply.
  • the mechanical twin crystal Since the mechanical twin crystal has good thermal stability, almost no change occurs in this temperature range, and the best yield strength and elongation will be obtained. .
  • the temperature exceeds 700 °C, complete recrystallization is likely to occur, the work hardening rate is reduced, and the yield strength of the material is drastically reduced.
  • the temperature is less than 550 ° C, the dislocation density in the crystal is too high, and the plasticity and formability of the material are still relatively high. difference.
  • TWIP steel production method with a yield strength exceeding 1000 MPa and a uniform elongation of 10% or more.
  • the casting process is carried out by using a suitable composition.
  • the slag is modified by transition metal and intermetallic alloy to form precipitates and cold rolling pre-deformation, and close to complete recrystallization temperature degradation treatment to improve the comprehensive mechanical properties of TWIP.
  • TWIP steel is controlled at the end point S of the steelmaking process. Below 0.0025%, the P is controlled to be 0.0025% or less, and the total oxygen content is controlled to be 0.0015% or less.
  • the TWIP steel is cast at a low superheat of 5 ° C - 10 ° C in the continuous casting process, adopting protective casting measures, using a mold electromagnetic stirring control to reduce the columnar crystal ratio and increasing the equiaxed crystal ratio, and the equiaxed crystal ratio of the slab Above 70%, the solidification end uses electromagnetic stirring to make the slab microstructure uniform and reduce carbon, phosphorus and sulfur segregation.
  • the macroscopic rating of the slab center defect is 0-2, and the C element center segregation degree is controlled between 1.0-1.1.
  • the segregation degree of P and S elements is controlled between 1.0-1.15, and the center segregation degree of Mn element is controlled between 1.0-1.2.
  • the TWIP steel undergoes a 10%-60% cold rolling pre-deformation process, and the process significantly improves the yield strength of the TWIP steel.
  • the TWIP steel has a volume fraction of 0.2%-0.5%, and a scale distribution of 10-150 nm is uniformly distributed in the matrix structure of the transition intermetallic compound precipitate phase A1 (C, N).
  • the TWIP steel has a volume fraction of 1% to 2%, and a scale distribution of 10-100 nm is uniformly distributed in the matrix structure of the intermetallic compound precipitate phase Ti ⁇ Nb ⁇ V (C, N).
  • the recovery and partial recrystallization annealing treatment temperature is between 550 ° C and 700 ° C, which is close to the lower limit of the complete recrystallization temperature of the steel, and the treatment time is from 100 s to 1000 s.
  • the chemical composition of the TWIP steel is expressed by mass fraction: carbon (C): 0.2-1.0%, manganese (Mn): 10-25%, aluminum (A1): 0.02-1.0%, phosphorus (P) ⁇ 0.0025 %, sulfur (S) ⁇ 0.0025%, nitrogen ( ⁇ 0.003%), containing at least one of the following alloying elements: titanium (Ti): 0.01-1.2%, milling (Nb): 0.01-1.2, vanadium (V): 0.01 -1.2%, the rest is iron.
  • the present invention belongs to the field of steel metallurgy and metal materials, and provides a TWIP steel production method having a yield strength exceeding 100 MPa and a uniform elongation exceeding 10%. It controls the hazardous elements and total oxygen content in the steelmaking step, selects the appropriate component to protect the slag during the continuous casting process, and adopts protective casting and low superheat low-speed casting process, using transition metal and intermetallic compound precipitation strengthening and cold rolling pre-deformation. Processes such as continuous annealing at a complete recrystallization temperature to improve the mechanical properties of TWIP, such that the yield strength exceeds 1000 MPa and the uniform elongation exceeds 10%.
  • a TWIP steel having a chemical composition of Fe-22%Mn-0.6%Cl%Al-0.5%V is used as a target, and the steelmaking process controls the mass fractions of S and P elements respectively.
  • the continuous casting process uses a low superheat of 10 ° C, a pull speed of 0.8 m / min for protection casting, the continuous casting billet is heated in a heating furnace at 1200 ° C for 1 hour, and then the final rolling temperature is 900 ° Hot rolling of C, rolled to a 3.5 mm thin plate, crimping temperature of 650 ° C, and then subjected to 60% cold rolling of pre-variable, thin plate thickness of 1.4 mm, continuous annealing in a continuous annealing furnace at 750 ° C After 1000s treatment, samples were taken on the cold rolled billet for traditional one-dimensional quasi-static tensile test and microstructure analysis.
  • the tensile strength of the specimen was more than 1150 MPa, the yield strength exceeded 1000 MPa, the elongation exceeded 15%, and the size of 20-100 nm was dispersed by TEM to distribute V (C, N) and Al in the steel matrix. C, N) precipitates with volume fractions of 1.2% and 0.3%, respectively. Then tensile tests were carried out at four different strain levels of 5%, 8%, 12% and 15% to characterize the microstructure after strain deformation. It was found that the deformation process at different strain levels has a certain density of deformation twins.
  • the TWIP steel obtained in this embodiment greatly improves the yield strength of the material to more than 100 MPa, and the uniform elongation of the material is controlled at more than 10%, which is an ideal automobile industry. Materials can also be widely used in other demand industries for special steels.
  • a further embodiment of the invention is a twinned inducing plastic steel comprising carbon 0.2-1.0%, manganese 10-25%, aluminum 0.02-1.0%, phosphorus ⁇ 0.0025%, sulfur ⁇ 0.0025%, nitrogen ⁇ 0.003 %, and at least one transition metal element having a total mass percentage of 0.01-2%: titanium, niobium, vanadium, balance iron; for example, total weight 1000kg, containing 2 to 10kg of carbon, 100 to 250kg Manganese, and so on.
  • the proportions involved in the various embodiments of the present invention are all percentages by mass unless otherwise stated.
  • a twin-induced plastic steel prepared by any of the above production methods, comprising carbon 0.2-1.0%, manganese 10-25%, aluminum 0.02-1.0%, phosphorus ⁇ 0.0025%, sulfur ⁇ 0.0025%, Nitrogen ⁇ 0.003%, and a total mass percentage of 0.01-2% of at least one transition metal element: titanium, niobium, vanadium, the balance being iron.
  • the twinned inducing plastic steel comprises at least one of the following elements and Dosage: 0.01-1.2% titanium, 0.01-1.2% ⁇ , 0.01-1.2% vanadium, for example, containing 0.1% titanium, 0.5% bismuth and 0.63% vanadium; for example, containing 1.1% titanium and 0.8% Oh, as another example, it contains 1.0% milling and 0.2% vanadium.
  • the total mass percentage of titanium, niobium and vanadium is 0.01-2%.
  • the embodiment of the present invention may further be a twin-induced plasticity steel formed by combining the technical features of the above embodiments and a production method thereof.

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  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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  • Treatment Of Steel In Its Molten State (AREA)

Abstract

La présente invention concerne un acier à plasticité induite par maclage et un procédé de production correspondant, ses constituants étant : C : 0,2-1,0 %, Mn : 10-25 %, Al : 0,02-1,0 %, P : <0,0025 %, S : <0,0025 %, N : <0,003 % ; contenant au moins l'un des éléments d'alliage suivants : Ti : 0,01-1,2 %, Nb : 0,01-1,2 %, V : 0,01-1,2 % ; le complément étant du fer élémentaire. Le procédé de production comprend une fusion, un coulage continu sous protection, et un laminage ; l'étape de laminage utilise une pré-dénaturation par laminage à froid, et un recuit est réalisé à la température approchant la recristallisation complète pour obtenir un acier à plasticité induite par maclage possédant une limite d'élasticité supérieure à 1000 MPa et un allongement uniforme supérieur à 10 %.
PCT/CN2013/087919 2013-11-27 2013-11-27 Acier à plasticité induite par maclage et son procédé de production WO2015077934A1 (fr)

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CN201380030717.4A CN104379277B (zh) 2013-11-27 2013-11-27 一种孪晶诱导塑性钢及其生产方法
PCT/CN2013/087919 WO2015077934A1 (fr) 2013-11-27 2013-11-27 Acier à plasticité induite par maclage et son procédé de production

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US20190218639A1 (en) * 2016-05-24 2019-07-18 Arcelormittal Twip steel sheet having an austenitic matrix
CN111383861A (zh) * 2018-12-28 2020-07-07 东莞科力线材技术有限公司 一种电磁继电器用的导磁材料及其制备方法
CN112233735A (zh) * 2020-09-07 2021-01-15 包头钢铁（集团）有限责任公司 一种珠光体钢轨钢化学成分的设计方法
CN113684411A (zh) * 2021-08-26 2021-11-23 江苏联峰实业有限公司 一种解决400MPa级含Nb钢筋无屈服平台的方法
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