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WO2021057954A9 - Acier pour structures d'alliage et procédé de fabrication associé - Google Patents

Acier pour structures d'alliage et procédé de fabrication associé Download PDF

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Publication number
WO2021057954A9
WO2021057954A9 PCT/CN2020/118043 CN2020118043W WO2021057954A9 WO 2021057954 A9 WO2021057954 A9 WO 2021057954A9 CN 2020118043 W CN2020118043 W CN 2020118043W WO 2021057954 A9 WO2021057954 A9 WO 2021057954A9
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Prior art keywords
steel
alloy
particles
structural steel
alloy structure
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PCT/CN2020/118043
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English (en)
Chinese (zh)
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WO2021057954A1 (fr
Inventor
郑宏光
柳向椿
刘俊江
翟瑞银
万根节
夏杨青
孟庆玉
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宝山钢铁股份有限公司
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Priority to US17/763,348 priority Critical patent/US20220349035A1/en
Priority to EP20869967.8A priority patent/EP4036266A4/fr
Priority to JP2022519356A priority patent/JP7443502B2/ja
Priority to KR1020227010806A priority patent/KR102713980B1/ko
Publication of WO2021057954A1 publication Critical patent/WO2021057954A1/fr
Publication of WO2021057954A9 publication Critical patent/WO2021057954A9/fr

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    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/58—Oils
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, 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
    • 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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • 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
    • 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
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a steel grade and a manufacturing method thereof, in particular to a steel for alloy structure and a manufacturing method thereof.
  • 40CrV can be used to manufacture various important parts with variable load and high load, such as locomotive connecting rods, crankshafts, push rods, propellers, beams, bushing brackets, studs, screws, non-carburized gears, nitriding treatment Various gears and pins, high-pressure boiler water pump shaft (diameter less than 30mm), high-pressure cylinder, steel pipe and bolts (the working temperature is less than 420 °C, the strength is 30MPa), etc.
  • the existing 40CrV composition range is as follows: C 0.37-0.44wt%; Si 0.17-0.37wt%; Mn 0.5-0.8wt%; S ⁇ 0.015wt%; P ⁇ 0.025wt%; Cr 0.8-1.1wt%; V 0.1-0.2wt%; Al ⁇ 0.015wl.
  • the mechanical properties of this steel are as follows: yield strength (Rel) ⁇ 735MPa; tensile strength (Rm) ⁇ 885MPa; elongation ⁇ 10%; hardness ⁇ 241HB; impact toughness ⁇ 71J.
  • One of the objectives of the present invention is to provide a steel for alloy structure, which adopts the design of adding trace alloying elements, and controls the total oxygen with a lower content by adding an appropriate amount of Zr and Mg. It further strengthens and toughens the alloy structural steel, so that the alloy structural steel has higher strength and lower material cost.
  • the present invention proposes a kind of steel for alloy structure, and its chemical element mass percentage is:
  • C In the alloy structural steel according to the present invention, C mainly affects the precipitation amount and precipitation temperature range of carbides. Controlling the lower mass percentage of C is beneficial to improve the mechanical properties of the alloy structural steel of the present invention. In addition, C has a certain strengthening effect, but too high mass percentage of C will reduce the corrosion resistance of the material. Considering the production capacity of the smelting equipment and taking into account the mechanical properties and impact toughness of the material, the mass percentage of C in the alloy structural steel of the present invention is controlled to be 0.35-0.45%.
  • Si can increase the strength of the steel in the steel, but it is not good for the formability and toughness of the steel. In addition, Si often remains in the smelting process, so it is important to properly select the content of Si. Based on this, the mass percentage of Si in the alloy structural steel of the present invention is controlled to be 0.27-0.35%.
  • Mn is a weak austenitic element that can suppress the harmful effects of sulfur in alloy structural steels and improve thermoplasticity.
  • too high mass percentage of Mn is not conducive to ensuring its corrosion resistance.
  • the mass percentage of Mn is controlled to be 0.6-0.8% in the technical solution of the present invention.
  • Al In the alloy structural steel according to the present invention, Al mainly controls the oxygen content in the steel and affects the dislocation behavior to strengthen the alloy. Increasing the total amount of Al can significantly improve the solution temperature and mechanical properties, but it will reduce the plasticity. In addition, the addition of Al is beneficial to the elongation deformation properties of the steel and improves the processing properties of the steel. Too high Al content will reduce the impact toughness of steel. Based on this, the mass percentage of Al in the alloy structural steel of the present invention is controlled to be 0.015-0.05%.
  • V has a very strong affinity with carbon and oxygen, and can form a corresponding stable compound.
  • V mainly exists in the form of carbides in steel.
  • the main function of V is to refine the structure and grain of the steel and reduce the strength and toughness of the steel.
  • V dissolves into solid solution at high temperature, it increases the hardenability; on the contrary, if it exists in the form of carbide, it reduces the hardenability.
  • V can increase the tempering stability of quenched steel and produce a secondary hardening effect.
  • Vanadium in alloy structural steel is often used in combination with manganese and chromium elements because it will reduce the hardenability under general heat treatment conditions. Vanadium is mainly used in quenched and tempered steel to improve the strength and yield ratio of steel, refine grains and reduce overheating sensitivity. Based on this, the mass percentage of V in the alloy structural steel of the present invention is controlled to be 0.06-0.1%.
  • Zr is a strong carbide forming element, and its function in steel is similar to that of niobium, tantalum and vanadium. Adding a small amount of Zr can play the role of degassing, purification and grain refinement, which is beneficial to the low temperature performance of steel and improves the stamping performance. In addition, a small amount of Zr is added, and part of the Zr is dissolved in the steel to form an appropriate amount of ZrC and ZrN, which is beneficial to refine the grains and improve the stamping performance. Based on this, the mass percentage of Zr in the alloy structural steel of the present invention is controlled to be 0.2-1.0%.
  • Mg is a very active metal element, which has a strong affinity with O, N, and S. Therefore, Mg is a good deoxidizer and desulfurizer in iron and steel smelting, and is also a good nodularizer for cast iron. However, Mg is hardly dissolved in the matrix of cast iron, and exists in the state of compounds MgS, MgO, Mg 3 N 2 and Mg 2 Si. In addition, Mg and C can also form a series of compounds, such as MgC 2 , Mg 2 C 3 . Based on this, the mass percentage of Mg in the alloy structural steel of the present invention is controlled to be 0.001-0.005%.
  • N is a stable austenite element. Controlling a relatively low mass percentage of N is beneficial to improve the impact toughness of the alloy structural steel of the present invention. In addition, higher mass percentages of nitrogen result in reduced toughness and ductility of the steel, and also reduce hot workability. Based on this, the mass percentage of N in the alloy structural steel of the present invention is controlled to be N ⁇ 0.005%.
  • O In the alloy structural steel of the present invention, O mainly exists as oxide inclusions, and a high total oxygen content indicates that there are many inclusions. Reducing the total oxygen content is beneficial to improve the comprehensive properties of the material. In order to ensure good mechanical and corrosion resistance properties of the material, in the technical solution of the present invention, the mass percentage of O is controlled to be O ⁇ 0.001%.
  • the alloy structural steel of the present invention also has at least one of the following chemical elements: Ce, Hf, La, Re, Sc and Y, and the total addition amount of these elements is ⁇ 1% .
  • a small amount of the above-mentioned rare earth elements can be added to combine oxygen and sulfur elements in steel to form rare earth oxides and sulfides, purify molten steel and reduce the size of inclusions.
  • the formed rare earth oxides and sulfides can be used as nucleation particles in the solidification process to refine the initial solidified grains, and also help to improve the properties of steel.
  • the mass percentage content of each element satisfies at least one of the following items:
  • the mass percentage content ratio of each element also satisfies at least one of the following items:
  • controlling the mass percentage of Zr to N, V, and C is beneficial to control the amount of ZrC and ZrN formed, and the formation of ZrC and ZrN can play a role in refining grains, improving steel mechanical properties and stamping properties. At the same time, it can also play a role in solidifying part of the N in the steel and reducing the mass percentage of the solid solution N.
  • the mass percentage content ratio of each element also satisfies at least one of the following items:
  • controlling the mass percentage of Mg to O and S can be beneficial to the formation of MgO and MgS in the alloy during the cooling and solidification process, and the formation of MgS and MgO can further refine the grains and stabilize the alloy. On the other hand, it can also reduce the damage of O and S in the alloy to the grain boundary, thereby improving the impact toughness of the alloy structural steel in this case.
  • the matrix of its microstructure is ferrite+pearlite, which has ZrC, ZrN, MgO, MgS particles.
  • the above-mentioned particles of ZrC, ZrN, MgO, and MgS mean that ZrC, ZrN, MgO, and MgS exist in the form of fine particles in the steel for alloy structure.
  • the above-mentioned particles can further refine and stabilize the austenite grain size during the continuous casting cooling and solidification process and the hot rolling process, thereby avoiding the formation of defects on the surface of the billet or the final product, and can also improve the mechanical properties of the product.
  • the sum of the number of ZrC and ZrN particles is 3-15 particles/mm 2 .
  • controlling the sum of the number of ZrC and ZrN particles to 3-15 particles/mm 2 can reduce the amount of solidified grains, improve the mechanical properties and stamping properties of steel, and reduce the amount of N in the solidified steel.
  • the effect of the mass percentage of dissolved N is better.
  • the sum of the numbers of MgO and MgS particles is 5-20 particles/mm 2 .
  • controlling the sum of the number of MgO and MgS particles to be 5-20 particles/mm 2 can further refine the grains, stabilize the austenite grains and reduce the effect of O and S on the grain boundaries in the alloy. Therefore, the effect of improving the impact toughness of the alloy structural steel in this case is better.
  • the diameters of the particles of ZrC, ZrN, MgO and MgS are 0.2-7 ⁇ m.
  • the yield strength is greater than or equal to 755MPa
  • the tensile strength is greater than or equal to 900MPa
  • the elongation is greater than or equal to 12%
  • the impact toughness is greater than or equal to 100J.
  • another object of the present invention is to provide the above-mentioned manufacturing method of alloy structural steel, through which alloy structural steel with higher mechanical properties, better impact toughness and more reasonable cost can be obtained.
  • the present invention proposes a method for manufacturing the above-mentioned alloy structural steel, which comprises the steps:
  • step (1) electric furnace smelting, LF and VD (or RH) refining can be used in step (1), and a small amount of zirconium iron, and magnesium-aluminum alloys, after the mass percentage of each chemical element in the steel meets the range limited in this case, soft stirring with argon blowing is performed, and the argon gas flow is controlled at 5-8 liters/min.
  • step (1) bloom continuous casting can be used for casting, and the pulling speed is controlled to be 0.45-0.65m/min; mold powder is used, and mold electromagnetic stirring is used, and the current is 500A , the frequency is 2.5-3.5Hz, and the equiaxed crystal proportion of the bloom after continuous casting is ⁇ 20%.
  • the blank in step (2), can be pretreated before blooming, for example, surface finishing and grinding can be performed to remove visible surface defects and ensure good surface quality.
  • the heating temperature during preliminary rolling is 1150-1250°C; the heating temperature during secondary hot rolling is 1150-1250°C .
  • step (4) the quenching heating temperature is controlled at 855-890° C., the quenching cooling rate is controlled at 50-90° C./s; the tempering heating temperature is controlled at 645-670° C. °C, the tempering cooling rate is controlled at 50-90°C/s.
  • the coolant used for quenching may be mineral oil, and the coolant used for tempering may be mineral oil or water.
  • the steel for alloy structure and the manufacturing method thereof of the present invention have the following advantages and beneficial effects:
  • the steel for alloy structure of the present invention adopts the design of adding trace alloy elements. By adding an appropriate amount of Zr and Mg, the total oxygen content is controlled at a lower content, and the characteristics of the added trace alloy elements are used to further strengthen and toughen the alloy structure. steel, so that the alloy structural steel has higher strength and lower material cost.
  • the alloy structural steel of embodiment 1-6 adopts the following steps to make:
  • RH refining can also be used for refining, and at the end of VD (or RH) refining, a small amount of zirconium-iron and magnesium-aluminum alloys can be added successively to prepare the chemical elements in the steel. After the mass percentage satisfies the range defined in this case, soft stirring is performed by blowing argon gas, and the argon gas flow rate is controlled at 5-8 liters/min.
  • step (1) bloom continuous casting can be used for casting, and the pulling speed is controlled to be 0.45-0.65m/min; mold powder is used, and mold electromagnetic stirring is used, and the current is 500A , the frequency is 2.5-3.5Hz, and the equiaxed crystal proportion of the bloom after continuous casting is ⁇ 20%.
  • the blank in step (2), can be pretreated before blooming, for example, surface finishing and grinding can be performed to remove visible surface defects and ensure good surface quality.
  • Comparative Examples 1-3 were obtained by using the components and manufacturing processes of the prior art.
  • Table 1 lists the mass percentage ratio of each chemical element of the alloy structural steels of Examples 1-6 and the existing structural steels of Comparative Examples 1-3.
  • Table 2 lists the microstructures in the obtained alloy structural steels of Examples 1-6 and the existing structural steels of Comparative Examples 1-3.
  • Table 3 lists the specific process parameters of the alloy structural steels of Examples 1-6 and the existing alloy structural steels of Comparative Examples 1-3.
  • the tensile test (yield strength R el , tensile strength R m , elongation test) of the present invention is tested by using a zwick/roell Z330 tensile testing machine, and the test standard is in accordance with the national standard GB/T 228.1-2010. Among them, the tests of yield strength R el , tensile strength R m and elongation are carried out according to the standards defined in 3.10.1, 3.10.2 and 3.6.1 of this standard, respectively.
  • the impact toughness was tested by Zwick/Roell PSW 750 impact testing machine.
  • the test standard was in accordance with the national standard GB/T 229-2007.
  • the value of impact toughness was obtained by measuring the energy absorbed by the alloy structural steel in the Charpy impact test.
  • the number of ZrC and ZrN particles, the number of MgO and MgS particles, the statistics and determination methods of ZrC, ZrN, MgO, MgS particle diameters were carried out by scanning electron microscope (SEM). oxford X-max 20, the determination standard is carried out according to GB/T 30834-2014.
  • Table 4 lists the test results of various examples and comparative examples.
  • Example 1 755 900 12 123 Example 2 765 905 13 125 Example 3 763 910 12 108 Example 4 770 908 14 137 Example 5 767 912 13 117 Example 6 758 907 12 100 Comparative Example 1 735 885 10 78 Comparative Example 2 730 890 11 85 Comparative Example 3 732 893 10 73
  • the steel for alloy structure in each embodiment of this case has ZrC, ZrN, MgO, MgS particles because of its microstructure of ferrite + pearlite, and these particles play a role in refining,
  • the effect of stabilizing the austenite grains is conducive to improving the mechanical properties of the material. Therefore, the alloy structural steels of the examples in this case have better mechanical properties than the existing structural steels in Comparative Examples 1-3 using the prior art.
  • the yield strength of the alloy structural steel of each embodiment is ⁇ 755 MPa
  • the tensile strength is ⁇ 900 MPa
  • the elongation is ⁇ 12%
  • the impact toughness is ⁇ 100J.
  • the steel for alloy structure of the present invention adopts the design of adding trace alloying elements.
  • the total oxygen content is controlled at a lower content, and the characteristics of the added trace alloying elements are used to further strengthen and toughen the steel.
  • the alloy structural steel can be melted, so that the alloy structural steel has higher strength and lower material cost.

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  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un acier pour une structure d'alliage, les éléments chimiques de l'acier étant, en pourcentage en masse : de 0,35 à 0,45 % de C, de 0,27 à 0,35 % de Si, de 0,6 à 0,8 % de Mn, de 0,015 à 0,05 % d'Al, de 0,06 à 0,1 % de V, de 0,2 à 1,0 % de Zr, de 0,001 à 0,005 % de Mg, de ≤ 0,025 % de P, de ≤ 0,015 % de S, de ≤ 0,005 % de N, de ≤ 0,001 % de O, le reste étant constitué de Fe et d'autres impuretés inévitables. De plus, l'invention concerne également un procédé de fabrication de l'acier pour une structure d'alliage, le procédé comprenant les étapes de : (1) fusion, raffinage et coulée ; (2) colmatage et dégrossissage ; (3) laminage à chaud secondaire pour former un produit ; et (4) traitement thermique, impliquant une trempe + un revenu. L'acier pour une structure d'alliage est conçu par l'ajout d'éléments d'alliage à l'état de trace, l'acier pour une structure d'alliage est plus résistante et renforcée, et le coût de fabrication est faible.
PCT/CN2020/118043 2019-09-27 2020-09-27 Acier pour structures d'alliage et procédé de fabrication associé WO2021057954A1 (fr)

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US17/763,348 US20220349035A1 (en) 2019-09-27 2020-09-27 Steel for alloy structure and manufacturing method therefor
EP20869967.8A EP4036266A4 (fr) 2019-09-27 2020-09-27 Acier pour structures d'alliage et procédé de fabrication associé
JP2022519356A JP7443502B2 (ja) 2019-09-27 2020-09-27 合金構造用鋼及びその製造方法
KR1020227010806A KR102713980B1 (ko) 2019-09-27 2020-09-27 합금 구조용 스틸 및 그 제조방법

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CN201910920640.7A CN112575242B (zh) 2019-09-27 2019-09-27 一种合金结构用钢及其制造方法
CN201910920640.7 2019-09-27

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CN112575242A (zh) 2021-03-30
KR102713980B1 (ko) 2024-10-11
KR20220054862A (ko) 2022-05-03
EP4036266A4 (fr) 2023-06-14
EP4036266A1 (fr) 2022-08-03
US20220349035A1 (en) 2022-11-03
JP2022550358A (ja) 2022-12-01
JP7443502B2 (ja) 2024-03-05
CN112575242B (zh) 2022-06-24

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