WO2024149253A1 - Acier vitrifié présentant une limite d'élasticité de 345 mpa ou plus, et son procédé de fabrication - Google Patents

Acier vitrifié présentant une limite d'élasticité de 345 mpa ou plus, et son procédé de fabrication Download PDF

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Publication number
WO2024149253A1
WO2024149253A1 PCT/CN2024/071393 CN2024071393W WO2024149253A1 WO 2024149253 A1 WO2024149253 A1 WO 2024149253A1 CN 2024071393 W CN2024071393 W CN 2024071393W WO 2024149253 A1 WO2024149253 A1 WO 2024149253A1
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Prior art keywords
glass
lined steel
lined
steel
yield strength
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PCT/CN2024/071393
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English (en)
Chinese (zh)
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孙全社
王双成
魏娇
陶孝勇
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宝山钢铁股份有限公司
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Publication of WO2024149253A1 publication Critical patent/WO2024149253A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C33/06—Making ferrous alloys by melting using master alloys
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the invention relates to a steel material and a manufacturing method thereof, in particular to a glass-lined steel and a manufacturing method thereof.
  • glass-lined containers are generally made of Q245R steel plates.
  • steel composition such as the main components of Q245R in GB 713 are C ⁇ 0.20%, Si ⁇ 0.35%, Mn: 0.50 ⁇ 1.00%, which sometimes causes scale explosion due to insufficient hydrogen traps in the steel during enameling;
  • the microstructure in the steel is mainly pearlite plus ferrite, the higher the content of pearlite, the more gases such as CO are generated during enameling and firing. These gases gather into bubbles or large bubbles in the glass layer, which will seriously damage its corrosion resistance and surface quality.
  • Q345R steel plates with higher strength.
  • Q245R steel plates have higher carbon and pearlite contents, so the harm of bubble generation will be more prominent.
  • the silicon and manganese contents are also high, which is very unfavorable for improving the enameling properties and glass layer quality.
  • One of the purposes of the present invention is to provide a glass-lined steel with a yield strength of more than 345 MPa, which meets the requirements of forming, welding and enameling for making glass-lined containers, and can achieve the requirements of thinning or lightening the glass-lined containers.
  • the glass-lined process it can reduce the number of enameling and firing, improve the processing efficiency, reduce energy consumption and the use of glaze, and improve the quality of the glass-lined layer.
  • the present invention provides a glass-lined steel having a yield strength of 345 MPa or more, which contains the following chemical elements in addition to Fe and unavoidable impurities in terms of mass %: C: 0.08 ⁇ 0.14%; Si: 0.16-0.30%; Mn: 0.80 ⁇ 1.20%; S: 0.001 ⁇ 0.015%; Al: 0.005 ⁇ 0.035%; RE: 0.0005 ⁇ 0.006%; Ti: 0.05-0.09%; V: 0.01 ⁇ 0.03%; 0 ⁇ N ⁇ 0.004%; O: 0.001 ⁇ 0.005%.
  • the present invention also provides a glass-lined steel having a yield strength of 345 MPa or more, which contains the following chemical elements in terms of mass %: C: 0.08 ⁇ 0.14%; Si: 0.16-0.30%; Mn: 0.80 ⁇ 1.20%; S: 0.001 ⁇ 0.015%; Al: 0.005 ⁇ 0.035%; RE: 0.0005 ⁇ 0.006%; Ti: 0.05-0.09%; V: 0.01 ⁇ 0.03%; 0 ⁇ N ⁇ 0.004%; O: 0.001 ⁇ 0.005%;
  • the balance is Fe and other inevitable impurities.
  • the glass-lined steel with a yield strength of 345 MPa or more described in the present invention further contains at least one of the following chemical elements: 0 ⁇ Cu ⁇ 0.08%; 0 ⁇ Cr ⁇ 0.08%; 0 ⁇ Ni ⁇ 0.04%; 0 ⁇ Mo ⁇ 0.04%.
  • the inevitable impurities in the glass-lined steel having a yield strength of 345 MPa or more described in the present invention P ⁇ 0.02%.
  • carbon, silicon and manganese are used as basic strengthening elements, and carbon, silicon and manganese are the main strengthening elements for achieving a yield strength of the steel plate of more than 345 MPa.
  • the existence of carbon in steel includes pearlite, carbide precipitation and solid solution carbon.
  • the present invention adds an appropriate amount of vanadium on the basis of adding an appropriate amount of alloy element titanium, and the vanadium forms vanadium carbonitride or vanadium carbide in the steel.
  • the present invention adds a very small amount of rare earth elements on the basis of adding an appropriate amount of alloy element titanium, which is beneficial to improving the continuous casting and pouring properties of steel.
  • C is an effective element for improving the strength of steel plates.
  • the carbon exists in the steel in the form of pearlite, carbide, solid solution, etc., and the cooling rate is controlled to prevent it from transforming into bainite, martensite and other structures.
  • the precipitation of pearlite and carbide in the steel plays a strengthening role, and an appropriate amount of pearlite structure is beneficial to stabilizing the strength of the steel before and after the glass lining is fired; on the other hand, during the enameling process, the precipitation of pearlite and carbide in the steel becomes a trap for capturing hydrogen, which plays a complementary role in improving the anti-scale explosion performance of the steel plate.
  • the present invention reduces the pearlite content in the steel by controlling the carbon content in the steel and adding alloying elements that form strong carbides, and prevents it from transforming into bainite, martensite and other structures through process control such as cooling rate.
  • the carbon content C of the present invention is 0.08-0.14%, which is not only much lower than that of Q345R, but also lower than the carbon content of 0.15% of conventional Q245R (see GB713-2014).
  • the present invention also adds strong carbide-forming elements such as titanium and vanadium, and part of the carbon exists in the form of compounds, which can significantly reduce the content of pearlite.
  • Si is a strengthening element, but too high a silicon content will impair the adhesion between the glass layer and the steel plate.
  • the mass percentage content of Si element is controlled at a relatively low level, i.e., 0.16-0.30%.
  • Mn is a strengthening element.
  • the purpose of adding manganese to steel is to improve the strength of the steel.
  • adding too much manganese will not only increase the alloy cost, but also increase bubble defects as the manganese content increases, which will damage the quality of the glass layer. Therefore, the present invention controls the manganese content to 0.80-1.20%.
  • manganese and aluminum are both deoxidizing elements. Adding manganese and aluminum can reduce the oxygen content in steel. Based on this, the present invention controls Al to 0.005-0.035%.
  • RE Rare earth elements
  • RE are mainly cerium, lanthanum or a mixture of cerium and lanthanum. They are very easy to react with oxygen and sulfur to form rare earth oxides or oxysulfides in steel. Moreover, the formation temperature of these inclusions is high. Generally speaking, they begin to form in molten steel. Therefore, the quantity and form of these compounds are relatively stable in steel and are less affected by subsequent thermal processing. They are relatively stable and reliable hydrogen storage traps when making glass linings. They can replace part of titanium to reduce the amount of titanium added to steel. Based on this, the contents of rare earth elements, oxygen and sulfur are controlled within the following ranges: RE: 0.0005-0.006%, O: 0.001-0.005%, S: 0.001-0.015%.
  • V is a strong carbon and nitride forming element, and vanadium forms compounds such as VN, VC or V(CN) in steel.
  • vanadium forms compounds such as VN, VC or V(CN) in steel.
  • the precipitation of vanadium can be controlled by reasonably controlling the hot rolling temperature, rolling process and cooling process, so that the precipitation of vanadium can improve the strength and increase the hydrogen storage trap.
  • the titanium nitride formed when adding titanium can prevent the austenite from heating during heating. Grain growth. Based on the characteristics that the formed VC or V(CN) particles play a role in precipitation strengthening and improving hydrogen storage capacity, the amount of V added in the present invention is V: 0.01-0.03%.
  • Ti and N in steel is very easy to form titanium nitride inclusions with Ti in preference to V, and the higher the content of titanium and nitrogen, the greater the solubility product of nitrogen and titanium, the higher the formation temperature of titanium nitride, and the larger the particle diameter formed. Titanium nitride particles are beneficial hydrogen storage traps in steel, but the hydrogen trap effect of large-particle titanium nitride inclusions will be weakened, and plasticity and toughness will be seriously damaged. Therefore, the present invention controls the lower content of nitrogen 0 ⁇ N ⁇ 0.004% and titanium 0.05 ⁇ 0.09% to avoid the formation of coarse titanium nitride inclusions, and optimizes the effect of titanium nitride on hydrogen storage and plasticity and toughness.
  • Cu, Ni, Cr and Mo are all residual elements in steel, so the inventors do not intentionally add these elements.
  • a very small amount of Cu, Ni, Cr and Mo is beneficial to the adhesion between the steel plate and the glass layer, but when the content is too high, it will hinder the adhesion between the steel plate and the glass layer. Therefore, when these elements exist in steel, their content is controlled as follows: 0 ⁇ Cu ⁇ 0.08%; 0 ⁇ Cr ⁇ 0.08%; 0 ⁇ Ni ⁇ 0.04%; 0 ⁇ Mo ⁇ 0.04%.
  • the microstructure of the glass-lined steel with a yield strength of 345 MPa or more described in the present invention is ferrite + dispersed pearlite, and does not contain martensite or bainite structure.
  • the term "dispersed state” means that the pearlite in the steel is substantially discontinuous or not in a banded form. Specifically, the maximum length of the continuous pearlite structure is not more than 50 ⁇ m, preferably not more than 30 ⁇ m.
  • the inclusions of the glass-lined steel having a yield strength of 345 MPa or more described in the present invention include rare earth oxides and rare earth oxysulfides.
  • the glass-lined steel with a yield strength of 345 MPa or above described in the present invention has a yield strength ⁇ 345 MPa, a tensile strength ⁇ 450 MPa, an elongation A50 ⁇ 27%, and a 0°C Charpy impact energy Akv ⁇ 120 J.
  • the glass-lined steel with a yield strength of more than 345 MPa described in the present invention has a thickness of 8-40 mm.
  • Another object of the present invention is to provide a method for manufacturing glass-lined steel with a yield strength of more than 345 MPa, the manufacturing method has a short process flow, simple process operation, easy control of process parameters and high production efficiency.
  • the present invention provides a method for manufacturing glass-lined steel with a yield strength of more than 345 MPa, which comprises the following steps performed in sequence:
  • the method for manufacturing glass-lined steel with a yield strength of 345 MPa or more described in the present invention can directly air-cool the rolled steel plate to room temperature, or water-cool it to the required final cooling temperature, and then air-cool it to room temperature, without the need for forced cooling or heat treatment steps. Therefore, the process flow is short, the manufacturing process is simple, the production efficiency is high, and the manufacturing cost is low.
  • the purpose of smelting and refining is to ensure the basic components of molten steel, remove impurity elements and harmful gases in the steel, and add alloys such as manganese, aluminum, silicon, and then add alloy elements such as titanium and vanadium and make them fully uniform and chemical composition adjustment, and finally add rare earth alloys including cerium, lanthanum and their mixtures in the form of alloys or wire feeding.
  • continuous casting operation can effectively ensure that the internal components of the slab are uniform and the surface quality is good.
  • the thickness of the continuous casting slab is allowed to vary from 200 mm to 350 mm according to the thickness of the finished steel plate.
  • the heating temperature is controlled to be 1100-1200°C.
  • step (2) the heating temperature is controlled to be 1100-1200°C, and the slab is reheated.
  • the structure in the steel will transform into austenite, and the austenite structure transformation and homogenization will be completed under sufficient heating and heat preservation conditions.
  • the rare earth inclusions, titanium nitride and sulfide (manganese titanium) formed in the continuous casting slab are basically not affected, that is, they are rarely dissolved during heating, while the vanadium compounds are basically completely dissolved.
  • the hot rolling finishing temperature is controlled to be 820-900°C.
  • the hot rolling finishing temperature is controlled within a relatively high temperature range of 820-900°C. This is because: within this temperature range, the microstructure in the rolled steel completes phase transformation and complete recrystallization to form pearlite and ferrite structures.
  • the solid-dissolved vanadium precipitates into VC and V(CN) particles.
  • the state of inclusions such as rare earth compounds and titanium nitride generated during the continuous casting process is relatively stable and is little affected by the re-hot rolling heating and rolling process.
  • step (4) of the manufacturing method of the present invention when water cooling is used for cooling, the cooling rate is controlled to be ⁇ 50°C/s, and the final cooling temperature is 550-750°C.
  • the glass-lined steel plate with a yield strength of more than 345 MPa according to the present invention can be obtained.
  • the enameling process it is allowed to apply the base glaze once or twice and the top glaze multiple times, or it is also allowed to directly apply the top glaze multiple times without applying the base glaze.
  • the firing temperature can be between 860 and 930°C.
  • the glass-lined steel with a yield strength of 345 MPa or more and the manufacturing method thereof according to the present invention have the following beneficial effects:
  • the present invention adds alloy elements titanium, vanadium and a small amount of rare earth elements, so that there are sufficient hydrogen storage traps in the steel that are less affected by the subsequent processing technology and can be stably controlled, and can prevent the nozzle from being blocked during the continuous casting process to achieve smooth continuous casting.
  • This can further enable the steel to be coated with only one base glaze or directly coated with top glaze without base glaze in the processing of glass-lined products, reducing the number of enameling times or firing times.
  • the present invention reduces the carbon content of the steel plate and improves the strength of the steel plate through strengthening mechanisms such as solid solution strengthening of alloy elements silicon, manganese and vanadium and precipitation strengthening of titanium and vanadium, which is beneficial to improving the plasticity, weldability and anti-glass lining bubble ability of the steel plate.
  • the carbon equivalent in the steel is reduced, and the transformation process of pearlite and ferrite to austenite can be significantly delayed during the heating process of glass lining sintering, preventing the growth of austenite grains.
  • the glass-lined steel with a yield strength of more than 345 MPa described in the present invention has a reduced steel plate thickness compared to the Q245R steel plate.
  • the container wall thickness can be reduced by more than 10%, thereby achieving lightweighting.
  • the glass-lined steel with a yield strength of more than 345 MPa described in the present invention can significantly improve the quality of the glass glaze layer because the pearlite content in the steel is significantly lower than that in commonly used Q245R or Q345R steel plates.
  • FIG. 1 is a metallographic structure photograph of glass-lined steel with a yield strength of more than 345 MPa under an optical microscope according to Example 3 of the present invention.
  • FIG. 2 is a photograph of the precipitation phase of the glass-lined steel with a yield strength of more than 345 MPa under a transmission electron microscope according to Example 3 of the present invention.
  • the glass-lined steels with a yield strength of 345 MPa or above in Examples 1-7 are all prepared by the following steps:
  • Table 1 lists the mass percentages of the chemical elements in the glass-lined steels with a yield strength of more than 345 MPa in Examples 1-7.
  • Table 2 lists the specific process parameters of glass-lined steel with a yield strength of 345 MPa or more in the above process steps of Examples 1-7.
  • Figure 1 is a metallographic structure photograph of the glass-lined steel with a yield strength of 345 MPa or more under an optical microscope in Example 3 of the present invention.
  • the microstructure of the glass-lined steel plate is ferrite + a small amount of pearlite (white is ferrite, black is pearlite), the pearlite is dispersed rather than distributed in a band, the maximum length does not exceed 30 ⁇ m, and does not contain martensite or bainite structure.
  • Figure 2 is a transmission electron microscope photograph of the precipitation phase of the glass-lined steel with a yield strength of 345 MPa or more according to Example 3 of the present invention. From Figure 2, V(CN) (black structure) distributed along the ferrite grain boundary can be seen.
  • the tensile test was processed into circular tensile specimens, 3 pieces per group, and the yield strength, tensile strength and elongation were tested according to the room temperature tensile test method of GB/T 228, and the average value was taken; the impact specimens were processed into Charpy impact specimens, and the specimen notch shape was KV2, 3 pieces per group, and the 0°C impact value was tested according to the impact test method of GB/T 229, and the average value was taken.
  • the test results are listed in Table 3.
  • the yield strength of the glass-lined steel with a yield strength of 345 MPa or more in Examples 1-7 is ⁇ 375 MPa
  • the tensile strength is ⁇ 454 MPa
  • the elongation A is ⁇ 27%
  • the 0°C Charpy impact energy Akv is ⁇ 124 J. It can be seen that the glass-lined steel with a yield strength of 345 MPa or more has high strength and low-temperature toughness.

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

Abstract

L'invention concerne un acier vitrifié présentant une limite d'élasticité de 345 MPa ou plus, et son procédé de fabrication. L'acier vitrifié comprend les éléments chimiques suivants en pourcentage en masse : C : 0,08-0,14 % ; Si : 0,16-0,30 % ; Mn : 0,80 à 1,20 % ; S : 0,001 à 0,015 % ; P ≤ 0,02% ; Al : 0,005-0,035 % ; RE : 0,0005-0,006 % ; Ti : 0,05-0,09 % ; V : 0,01 à 0,03 % ; 0 ＜ N ≤ 0,004 % ; O : 0,001 à 0,005 % ; et comprend en outre au moins l'un des éléments parmi Cu, Cr, Ni et Mo, où : 0 < Cu ≤ 0,08 % ; 0 ＜ Cr ≤ 0,08 % ; 0 ＜ Ni ≤ 0,04 % ; et 0 ＜ Mo ≤ 0,04 %.
PCT/CN2024/071393 2023-01-10 2024-01-09 Acier vitrifié présentant une limite d'élasticité de 345 mpa ou plus, et son procédé de fabrication WO2024149253A1 (fr)

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Application Number Priority Date Filing Date Title
CN202310033305.1 2023-01-10
CN202310033305.1A CN118326248A (zh) 2023-01-10 2023-01-10 一种屈服强度345MPa以上的搪玻璃用钢及其制造方法

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WO2024149253A1 true WO2024149253A1 (fr) 2024-07-18

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Citations (8)

* Cited by examiner, † Cited by third party
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JPH0967647A (ja) * 1995-08-29 1997-03-11 Sumitomo Metal Ind Ltd ほうろう用冷延鋼板およびその製造方法
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