WO2016119500A1 - Plaque d'acier à haute performance de blocage de craquelures et son procédé de production - Google Patents

Plaque d'acier à haute performance de blocage de craquelures et son procédé de production Download PDF

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WO2016119500A1
WO2016119500A1 PCT/CN2015/093745 CN2015093745W WO2016119500A1 WO 2016119500 A1 WO2016119500 A1 WO 2016119500A1 CN 2015093745 W CN2015093745 W CN 2015093745W WO 2016119500 A1 WO2016119500 A1 WO 2016119500A1
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steel sheet
high crack
property according
crack arresting
arresting property
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PCT/CN2015/093745
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English (en)
Chinese (zh)
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李冰
张才毅
高珊
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宝山钢铁股份有限公司
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Priority to KR1020177023668A priority Critical patent/KR20170107070A/ko
Publication of WO2016119500A1 publication Critical patent/WO2016119500A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous 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
    • C22C38/18—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
    • 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
    • C21D8/0247—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
    • C22C38/002—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
    • C22C38/18—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
    • C22C38/48—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
    • 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
    • C21D2201/05—Grain orientation
    • 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

Definitions

  • the present invention relates to a steel sheet and a method of manufacturing the same, and more particularly to an alloy steel sheet and a method of manufacturing the same.
  • Japanese Patent Publication No. CN101307412A published on November 19, 2008, entitled "Stainless steel crack propagation stop characteristic and steel sheet having excellent toughness at the center portion of the thickness” and a method for producing the same, discloses a steel sheet.
  • the mass percentage (wt.%) of each chemical element in the steel sheet is: C: 0.01-0.06, Si: 0.01-0.8, Mn: 1.0-1.8, Cr: 0.05-0.5, Ni: 0.20-0.8, Mo : 0.05-0.5, Cu: 0.05-0.08, Alt: 0.01-0.08, Nb: 0.02-0.08, Ti: 0.005-0.03, B: 0.00003-0.0003, Ca: 0.0005-0.0030, N: 0.003-0.008, REM: 0.0050 -0.030; and the steel sheet is composed of a ferrite-based structure, and the orientation of the two crystals is in the region of the entire thickness of the portion of the outermost layer of the steel sheet corresponding to the thickness of 1%.
  • Crystal grains enclosed have an average equivalent circle diameter of 8 mm or less and satisfy the relationship of the following formula (1): 1-(A2 - A1) / 100 ⁇ 0.8, wherein A1: crystal grains having a crystal orientation difference of 55 or more The proportion (area%) in the population, A2: the proportion (area%) of the crystal grains having a crystal orientation difference of less than 15° in the whole.
  • the mass percentage (wt.%) of each chemical element of the steel sheet is: C: 0.01-0.30, Si: ⁇ 0.5, Mn: ⁇ 2.0, Cr: ⁇ 0.5, Ni: ⁇ 1.0, Mo: ⁇ 0.5, Cu : ⁇ 0.9, V: ⁇ 0.1, Alt: 0.001-0.1, Nb: 0.005-0.05, Ti: 0.005-0.02, B: 0.0003-0.003, Ca: 0.0003-0.005, N: 0.001-0.008, Mg: 0.0003-0.005 ;REM: 0.0003-0.005; the balance is Fe and other unavoidable impurities.
  • the technical solution of the above patent document adopts ultra-low carbon and repeated phase change means to obtain surface ultrafine crystal.
  • Japanese Patent Publication No. JP2002-241891A published on August 28, 2002, entitled "Structural steel having excellent brittle crack propagation stop characteristics and fatigue crack propagation characteristics after plastic deformation, and a method for producing the same"
  • the steel plate in the Japanese patent document adopts a chemical element composition design of ultra-low carbon, high Ni and no Al, and through the controlled rolling process, the (211) surface texture parallel to the rolling plane is developed, and (100) The crystal texture is
  • the object of the present invention is to provide a steel sheet having high crack arresting property, which has high strength and good low temperature impact toughness, and has a yield strength of ⁇ 400 MPa, and a -40 °C Charpy V-notch impact energy ⁇ 64 J.
  • it compared with the steel plate in the prior art, it has excellent crack arresting performance, and its non-plastic transition temperature (NDTT, Nil-Ductility Transition Temperature) ⁇ -70 ° C, which is particularly suitable for use in ships, offshore engineering structures, etc. Manufacturing field.
  • the present invention proposes a steel sheet having high crack arresting property, wherein the chemical element mass percentage content is:
  • the balance is Fe and other unavoidable impurities.
  • C is the most basic strengthening element.
  • a gap solid solution can be formed to function as a solid solution strengthening, and C can also be combined with a forming element of a strong carbide to form a carbide precipitate, thereby functioning as a precipitation strengthening.
  • C can also improve the hardenability of steel.
  • C which is too high in content will adversely affect the ductility, toughness, crack arrestability and weldability of the steel sheet, and also reduce the solid solution of microalloying elements such as Nb and V. Affect the precipitation enhancement effect.
  • the content of the C element in the steel sheet having high crack arresting property according to the present invention is controlled to be between 0.04 and 0.12%.
  • Si acts as a reducing agent and a deoxidizer to eliminate the adverse effects of FeO inclusions on steel.
  • Si exists in a solid solution state in ferrite or austenite, which can increase the hardness and strength of ferrite or austenite and reduce the austenite phase region.
  • the present invention controls Si to 0.10% ⁇ Si ⁇ 0.30%.
  • Mn is one of the most basic alloying elements for low-alloy high-strength steels.
  • the strength of the steel sheet is increased by solid solution strengthening of Mn to compensate for the loss of strength of the steel sheet due to a decrease in the C content in the steel sheet.
  • Mn is also an element that expands the ⁇ phase region, which can reduce the ⁇ phase temperature of steel. Degree, help to obtain fine phase change products in the steel plate to improve the toughness and crack arrest performance of the steel plate.
  • the mass percentage of Mn in the steel sheet having high crack arresting property of the present invention is from 0.60 to 1.90%.
  • Chromium is one of the important elements for improving the hardenability of steel sheets. For steel plates with extra-thickness specifications, it is necessary to increase the hardenability of the steel sheet by adding more Cr elements to compensate for the strength loss caused by the thickness, and to improve the strength of the steel sheet while improving the performance of the steel sheet in the thickness direction. Uniformity. Cr can also inhibit the transformation of pro-eutectoid ferrite and pearlite, which is beneficial to obtain acicular ferrite structure.
  • the content of Cr in the technical solution of the present invention should be limited to a range of 0.01% to 0.40%.
  • Nickel is an element that improves the low temperature toughness of materials. Adding an appropriate amount of Ni can reduce the stacking fault energy of the crystal, facilitate the slip motion of the dislocation, improve the impact toughness of the material, and especially improve the impact toughness of the central portion of the extra-thick plate. At the same time, the addition of Ni element in the technical solution can also improve the crack arrest performance of the steel sheet. In addition, Ni can also enhance the hardenability of Mo. However, if the Ni content is too high, the slab surface tends to form a high-viscosity iron oxide scale, which is difficult to remove in the subsequent manufacturing process, thereby affecting the surface quality and fatigue properties of the steel sheet.
  • the Ni content in the steel sheet having high crack arresting property according to the present invention needs to be controlled to be 0.10% to 0.70%.
  • Mo is an element that improves the hardenability of a steel sheet, and its effect is second only to the Mn element. Mo can not only effectively increase the strength of the steel sheet, but also inhibit the transformation of the pro-eutectoid ferrite and pearlite to help the steel sheet obtain the acicular ferrite structure. However, as the Mo content increases, the yield strength of the steel sheet gradually increases, while the plasticity of the steel sheet gradually decreases. For the steel sheet having high crack arresting property of the present invention, the mass percentage content of Mo should be set to 0.001% to 0.40%.
  • Cu can appropriately improve the hardenability of the steel sheet, and Cu can also improve the atmospheric corrosion resistance of the steel sheet.
  • the addition of an excessively high amount of Cu element to the steel deteriorates the weldability of the steel sheet, so the content of the Cu element in the steel sheet having high crack arresting property according to the present invention is controlled to be 0.001% to 0.50%.
  • Al is an element added to steel for deoxidation. After the deoxidation is complete, Al lowers the steel plate The content of O in the steel to improve the aging properties of the steel sheet. In addition, the addition of an appropriate amount of Al is also advantageous for refining the grains, thereby improving the toughness of the steel. Therefore, the content of the Al element in the steel sheet having high crack arresting property in the present invention is limited to 0.01 to 0.06%.
  • Nb is one of the most effective elements for increasing the recrystallization termination temperature. Nb can effectively reduce the rolling mill load and has a significant effect on grain refinement.
  • the rolling deformation is completed in the recrystallization and non-recrystallization rolling stages, and at this stage, Nb is precipitated by strain to inhibit the recovery and recrystallization of the deformed austenite, thereby refining The effect of grain size.
  • the Nb having a too high content cannot be dissolved, and the Nb is not advantageous.
  • Nb is also an expensive metal element, and adding more Nb will increase the manufacturing cost accordingly. Therefore, the Nb content in the steel sheet having high crack arresting property of the present invention should be controlled to be 0.01% to 0.06%.
  • Titanium is a strong solid N element. Since the Ti/N ratio is 3.42, a certain amount of N element can be fixed by using a small amount of Ti. For example, Ti of about 0.02 wt.% can fix N in a steel having a mass percentage of 60 ppm or less. In the slab continuous casting, the added Ti can form a fine high-temperature stable TiN precipitation phase with N. Such fine TiN particles can effectively hinder the growth of austenite grains during reheating of the slab, and contribute to the improvement of the solid solubility of Nb in austenite.
  • the addition of an appropriate Ti content is advantageous for the formation of stable TiN particles, which acts to suppress grain growth in the heat-affected zone during welding to improve the impact toughness of the weld heat affected zone.
  • N The nitride formed by N and alloying elements is a non-metallic inclusion, and more importantly, the N element reduces the role of the alloying element.
  • N also has a beneficial effect, and TiN formed with Ti can prevent the growth of austenite grains when the slab is heated.
  • its side effects are greater, so the technical solution limits the N content to ⁇ 0.007%.
  • the form of sulfide can be controlled by Ca treatment, the anisotropy of the steel sheet can be improved, and the low temperature toughness of the steel sheet can be improved.
  • the Ca content is less than 0.0001 wt.%, it does not produce any effect, and when the Ca content is more than 0.0045.wt%, many CaO, CaS are generated, and large inclusions are formed, which damages the toughness of the steel sheet. It even affects the welding performance of the steel sheet. Therefore, in the steel sheet having high crack arresting property of the present invention, it is necessary to set the Ca content to 0.0001% to 0.0045%.
  • Phosphorus, sulfur: P and S are inevitable harmful impurity elements in steel, they are easily formed in steel Defects such as segregation and inclusions deteriorate the weldability, impact toughness and anti-HIC performance of the steel sheet. For this reason, it is necessary to control P ⁇ 0.015 wt.% in the steel sheet having high crack arresting property of the present invention, and to control S to ⁇ 0.0040 wt.%.
  • the inclusion treatment of the S can be spheroidized and evenly distributed by the Ca treatment inclusion modification technique, reducing the influence on the toughness and corrosivity of the steel sheet.
  • Ca and S also need to satisfy: 1.0 ⁇ Ca / S ⁇ 2.0 in order to obtain a good sulfide treatment effect, thereby improving the crack arrest performance of the steel sheet.
  • the steel plate with high crack arresting property of the present invention does not add alloying elements such as V, Zr and W, and adopts low C, Ni-Cr-Mo alloying and Nb, Ti micro. Alloyed component system.
  • the steel sheet having high crack arresting property of the present invention has an average effective crystal grain size d ⁇ 7 ⁇ m and a grain orientation difference of ⁇ 15°.
  • a small angle grain boundary (grain orientation difference ⁇ 15°) does not effectively prevent crack propagation and thus has no effect on the toughness of the steel. This is because, in the small angle region, the grain boundary energy E increases with orientation, and when the orientation difference is ⁇ 15°, the grain boundary can reach the maximum value and remains unchanged. Only at large angle grain boundaries where the grain orientation difference is ⁇ 15°, the cleavage crack can undergo a significant transition, which consumes more energy. Therefore, the structural unit with a grain orientation difference of ⁇ 15° can be used as an effective crystal grain for controlling the cleavage crack propagation, and the higher the ratio of the large-angle grain boundary, the better the crack growth resistance is prevented.
  • the smaller the effective grain size obtained the stronger the ability to prevent crack propagation, that is, the better the crack arrest performance.
  • the inventors of the present technical solution have found that when the average effective grain size d ⁇ 7 ⁇ m, the crack arresting property is excellent, and conversely, the crack arresting property is rapidly lowered.
  • the steel material consists of a myriad of crystal grains.
  • the growth direction may be different, that is, the grain orientation is different (substructures with uniform grain orientation form a grain), different crystals
  • the difference in orientation between the particles is the difference in grain orientation. This difference in orientation is determined by setting a coordinate system. After determining the orientation of different crystal grains, the difference can be calculated.
  • the general grain orientation difference can be directly measured by EBSD and other methods. This technical terminology is well known to those skilled in the art, and thus is only briefly described herein and will not be described again.
  • the average effective grain size of the above-mentioned steel sheet having high crack arrestability needs to be obtained mainly by rational composition design and subsequent process control.
  • the steel sheet having high crack arresting property according to the present invention further contains B, which satisfies: 0 ⁇ B ⁇ 0.0025 wt.%.
  • the B element mainly serves to improve the hardenability of the steel sheet to ensure the mechanical properties of the steel sheet.
  • the B content is less than 0.0025 wt.%, the effect that can be achieved is optimal.
  • the premise that B can function is that it must be dissolved in steel, and the addition of Mo and Ti contributes to the improvement of the hardenability of B.
  • too high a C content will lower the hardenability of B, and based on this, in the case where B is added, the content of C should be kept at a low level.
  • C and Mn also satisfy: 0.10 wt% ⁇ C + Mn / 6 ⁇ 0.50 wt%.
  • Cr, Mo, B, C and Mn also satisfy: 0.9 wt% ⁇ (Cr + Mo + B) / (C + Mn / 6) ⁇ 3.3 wt%.
  • Ni, Nb, Ti, Al, C and Mn also satisfy: 0.9 wt% ⁇ (Ni + Nb + Ti + Al) / (C + Mn /6) ⁇ 2.2 wt%.
  • the above-mentioned added alloying elements are controlled under the premise of the defined mass percentage content, and further defining that these elements satisfy the above relationship is to ensure the balance of the alloying element content, so as to further ensure that the steel sheet obtains good strength and toughness matching, thereby The steel plate provides better crack arrest performance.
  • microstructure of the steel sheet having high crack arresting property according to the present invention is acicular ferrite + polygonal ferrite.
  • the microstructure is defined as ferrite + acicular ferrite, on the one hand, because the acicular ferrite itself has good crack arresting property, and on the other hand, because the two-phase structure has a lower
  • the yield ratio is sufficient to absorb energy and improve the crack arrest performance.
  • the comparative example (area ratio) of the above acicular ferrite is ⁇ 90%.
  • acicular ferrite ⁇ 90% is beneficial to further prevent crack propagation and improve the crack arrest performance of the steel.
  • the present invention also provides the above-described method for producing a steel sheet having high crack arresting properties, which comprises the steps of: smelting, refining, casting, slab heating, controlled rolling, and controlled cooling.
  • the heating temperature T 1120+420 C Nb +190 C Ti ⁇ 20, wherein the temperature unit is °C, C Nb is the content of Nb, the unit is wt.%, and C Ti is the content of Ti, and the unit is wt.%.
  • the purpose of setting the reheating temperature of the steel sheet slab is to ensure sufficient solid solution of microalloying elements such as Nb, V, Ti, etc., and to ensure precipitation of carbonitrides in the subsequent rolling process to prevent recrystallized grains. Growing up, thus playing the role of refining the grains.
  • the rolling temperature is Ar3+200°C to Ar3+350°C
  • the finishing rolling temperature is Ar3+40°C. ⁇ Ar3 + 100 ° C.
  • Ar3 is the temperature at which the austenite changes to a ferrite equilibrium phase transition
  • the arc rolling temperature is controlled to Ar3+200°C to Ar3+350°C in order to ensure that the steel sheet starts rolling in the recrystallization zone to fully recrystallize.
  • the precipitation of the nitride further effects the precipitation precipitation strengthening.
  • the cumulative reduction ratio is 60 to 99% in the controlled rolling step.
  • the cumulative reduction ratio in the controlled rolling step is limited to 60 to 99% in order to sufficiently deform the steel sheet, to refine the grain in the steel, and in particular to ensure sufficient deformation of the core portion of the steel sheet to obtain a uniform structure.
  • the cooling temperature is Ar3 + 15 ° C to Ar 3 + 50 ° C
  • the final cooling temperature is 250 to 450 ° C. .
  • the reason for setting the cooling temperature is to rapidly cool the steel sheet under the condition of complete austenitizing to obtain the microstructure required for the steel sheet, and the reason for setting the final cooling temperature is as follows:
  • the final cooling temperature range is lower than the phase transition end temperature of the acicular ferrite, which can cause the steel sheet to undergo a sufficient phase transformation, thereby obtaining more than 90% of acicular ferrite, thereby giving the steel sheet good strength and crack arresting performance.
  • the cooling rate is 10 to 30 ° C/s.
  • the cooling rate is obtained.
  • the control is 10 to 30 ° C / s.
  • the steel plate with high crack arresting property of the invention has high strength and good low temperature impact toughness, and its yield strength is ⁇ 400Mpa, and the -40°C Charpy V-notch impact energy is ⁇ 64J.
  • the steel sheet having high crack arresting property according to the present invention has excellent crack arresting performance and has a plasticity-free transition temperature (NDTT) ⁇ -70 ° C as compared with the steel sheet of the same thickness in the prior art.
  • NDTT plasticity-free transition temperature
  • the technical solution described in the present invention is capable of producing a steel sheet having a high crack arresting property of thickness ⁇ 90 mm, and is particularly suitable for production in the field of marine and offshore engineering structures.
  • the reduction rate is 60 to 99%;
  • the opening temperature is Ar3 + 15 ° C ⁇ Ar3 + 50 ° C
  • the final cooling temperature is 250 ⁇ 450 ° C
  • the cooling rate is 10 ⁇ 30 ° C / s
  • Table 1 lists the mass percentage contents of the respective chemical elements in the steel sheets of Examples A1 to A8.
  • Ceq C + Mn / 6 + (Cr + Mo + V) / 5 + (Ni + Cu) / 15.
  • Table 2 lists the process parameters of the method for producing the steel sheets in Examples A1 to A8.
  • Table 3 lists the relationship and average effective grain size parameters satisfied by the relevant chemical elements in the steel sheets of Examples A1 - A8.
  • the finished board in the above embodiment is subjected to rod stretching ( ⁇ 10 mm) or plate stretching, Charpy V-notch impact, and NDTT performance test (Nil-Ductility Transition Temperature, NDTT performance is an important index for measuring the crack arrestability of the steel sheet)
  • the mechanical properties obtained are shown in Table 4.
  • Table 4 lists the mechanical properties of the steel sheets having high crack arresting properties in Examples A1 to A8 of the present invention.
  • NDTT is Nil-Ductility Transition Temperature.
  • the steel sheets in the examples A1-A8 of the present case have high strength, the yield strength is ⁇ 412 MPa, the tensile strength is ⁇ 524 MPa, and the low temperature toughness is good, and the average value of the impact work is 276 J or more.
  • the elongation rate is over 24%.
  • the steel sheets in Examples A1 to A8 also had excellent crack arresting properties, and their plastic-free transition temperatures (NDTT) ⁇ -75 °C. Therefore, the steel plate with high crack arresting property according to the present invention can be applied to key parts such as ships and offshore engineering structures. Manufacturing and production of components.

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  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne une plaque d'acier à haute performance de blocage de craquelures et son procédé de production ; les teneurs (en % en poids) des éléments chimiques dans la plaque d'acier sont les suivantes : 0,04 % ≤ C ≤ 0,12 %, 0,10 % ≤ Si ≤ 0,30 %, 0,60 % ≤ Mn ≤ 1,90 %, P ≤ 0,015 %, S ≤ 0,0040 %, 0,01 % ≤ Cr ≤ 0,40 %, 0,10 % ≤ Ni ≤ 0,70 %, 0,001 % ≤ Mo ≤ 0,40 %, 0,001 % ≤ Cu ≤ 0,50 %, 0,01 % ≤ Al ≤ 0,06 %, 0,01 % ≤ Nb ≤ 0,06 %, 0,01 % ≤ Ti ≤ 0,06 %, N ≤ 0,007 %, 0,0001 % ≤ Ca ≤ 0,0045 % et 1,0 ≤ Ca/S ≤ 2,0 et le reste étant composé de Fe et d'impuretés inévitables. L'invention concerne également un procédé de production de la plaque d'acier, le procédé de fabrication comprenant les étapes suivantes : fonte, affinage externe, coulée, chauffage de dalle, laminage contrôlé et refroidissement contrôlé.
PCT/CN2015/093745 2015-01-30 2015-11-04 Plaque d'acier à haute performance de blocage de craquelures et son procédé de production WO2016119500A1 (fr)

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