EP3124640B1 - Plaque d'acier ayant une limite d'élasticité de l'ordre de 890 mpa et une faible sensibilité à la fissuration de soudage et son procédé de fabrication - Google Patents

Plaque d'acier ayant une limite d'élasticité de l'ordre de 890 mpa et une faible sensibilité à la fissuration de soudage et son procédé de fabrication Download PDF

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EP3124640B1
EP3124640B1 EP15767692.5A EP15767692A EP3124640B1 EP 3124640 B1 EP3124640 B1 EP 3124640B1 EP 15767692 A EP15767692 A EP 15767692A EP 3124640 B1 EP3124640 B1 EP 3124640B1
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Prior art keywords
steel plate
rolling
steel
thickness
temperature
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EP3124640A4 (fr
EP3124640A1 (fr
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Liandeng Yao
Sixin Zhao
Pengjian WANG
Yuchuan MIAO
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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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
    • 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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0231—Warm rolling
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a method for manufacturing a steel plate with a high strength and low welding crack sensitivity, and in particular, a steel plate with a yield strength at an 890 Mpa level and low welding crack sensitivity.
  • the thermo-mechanical treatment of the steel plate is usually done by a controlled rolling and controlled cooling process (TMCP).
  • TMCP controlled rolling and controlled cooling process
  • the refinement of the microstructures or the formation of the high strength structures such as ultrafine bainite can be realized by controlling the deformation rate and cooling rate, thus improving the yield strength of the steel.
  • composition of the low-carbon and high-strength steel produced using TMCP is mainly Mn-Ni-Nb-Mo-Ti and Si-Mn-Cr-Mo-Ni-Cu-Nb-Ti-Al-B systems.
  • the chemical composition of a low-alloy and high-strength steel produced by the TMCP process in two temperature stages disclosed in WO 99/05335 A1 is as follows (wt.%): C: 0.05-0.10%, Mn: 1.7-2.1%, Ni: 0.2-1.0%, Mo: 0.25-0.6 Mo%, Nb: 0.01-0.10%, Ti: 0.005-0.03%, P ⁇ 0.015%, and S ⁇ 0.003%.
  • the chemical composition of a superlow carbon bainitic steel disclosed in CN 1 521 285 A is as follows (wt.%): C: 0.01-0.05%, Si: 0.05-0.55%, Mn: 1.0-2.2%, Ni: 0.0-1.0%, Mo: 0.0-0.5%, Cr: 0.0-0.7%, Cu: 0.0-1.8%, Nb: 0.015-0.070%, Ti: 0.005-0.03%, B: 0.0005-0.005%, and Al: 0.015-0.07%.
  • the alloying element designs of the above two types of the steels disclosed are an Mn-Ni-Nb-Mo-Ti and an Si-Mn-Cr-Mo-Ni-Cu-Nb-Ti-Al-B system respectively; since Mo and Ni are both precious metals, the production costs of such steel plates are relatively high from the analysis of the type and the total amount of the alloying elements added.
  • CN 103 060 690 A discloses a high-strength steel plate, comprising chemical elements in mass percentage of 0.070-0.115% of C, 0.20-0.50% of Si, 1.80-2.30% of Mn, 0-0.35% of Cr, 0.10-0.40% of Mo, 0.03-0.06% of Nb, 0.03-0.06% of V, 0.002-0.04% of Ti, 0.01-0.08% of Al, 0.0006-0.0020% of B, less than or equal to 0.0060% of N, less than or equal to 0.0040% of O, 0-0.0045% of Ca and the balance of Fe and other unavoidable impurities. Further, a method for manufacturing of such a high-strength steel plate is disclosed.
  • CN 101 481 774 A discloses a crack sensitivity steel plate with the yield strength of 500MPa, which is characterized by comprising the following chemical elements in terms of weight percentage: 0.010 to 0.09 percent of C, 0.10 to 0.65 percent of Si, 1.10 to 2.00 percent of Mn, less than or equal to 0.010 percent of P, less than or equal to 0.006 percent of S, 0.020 to 0.090 percent of Nb, 0.02 to 0.06 percent of Al, 0.004 to 0.030 percent of Ti, 0.0005 to 0.0025 percent of B and the balance of Fe and inevitable impurities.
  • the manufacturing method comprises the following steps: smelting and casting the raw materials into casting blank or steel ingot; 2) heating; 3) rolling; and 4) entering a cooling accelerator, cooling till the temperature of 450 to 560 DEG C, and air cooling after water drainage.
  • CN 102 618 793 A discloses a steel plate with yield strength of 960MPa, which comprises the following chemical components in weight percent: 0.07-0.11 percent of C, 0.10-0.50 percent of Si, 1.60-2.20 percent of Mn, not greater than 0.015 percent of P, not greater than 0.003 percent of S, 0.10-0.35 percent of Cr, 0.20-0.50 percent of Mo, 0.02-0.06 percent of Nb, 0.02-0.06 percent of V, 0.003-0.04 percent of Ti, 0.02-0.07 percent of Al, 0.0006-0.0025 percent of B and the balance of Fe and other inevitable impurities.
  • the steel plate with the yield strength of 960MPa also meets the following relational expressions: C+Mn is not less than 1.853Si+2.078Cr+3.112Mo-1298.532B but is not greater than 5.891Si+4.115Cr+4.797Mo-398.532B, and ln(AEQ) is not less than 2.08 but is not greater than 3.41.
  • the invention also discloses a manufacturing method for the steel plate.
  • the tensile strength of the obtained steel plate is not less than 980MPa
  • the Charpy impact power Akv (-40 DEG C) is not less than 80J
  • the carbon equivalent (CEV) is not greater than 0.58 percent.
  • An object of the present invention is to provide a steel plate with a yield strength at an 890 Mpa level and low welding crack sensitivity and a method for manufacturing the same, using the type of steel of an Si-Mn-Nb-Mo-V-Ti-Al-B system, by the controlled thermo-mechanical rolling and cooling technologies, without tempering, and the steel plate has a welding crack sensitivity index Pcm ⁇ 0.25%, a yield strength of greater than 890 MPa, a tensile strength of greater than 950 MPa, a Charpy impact energy Akv (-20°C) ⁇ 120 J, a plate thickness of up to 60 mm, has a good low-temperature toughness and weldability, and is a low-carbon superfine bainite lath steel plate with low welding crack sensitivity.
  • the technical solution of the present invention comprises the features of claim 1.
  • a further improvement is subject to dependent claim 2.
  • the manufacturing method of the invention results in a steel plate with a yield strength at an 890 Mpa level and low welding crack sensitivity, wherein the steel plate has the following components in weight percentage: C of 0.06-0.13 wt.%, Si of 0.05-0.70 wt.%, Mn of 1.20-2.30 wt.%, Mo of 0-0.25 wt.%, Nb of 0.03-0.11 wt.%, Ti of 0.002-0.050 wt.%, Al of 0.02-0.15 wt.%, and B of 0-0.0020 wt.%, with 2Si+3Mn+4Mo ⁇ 8.5 wt.%, the balance being Fe and inevitable impurities; and the steel plate meets the welding crack sensitivity index Pcm ⁇ 0.25%.
  • the contents of the three elements, Si, Mn and Mo, should comply with the following relationship: 2Si+3Mn+4Mo ⁇ 8.5 wt.%, to meet that the steel plate of the present invention has a good welding property. Specifically, it can be ensure that the steel plate having a thickness of 60 mm or less has no cracks upon welding at relatively low preheating temperature (normal temperature to 50°C) conditions.
  • the steel plate having a maximum thickness of 60 mm is produced using the chemical composition designed in the present invention and by reasonably using the action of various alloying elements.
  • the welding crack sensitivity index Pcm is an indicator for judging the weld cold cracking inclination of the steel, wherein the smaller the Pcm, the better the weldability, and conversely, the worse the weldability.
  • Good weldability means that the occurrence of weld cracking is not easy during welding; in contrast, cracks easily occur in the steel having poor weldability; in order to prevent cracking, steel is preheated before welding; the better the weldability, the lower the preheating temperature required, inversely, a higher preheating temperature is required.
  • a Pcm value for the type of steel of trademark Q800CF should be lower than 0.28%.
  • the superfine bainite lath steel plate with a high strength and low welding crack sensitivity involved in the present invention has a welding crack sensitivity of lower than 0.20%, and has an excellent welding property.
  • a method for manufacturing a steel plate with a yield strength at 890 Mpa level and low welding crack sensitivity of the present invention comprises the steps of:
  • the following chemical components were smelt and casted to a continuous casting billet or steel ingot of a thickness not less than 4 times of the thickness of the finished steel plate; wherein the steel plate has the following components in weight percentage: C of 0.06-0.13 wt.%, Si of 0.05-0.70 wt.%, Mn of 1.20-2.30 wt.%, Mo of 0-0.25 wt.%, Nb of 0.03-0.11 wt.%, Ti of 0.002-0.050 wt.%, Al of 0.02-0.15 wt.%, and B of 0-0.0020 wt.%, with 2Si+3Mn+4Mo ⁇ 8.5 wt.%, the balance being Fe and inevitable impurities; and the steel plate meets the welding crack sensitivity index Pcm ⁇ 0.25%;
  • the heating temperature is 1050-1180°C, and the holding time is 120 to 180 minutes; the rolling is divided into a first stage of rolling and a second stage of rolling; during the first stage of rolling, the start rolling temperature is 1050-1150°C, and when the thickness of the rolled piece reached 2-3 times of the thickness of the finished steel plate, it is stayed in the roller bed until the temperature reached 800-860°C; during the second stage of rolling, the pass deformation rate is 10-28%, and the finish rolling temperature is 780-840°C;
  • the steel plate is cooled to 220-350°C at a speed of 15-30°C/S, and air cooled after being out of water; a Charpy impact energy Akv (-20°C) of the steel plate is ⁇ 120 J. further, in step 3), the air cooling is cooling in packed formation or in a cold bed.
  • the non-recrystallizing temperature is about 950-1050°C. It is firstly rolled at a relatively high temperature, and there is a certain dislocation density in the austenite. During the relaxation process of lowering the temperature of the rolled billet to 800-860°C, a recovery and static recrystallization process inside the austenite crystal grains occur, thus refining the austenite crystal grains. In the relaxation process, individual precipitation and complex precipitation of carbonitrides of Nb, V and Ti occur simultaneously.
  • the precipitated carbonitrides pin the dislocation and subgrain boundary movements, reserves a lot of dislocation in the austenite crystal grains, and provides a lot of nucleation sites for the formation of bainite during the cooling process. Rolling at 800-860°C greatly increases the dislocation density in the austenite.
  • the carbonitride precipitated at the dislocation inhibits the coarsing of the deformed crystal grains. Due to the precipitating effect induced by deformation, a relatively large pass deformation rate will facilitate the formation of finer and more diffusive precipitates.
  • the precipitates from high density dislocation and fine diffusion provide high density of nucleation sites for bainite, and the pining effect of the second phase particles on the bainite growth interface inhibits the growth and coarsing of the bainite laths, which is beneficial for both the strength and toughness of the steel.
  • the finish rolling temperature is controlled in the low temperature section of the non-recrystallization zone, and at the same time, this temperature zone is close to the phase transmission point Ar 3 , i.e. the finish rolling temperature is 780-840°C, and finishing rolling within this temperature range can increase the defects in the austenite by increasing the deformation and inhibiting the recovery, thus providing higher energy accumulation for the bainite phase change without bringing about a too high load to the roller, being suitable for producing a thick plate.
  • the steel plate is sent to an accelerated cooling device, and cooled to 220-350°C at a rate of 15-30°C/s.
  • a faster cooling speed can avoid the formation of ferrite and pearlite, and directly enters the bainite transition area of the CCT curve.
  • a faster cooling speed results in the overcooling of the austenite, increases the driving force of a chemical phase change, and increase the driving force of the bainite nucleation when considered by combining the strain storage energy ⁇ G d caused during the rolling process. Due to the high dislocation density in the crystal grains, the nucleation sites of bainite increase. Considered by combining both the thermodynamic and dynamic factors, the bainite can nucleate at a very large speed.
  • a faster cooling speed enables the bainite transformation to be completed quickly and inhibits the coarsing of the bainite ferrite laths. Air cooling in packed formation at 220-350°C can enable a more complete precipitation of the carbide of V in the ferrite, thus enhancing the contribution of the precipitation strengthening to the strength. Therefore, the matrix structure composed mainly of the refined bainite can be obtained by the heat treatment process of the present invention, so as to produce steel plates having a higher strength and a good toughness.
  • the thermo-mechanical treatment of the steel plate is usually done by a controlled rolling and controlled cooling process (TMCP).
  • TMCP controlled rolling and controlled cooling process
  • the refinement of the microstructures or the formation of the high strength structures such as ultrafine bainite can be realized by controlling the deformation rate and cooling rate, thus improving the yield strength of the steel.
  • a microalloy element Nb is added, and during the heat treatment Nb may form a carbonitride, which has a precipitation strengthening effect.
  • Nb in a solid solution in the matrix has a solid solution strengthening effect.
  • modified TMCP and Relaxation Precipitation Controlling (RPC) technologies are used to form a stable dislocation network, and diffusive and fine second phase particles precipitate out at the dislocation and subgrain boundary; the refinement of the bainite lath is achieved by promoting the nucleation and inhibiting the growth, and a combined action of dislocation strengthening, precipitation strengthening and fine grain strengthening is formed, thus improving the strength and roughness of the steel, its principle mechanism being as follows: the steel plate fully deforms in the recrystallization zone, such that a high defect accumulation occurs in the deformed austenite, thus greatly increasing the dislocation density in the austenite.
  • Dislocation within the crystals will be re-arranged during the controlled cooling relaxation after rolling and deforming. Since a hydrostatic pressure field exits in the edge dislocation, interstitial atoms such as B will enrich to the dislocation, grain boundary and subgrain boundary, and reduce the dislocation mobility. The high density dislocation resulting from the deformation will evolve during the recovery to form a stable dislocation network.
  • the microalloy elements such as Nb, V, Ti precipitate out at the grain boundary, subgrain boundary and dislocations in the form of carbonitrides of different stoichiometric ratios such as (Nb, V, Ti) x (C,N) y .
  • the second phase particles such as the precipitated carbonitrides, pin the dislocations and subgrain boundary within the crystal grains and stabilize the substructures, such as dislocation walls and the like.
  • the dislocation density of the steel is further increased by rolling.
  • the deformed austenite is accelerated cooled, the deformed austenite crystal grains with dislocation and carbonitride precipitation configuration at the beginning of the phase change is different from the circumstance that after deformation, no relaxation occurs and there are a lot of dislocations disorderly distributed.
  • a subgrain boundary with a certain orientation difference is a preferred nucleation site, and if a second phase, which has a heterophasic interface with the matrix, precipitates out nearby, this will be more advantageous for the new phase nucleation during phase change.
  • a lot of new phase crystal grains will nucleate within the original austenite crystal grains.
  • the orientation difference between the subgrains is increased to a certain extent. After the medium temperature transformed product, such as bainite, nucleates at the subgrain boundary, it is hindered by the front subgrain boundary during the growth.
  • the bainite ferrite forms, its phase change interface is daggled by the precipitated second phase carbonitride particles, which inhibits its growth process.
  • the TMCP + RPC process results in a high density dislocation network structure, and the second phase precipitation particle points provide a lot of potential nucleation sites for the nucleation of the bainite ferrite
  • the daggling effect of the second phase particles to the moving interface and the evolved subgrain boundary have an inhibiting effect on the growth of the bainite.
  • the combined effect of promoting the nucleation and inhibiting the growth in the process refines the bainite ferrite laths of the final structure.
  • Table 1 is the chemical composition (wt.%) of the steel plate of the examples of the present invention and the Pcm (%) values.
  • Table 2 is the mechanical property of the steel plate of the examples of the present invention.
  • Table 3 is the test (small Tekken test) results of the welding property of the steel plate with an 890 Mpa level and low welding crack sensitivity of Example 1 of the present invention.
  • the chemical components as shown in Table 2 are smelt in an electric furnace or a converter and casted to a continuous casting billet or steel ingot, which is then heated to 1110°C for a holding time of 120 min and is subjected to a first stage of rolling in a middle, and thick rolling mill, wherein the start rolling temperature is 1050°C, when the thickness of the rolled piece is 60 mm, it is stayed in the roller bed until the temperature reached 850°C, and then a second stage of rolling is performed, wherein the pass deformation rate in the second stage of rolling is 15-28%, the finish rolling temperature is 830°C, and the thickness of the finished steel plate is 20 mm.
  • the steel plate is sent to an accelerated cooling (ACC) device, and cooled to 300°C at a rate of 30°C/s, followed by cooling in packed formation or in a cold bed after being out of water.
  • ACC accelerated cooling
  • Example 1 It is performed as in Example 1,wherein the heating temperature is 1050°C and holding time is 240 min; the start rolling temperature in the first stage of rolling is 1040°C, and the thickness of the rolled piece is 90 mm; the start rolling temperature in the second stage of rolling is 840°C, the pass deformation rate is 15-20%, the finish rolling temperature is 810°C, and the thickness of the finished steel plate is 30 mm; and the cooling rate of the steel plate is 25°C/S, and the final temperature is 350°C.
  • Example 1 It is performed as in Example 1,wherein the heating temperature is 1150°C and the holding time is 150 min; the start rolling temperature in the first stage of rolling is 1080°C, and the thickness of the rolled piece is 120 mm; the start rolling temperature in the second stage of rolling is 830°C, the pass deformation rate is 10-15%, the finish rolling temperature is 820°C, and the thickness of the finished steel plate is 40 mm; and the cooling rate of the steel plate is 20°C/S, and the final temperature is 330°C.
  • Example 1 It is performed as in Example 1,wherein the heating temperature is 1120°C and the holding time is 180 min; the start rolling temperature in the first stage of rolling is 1070°C, and the thickness of the rolled piece is 150 mm; the start rolling temperature in the second stage of rolling is 830°C, the pass deformation rate is 10-20%, the finish rolling temperature is 800°C, and the thickness of the finished steel plate is 50 mm; and the cooling rate of the steel plate is 15°C/S, and the final temperature is 285°C.
  • Example 1 It is performed as in Example 1,wherein the heating temperature is 1130°C and the holding time is 180 min; the start rolling temperature in the first stage of rolling is 1080°C, and the thickness of the rolled piece is 150 mm; the start rolling temperature in the second stage of rolling is 840°C, the pass deformation rate is 10-15%, the finish rolling temperature is 810°C, and the thickness of the finished steel plate is 60 mm; and the cooling rate of the steel plate is 15°C/S, and the final temperature is 220°C.
  • Example 1 It is performed as in Example 1,wherein the heating temperature is 1120°C and the holding time is 180 min; the start rolling temperature in the first stage of rolling is 1050°C, and the thickness of the rolled piece is 120 mm; the start rolling temperature in the second stage of rolling 820°C, the pass deformation rate is 15-25%, the finish rolling temperature is 780°C, and the thickness of the finished steel plate is 40 mm; and the cooling rate of the steel plate is 20°C/S, and the final temperature is 300°C.
  • Table 1 unit weight percentage Examples C Si Mn Nb Al Ti Cr Mo B Fe Pcm 1 0.09 0.35 1.80 0.070 0.02 0.015 0.16 0.25 0.0018 the balance 0.22 5 2 0.06 0.70 2.25 0.045 0.06 0.020 0 0 0.0010 the balance 0.20 1 3 0.08 0.40 2.06 0.085 0.04 0.050 0.20 0.10 0.0011 the balance 0.21 9 4 0.13 0.55 1.20 0.110 0.15 0 0.16 0.25 0.0015 the balance 0.24 1 5 0.06 0.05 1.45 0.065 0.07 0.020 0.12 0.20 0.0010 the balance 0.15 9 6 0.10 0.15 1.90 0.095 0.09 0.008 0.15 0.22 0.0020 0.23 2 Table 2 Examples Yield strength MPa Tensile strength MPa Elongation % -20°C Longitudinal impact energy J 1 940 1050 16.0 189 216 204 965 1065 16.5 2 950 1060 15.9 208 190 209 975 1070 15.2 3 955 1058 1
  • the Pcm of the steel plate with a yield strength at an 890 Mpa level and low welding crack sensitivity involved in the present invention is ⁇ 0.25%
  • the yield strength is larger than 890 MPa
  • the tensile strength is larger than 950 MPa
  • the Charpy impact energy Akv (-20°C) is ⁇ 120 J
  • the plate thickness can be up to 60 mm
  • the steel plate has an excellent low-temperature toughness and weldability.
  • Example 1 of the present invention is tested for the welding property (small Tekken test), under conditions of room temperature and 50°C, and no crack is observed (see table 3), indicating that the type of steel of the present invention has an excellent welding property, and generally does not require preheating when welding.
  • Table 3 Test temp eratu re Examples Surface crack rate % Root crack rate % section crack rate % Environ mental temperat ure Relat ive humi dity RT 1 0 0 0 22°C 60% 2 0 0 0 3 0 0 0 50°C 4 0 0 0 5 0 0 0 0 0

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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)
  • Heat Treatment Of Steel (AREA)

Claims (2)

  1. Procédé pour fabriquer une plaque d'acier avec une limite d'élasticité au niveau de 890 Mpa et une faible sensibilité aux fissures de soudage, comprenant les étapes de:
    1) fusion et coulée
    les composants chimiques suivants ont été fondus et coulés en une billette de coulée continue ou lingot d'acier d'une épaisseur non inférieure à 4 fois l'épaisseur de la plaque d'acier finie; la billette de coulée continue ou le lingot d'acier a les composants chimiques suivants en pourcentage en poids: C de 0,06-0,13% en poids, Si de 0,05-0,70% en poids, Mn de 1,20-2,30% en poids, Mo de 0-0,25% en poids, Nb de 0,03-0,11% en poids, Ti de 0,002-0,050% en poids, Al de 0,02-0,15% en poids, B de 0-0,0020% en poids et Cr de 0-0,20% en poids avec 2Si + 3Mn + 4Mo ≤ 8,5% en poids, le complément étant Fe et des impuretés inévitables; et la plaque d'acier répond à l'indice de sensibilité aux fissures de soudage Pcm ≤ 0,25% selon la formule: Pcm = C + Si/30 + Ni/60 + (Mn + Cr + Cu)/20 + Mo/15 + V/10 + 5B;
    2) chauffage et laminage
    la température de chauffage est 1050-1180°C et le temps de maintien est 120 à 180 minutes; le laminage est divisé en une première étape de laminage et une seconde étape de laminage; pendant la première étape de laminage, la température de laminage commençant est 1050-1150°C, et lorsque l'épaisseur de la pièce laminée atteint 2-3 fois l'épaisseur de la plaque d'acier finie, elle est maintenue dans le train de rouleaux jusqu'à ce que la température atteigne 800-860°C;
    pendant la seconde étape de laminage, le taux de déformation par passe est 10-28% et la température de laminage de finition est 780-840°C;
    3) refroidissement
    la plaque d'acier est refroidie à 220-350°C à une vitesse de 15-30°C/S, et refroidie à l'air après avoir été hors de l'eau;
    la plaque d'acier ayant une limite d'élasticité > 890 MPa, une résistance à la traction > 950 MPa, une énergie de choc Charpy Akv (-20°C) ≥ 120 J et une épaisseur de plaque < 60 mm.
  2. Procédé pour fabriquer la plaque d'acier avec une limite d'élasticité au niveau de 890 Mpa et une faible sensibilité aux fissures de soudage selon la revendication 1, caractérisé en ce que, dans l'étape 3), le refroidissement à l'air est un refroidissement en formation tassée ou dans un lit froid.
EP15767692.5A 2014-03-25 2015-01-15 Plaque d'acier ayant une limite d'élasticité de l'ordre de 890 mpa et une faible sensibilité à la fissuration de soudage et son procédé de fabrication Active EP3124640B1 (fr)

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CN201410114779.XA CN103898406B (zh) 2014-03-25 2014-03-25 一种屈服强度890MPa级低焊接裂纹敏感性钢板及其制造方法
PCT/CN2015/070729 WO2015143932A1 (fr) 2014-03-25 2015-01-15 Plaque d'acier ayant une limite d'élasticité de l'ordre de 890 mpa et une faible sensibilité à la fissuration de soudage et son procédé de fabrication

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4245878A4 (fr) * 2021-02-26 2025-04-02 Nippon Steel Corporation Tôle d'acier et son procédé de production

Families Citing this family (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103898406B (zh) * 2014-03-25 2016-08-24 宝山钢铁股份有限公司 一种屈服强度890MPa级低焊接裂纹敏感性钢板及其制造方法
JP2019060006A (ja) * 2017-09-28 2019-04-18 株式会社日立製作所 合金部材及びそれを用いた製造物
CN108315666A (zh) * 2018-02-12 2018-07-24 舞阳钢铁有限责任公司 低焊接裂纹敏感性q500gje钢板及其生产方法
CN108642380B (zh) * 2018-05-15 2020-08-25 首钢集团有限公司 一种900MPa级别的抗冲击波钢板及其制造方法
CN109735764B (zh) * 2019-01-17 2019-12-31 江苏利淮钢铁有限公司 一种800MPa级高强韧性贝氏体汽车大梁扁钢及其生产方法
CN110004358B (zh) * 2019-03-29 2021-05-25 山东钢铁集团日照有限公司 一种低Pcm值大厚度易焊接海工钢板及其生产方法
CN113322420A (zh) 2020-02-28 2021-08-31 宝山钢铁股份有限公司 一种具有优异低温冲击韧性的控制屈强比钢及其制造方法
CN112575257B (zh) * 2020-12-04 2022-03-11 安阳钢铁股份有限公司 一种低成本含硼非调质700MPa高强度钢及其制造方法
CN114752850B (zh) * 2021-01-12 2023-03-14 宝山钢铁股份有限公司 一种屈服强度785MPa级高强钢板及其制造方法
CN113430460A (zh) * 2021-06-19 2021-09-24 宝钢湛江钢铁有限公司 一种屈服强度690MPa级低成本高强非调质钢板及其制造方法
CN113802057A (zh) * 2021-08-16 2021-12-17 共享铸钢有限公司 一种大型铸钢产品裂纹缺陷的控制方法
CN114150209B (zh) * 2021-11-16 2022-10-25 山东钢铁集团日照有限公司 一种屈服强度不小于550MPa的高性能桥梁钢及其制备方法和应用
CN116219292B (zh) * 2023-02-27 2025-02-18 鞍钢股份有限公司 一种超高强低焊接裂纹敏感性水电用钢及其制造方法
CN116607073B (zh) * 2023-05-26 2025-09-30 鞍钢股份有限公司 薄坯生产厚规格430MPa高韧性管桩用钢及生产方法
CN119194232B (zh) * 2023-06-27 2025-11-14 宝山钢铁股份有限公司 一种低成本690MPa级别不预热焊接煤矿机械用钢及其制造方法
CN119194240B (zh) * 2024-08-20 2025-11-21 马鞍山钢铁股份有限公司 屈服强度为90ksi级的连续油管用酸洗钢带及制备方法

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2752708B2 (ja) * 1989-07-27 1998-05-18 川崎製鉄株式会社 良加工性高強度熱延薄鋼板およびその製造方法
EP1708677A4 (fr) * 2004-01-07 2010-12-22 E L Management Corp Composition cosmetique contenant une proteine et un inhibiteur d'enzyme
JP4418391B2 (ja) * 2005-03-30 2010-02-17 新日本製鐵株式会社 音響異方性が小さい降伏強さ６５０ＭＰａ以上の高張力鋼板およびその製造方法
CN101418418B (zh) * 2007-10-26 2010-11-24 宝山钢铁股份有限公司 屈服强度690MPa级低裂纹敏感性钢板及其制造方法
CN101418416B (zh) * 2007-10-26 2010-12-01 宝山钢铁股份有限公司 屈服强度800MPa级低焊接裂纹敏感性钢板及其制造方法
CN101481774B (zh) * 2008-01-07 2010-11-24 宝山钢铁股份有限公司 一种屈服强度500MPa级低裂纹敏感性钢板及其制造方法
JP5337412B2 (ja) * 2008-06-19 2013-11-06 株式会社神戸製鋼所 脆性亀裂伝播停止特性に優れた厚鋼板およびその製造方法
KR101094310B1 (ko) * 2008-09-18 2011-12-19 한국기계연구원 저온인성이 우수한 용접성 초고강도강 및 그 제조방법
BR112012020133B1 (pt) * 2010-05-14 2018-07-17 Nippon Steel & Sumitomo Metal Corp chapa de aço e método pa ra sua produção
CN101942616B (zh) * 2010-09-15 2012-10-03 北京科技大学 一种高延伸率高强度低碳贝氏体钢板及其生产方法
CA2808119C (fr) * 2011-04-19 2014-07-08 Nippon Steel & Sumitomo Metal Corporation Tube d'acier soude par resistance electrique pour utilisation dans un puits de petrole, et son procede de production
CN102618793B (zh) * 2012-03-30 2013-11-20 宝山钢铁股份有限公司 一种屈服强度 960MPa 级钢板及其制造方法
CN103060690A (zh) * 2013-01-22 2013-04-24 宝山钢铁股份有限公司 一种高强度钢板及其制造方法
CN103484768B (zh) * 2013-09-30 2016-03-09 武汉钢铁(集团)公司 一种长度≥30m的高强工程用钢板及生产方法
CN103898406B (zh) * 2014-03-25 2016-08-24 宝山钢铁股份有限公司 一种屈服强度890MPa级低焊接裂纹敏感性钢板及其制造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4245878A4 (fr) * 2021-02-26 2025-04-02 Nippon Steel Corporation Tôle d'acier et son procédé de production

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EP3124640A4 (fr) 2017-12-27
EP3124640A1 (fr) 2017-02-01
JP6502377B2 (ja) 2019-04-17
KR102291866B1 (ko) 2021-08-20
CN103898406B (zh) 2016-08-24
BR112016021752B1 (pt) 2021-05-04
CN103898406A (zh) 2014-07-02
BR112016021752A2 (pt) 2017-08-15
JP2017512903A (ja) 2017-05-25
AU2015235813A1 (en) 2016-10-06
KR20160137542A (ko) 2016-11-30
US20180355452A1 (en) 2018-12-13

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