WO2014201887A1 - 超高韧性、优良焊接性ht550钢板及其制造方法 - Google Patents

超高韧性、优良焊接性ht550钢板及其制造方法 Download PDF

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WO2014201887A1
WO2014201887A1 PCT/CN2014/074084 CN2014074084W WO2014201887A1 WO 2014201887 A1 WO2014201887 A1 WO 2014201887A1 CN 2014074084 W CN2014074084 W CN 2014074084W WO 2014201887 A1 WO2014201887 A1 WO 2014201887A1
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steel plate
rolling
steel
toughness
temperature
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French (fr)
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刘自成
李先聚
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to KR1020157032995A priority Critical patent/KR20150143838A/ko
Priority to CA2914441A priority patent/CA2914441C/en
Priority to JP2016514253A priority patent/JP6198937B2/ja
Priority to US14/889,052 priority patent/US10208362B2/en
Priority to BR112015027406-4A priority patent/BR112015027406B1/pt
Priority to EP14813459.6A priority patent/EP3012340B1/en
Priority to ES14813459T priority patent/ES2790421T3/es
Publication of WO2014201887A1 publication Critical patent/WO2014201887A1/zh
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • 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
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • 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
    • C21D8/0247—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 heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • C21D8/0247—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 heat treatment
    • C21D8/0263—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 heat treatment following hot rolling
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • 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
    • C21D2211/002—Bainite
    • 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 invention relates to an ultra-high toughness and excellent weldability HT550 steel plate and a manufacturing method thereof, and the Charpy impact of the yield strength ⁇ 460 MPa, the tensile strength 550 MPa to 700 MPa, the yield ratio ⁇ 0.85, - 60 ° C is obtained by the TMCP process.
  • the microstructure of the steel plate is fine ferrite + self-tempered bainite, and the average grain size is below 15 ⁇ . Background technique
  • low carbon (high strength) low alloy steel is one of the most important engineering structural materials, widely used in oil and gas pipelines, offshore platforms, shipbuilding, bridge structures, boiler containers, building structures, automotive industry, railway transportation and machinery manufacturing. in.
  • low-carbon (high-strength) low-alloy steel depends on its chemical composition and process regime of the manufacturing process. Among them, strength, plasticity, toughness and weldability are the most important properties of low-carbon (high-strength) low-alloy steel, which ultimately depends on The microstructure of the finished steel. As technology continues to advance, people have higher requirements for the toughness and strong plasticity of high-strength steel, that is, while maintaining low manufacturing costs, the mechanical properties and performance of steel sheets are greatly improved. In order to reduce the amount of steel used to save costs, reduce the weight, stability and safety of the steel structure, it is more important to further improve the safety and stability of the steel structure, durability and hot and cold processability, adapt to different construction environments, different processing Process requirements.
  • Japan, South Korea and the European Union have set off a research climax to develop a new generation of high-performance steel materials, and strive to obtain better structural matching through alloy combination optimization and innovative manufacturing technology, so that high-strength steel can obtain better toughness and strong plasticity. match.
  • Ni element can not only improve the strength and hardenability of the steel sheet, but also reduce the phase transition temperature and refine the Bayesian Body/martensitic lath grain size; more importantly, Ni can only improve bainite/
  • the elements of intrinsic low temperature toughness of martensite laths increase the orientation angle between bainite/martensitic laths and increase the propagation resistance of cracks in bainite/martensitic crystallites.
  • the high alloy content of the steel plate not only leads to higher manufacturing cost of the steel plate, but also higher carbon equivalent Ceq and welding cold crack sensitivity index Pcm, which brings greater difficulty to the field welding, preheating before welding, welding After heat treatment, the welding cost increases, the welding efficiency decreases, and the welding work environment deteriorates.
  • a large number of patent documents only show how to achieve the strength and low temperature toughness of the base metal plate, improve the welding performance of the steel plate, and obtain excellent welding heat affected zone.
  • HAZ low temperature toughness description is less, and it does not involve how to ensure the hardenability of the central part of the quenched and tempered steel plate to ensure the strength and toughness of the steel plate and the strength and toughness uniformity along the thickness direction of the steel plate (Japanese Patent No. 63-93845, Sho 63- 79921, Pp. 60-258410, Japanese Patent Application Laid-Open No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. He
  • HAZ organization forming high-strength and high-toughness acicular ferrite structure
  • Sumitomo Metal Co., Ltd. uses technology to control B/N ⁇ 0.5, low silicon, ultra-low aluminum, medium N content, etc.
  • the problem of heat input weldability has achieved good results and has been successfully used in engineering performance ("Iron Steel", 1978, Vol.64, P2205). Summary of the invention
  • the object of the present invention is to provide an ultra-high toughness and excellent weldability HT550 steel plate and a manufacturing method thereof.
  • the microstructure of the finished steel plate is fine ferrite + self-tempered bainite, average grain size.
  • the steel plate can withstand large heat input welding, and is especially suitable for cross-sea bridge structures, ocean wind tower structures, offshore platform structures and hydropower structures, and can realize low-cost stable batch industrial production.
  • the invention adopts a component system of ultra-low C-high Mn-Nb microalloying-ultra-Ti treatment, and controls Mn/C between 15 and 30, (%Si)x(%Ceq) ⁇ 0.050, (% C)x(%Si) ⁇ 0.010, (%Mo)x[(%C) + 0.13 (%Si)] between 0.003 and 0.020, Ti/N between 2.0 and 4.0, (Cu + Ni + Mo) alloyed with Ni/Cu ⁇ 1.0, Ca treated and Ca/S ratio at 0.80 ⁇ Metallurgical techniques such as 3.00.
  • the ultrahigh toughness and excellent weldability HT550 steel sheet of the present invention has a weight percentage of components: C: 0.04% to 0.09%, Si: ⁇ 0.15%, Mn: 1.25% to 1.55%, P: ⁇ 0.013% , S: ⁇ 0.003%, Cu: 0.10% ⁇ 0.30%, Ni: 0.20% ⁇ 0.60%, Mo: 0.05% ⁇ 0.25%, Als: 0.030% ⁇ 0.060%, Ti: 0.006% ⁇ 0.014%, Nb: 0.015 % ⁇ 0.030%, N: ⁇ 0.0050%, Ca: 0.001% ⁇ 0.004%, the rest are Fe and unavoidable inclusions; and the above element content must satisfy the following relationship at the same time:
  • (%Si)x(%C) ⁇ 0.010 increase the critical cooling rate of bainite transformation, reduce the temperature range of mid-temperature phase transition, promote the formation of pro-eutectoid ferrite, increase the austenite hardenability of untransformed Promote the formation of lower bainite, ensure that the microstructure of the steel plate after TMCP is ferrite + self-tempered bainite, to ensure the super-temperature impact toughness of the steel plate; secondly, suppress the precipitation of MA island in the HAZ of large heat input welding, improve the weldability and Welding HAZ ultra low temperature toughness.
  • (%Mo)x[(%C) + 0.13(%Si)] is between 0.003 and 0.020, which guarantees the reduction of the strength reduction caused by the reduction of C and Si content by adding Mo element, through the C-Si-Mo element
  • the matching design balances the strength, plasticity, weldability and ultra-low temperature toughness of the steel plate to ensure that the steel plate has excellent ultra-low temperature toughness and weldability. At the same time, the strength and plasticity of the steel plate reach the development goal, and the subsequent process window is large, and the field is easy to realize.
  • Ti/N is between 2.0 and 4.0, ensuring uniform and fine TiN particles, strong anti-Oswald ripening ability, ensuring uniform austenite grains during slab heating and rolling, and inhibiting the length of welded HAZ grains. Large, improving the temperature toughness of HAZ for large heat input welding.
  • the relationship between Ca and S: Ca/S is between 0.80 and 3.0, which ensures the spheroidization of sulfide in steel, prevents the occurrence of hot cracks in the process of large heat input welding, and improves the heat input weldability of the steel plate.
  • C has a great influence on the strength, low temperature toughness, elongation and weldability of TMCP steel. From the viewpoint of improving the low temperature toughness and weldability of TMCP steel, it is hoped that the C content in the steel is controlled to be low; but the hardenability and strength of the steel sheet steel are strong. Toughness, strong plasticity matching, ultra-low temperature toughness and microstructure control and manufacturing cost in the manufacturing process, C content should not be controlled too low, too low C content easily lead to excessive grain boundary mobility, base metal plate and welding HAZ The grain size is coarse, which seriously degrades the low temperature toughness of the base metal plate and the welded HAZ. The reasonable range of the C content is 0.04% ⁇ 0.09%.
  • Si promotes the deoxidation of molten steel and can increase the strength of the steel sheet.
  • the deoxidizing effect of Si is not large when using A1 deoxidized molten steel.
  • Si can improve the strength of the steel sheet, Si seriously damages the ultra-low temperature toughness, elongation and weldability of the steel sheet, especially in comparison.
  • Si Under the condition of large heat input welding, Si not only promotes the formation of MA island, but also the size of the formed MA island is coarse, the number is increased and the distribution is uneven, which seriously damages the toughness of the weld heat affected zone (HAZ). Therefore, the Si content in the steel should be exhausted.
  • the control may be low, and the Si content is controlled to be less than 0.15% in consideration of the economy and operability of the steel making process.
  • Mn as the most important alloying element in addition to increasing the strength of the steel sheet, but also having an austenite phase area enlarged, reduced A, Ar 3 point temperature, the microstructure of the steel sheet thinning TMCP steel sheet to improve the low temperature toughness of the steel acts to promote The formation of low temperature phase transformation structure increases the strength of the steel sheet; however, Mn is prone to segregation during solidification of molten steel. Especially when the content of Mn is high, it not only causes difficulty in casting operation, but also is easily conjugated with elements such as C, P and S.
  • the Mn content is suitable for 1.25% to 1.55%.
  • P as a harmful inclusion in steel has great damage to the mechanical properties of steel, especially ultra-low temperature impact toughness, elongation, weldability (especially large heat input weldability) and weld joint performance.
  • the theoretical requirement is as low as possible;
  • the P content needs to be controlled at ⁇ 0.013%.
  • S as a harmful inclusion in steel has a great damage to the low temperature toughness of steel, more importantly S in steel
  • MnS inclusions are formed.
  • the plasticity of MnS causes MnS to extend along the rolling direction, forming a band of inclusions along the MnS, which seriously damages the low temperature impact toughness, elongation, Z-direction performance of the steel sheet.
  • Weldability and weld joint performance, and S is also the main element of hot brittleness during hot rolling.
  • the theoretical requirement is as low as possible; but considering the operability of steel making, steelmaking cost and smooth flow principle, it is required for excellent welding. Properties, - 60 ° C toughness and excellent toughness / strong plasticity matching TMCP steel, S content needs to be controlled at ⁇ 0.003%.
  • Cu is also an austenite stabilizing element. Adding Cu can also lower the temperature of ⁇ ⁇ and Ar 3 points, improve the hardenability of the steel sheet and the atmospheric corrosion resistance of the steel sheet, refine the microstructure of the TMCP steel sheet, and improve the ultra-low temperature toughness of the TMCP steel sheet.
  • the amount of Cu added is too high, higher than 0.30%, which is liable to cause copper brittleness, cracking of the surface of the slab, internal cracking and deterioration of the performance of the welded joint of the thick steel plate; the amount of Cu added is too small, less than 0.10%, and any effect is exerted.
  • the Cu content is controlled between 0.10% and 0.30%;
  • Cu, Ni composite addition in addition to reducing the copper brittleness of copper-containing steel, reducing the effect of intergranular cracking during hot rolling, more importantly, Cu, Ni Both are austenite stabilizing elements.
  • Cu and Ni composite addition can greatly reduce the temperature of ⁇ ⁇ and Ar 3 points and increase the driving force of austenite to ferrite transformation, resulting in austenite occurring at lower temperatures.
  • the phase transformation greatly refines the microstructure of the TMCP steel plate, increases the orientation angle between the bainite laths, increases the expansion resistance of the crack in the bainite crystal cluster, and greatly improves the ultra-low temperature toughness of the TMCP steel sheet.
  • Ni not only improves the dislocation mobility in the ferrite phase, promotes the dislocation slip, and improves the intrinsic plastic toughness of ferrite grains and bainite laths; in addition, Ni acts as a strong austenite.
  • Chemical element greatly reduce the temperature of Arj, Ar 3 point, improve the driving force of austenite to ferrite transformation, lead to phase transformation of austenite at lower temperature, and greatly refine the microstructure of TMCP steel plate
  • the structure increases the orientation angle between the bainite laths, increases the expansion resistance of the cracks in the bainite crystallites, and greatly improves the ultra-low temperature toughness of the TMCP steel sheet. Therefore, Ni has the same strength, elongation and low temperature of the TMCP steel sheet.
  • Ni is a very Valuable elements, from the performance price ratio, Ni content is controlled between 0.20% ⁇ 0.60%.
  • Mo can greatly improve the hardenability of the steel sheet and promote the formation of bainite during accelerated cooling.
  • Mo acts as a strong carbide forming element to promote the formation of bainite and increase the bainite crystal cluster.
  • the size and the formed bainite strips have a small difference in orientation, which reduces the resistance of the cracks to the bainite crystal clusters; therefore, Mo greatly improves the strength of the quenched and tempered steel sheets while reducing the low temperature toughness of the TMCP steel sheets.
  • Als in steel can fix the free [N] in the steel, reduce the free heat affected zone (HAZ) [N], and improve the low temperature toughness of the welded HAZ; therefore, the lower limit of Als is controlled at 0.030%; however, excessive Als is added to the steel. Not only will it cause casting difficulties, but also a large amount of dispersed needle-like ⁇ 1 2 ⁇ 3 inclusions will be formed in the steel, which will impair the internal quality of the steel sheet, low temperature toughness and high heat input weldability, so the upper limit of Als is controlled at 0.060%.
  • the Ti content is between 0.006% and 0.014%, which inhibits the excessive growth of austenite grains during slab heating and hot rolling, improves the low temperature toughness of the steel sheet, and more importantly inhibits the growth of HAZ grains during welding and improves HAZ. Toughness; Secondly, the affinity of Ti and N is much greater than the affinity of A1 and N. When Ti is added to steel, N preferentially combines with Ti to form dispersed TiN particles, which greatly reduces the heat affected zone (HAZ). N], improving the low temperature toughness of the welded HAZ.
  • the purpose of adding a small amount of Nb element in the steel is to control the rolling without recrystallization and improve the strength and toughness of the TMCP steel.
  • the Nb addition amount is less than 0.015%, the strengthening ability of the TMCP steel sheet is in addition to the control rolling effect which cannot be effectively exerted.
  • the amount of Nb added exceeds 0.030%, the upper bainite (Bu) formation and the Nb(C, N) secondary precipitation embrittlement are induced under the large heat input welding condition, which seriously damages the heat affected zone of the large heat input welding.
  • HAZ high temperature toughness
  • Ca treatment of steel can further purify the molten steel on the one hand, and denaturing the sulfide in the steel on the other hand, making it into a non-deformable, stable small spherical sulfide, suppressing the hot brittleness of S, and increasing the steel plate.
  • the amount of Ca added depends on the level of S in the steel, the amount of Ca added is too low, and the treatment effect is not large; the amount of Ca added is too high, and the Ca(O, S) size is too large, and the brittleness is also increased.
  • the starting point of the crack initiation reduces the low temperature toughness and elongation of the steel, while also reducing the purity of the steel and contaminating the molten steel.
  • the Ca content is suitably in the range of 0.0010% to 0.0040%.
  • the method for producing an ultrahigh toughness and excellent weldability HT550 steel sheet according to the present invention comprises the following steps:
  • the slab heating temperature is controlled between 1050 ° C ⁇ 1150 ° C;
  • the total compression ratio of the steel plate is the thickness of the slab / the thickness of the finished steel plate is ⁇ 4.0;
  • the first stage is the rough rolling deformation stage, which adopts the maximum rolling capacity of the rolling mill for uninterrupted rolling, and the control pass reduction rate is ⁇ 8%, the cumulative reduction rate is 50%, and the final rolling temperature is ⁇ 1000°;
  • the intermediate billet is cooled rapidly by forced water cooling to ensure that the intermediate billet is reduced to ⁇ 10min to the rolling temperature of the unrecrystallized controlled rolling, preventing the intermediate billet from appearing mixed crystals and ensuring the uniformity and fineness of the steel sheet. Obtained - 60 ° C ultra low temperature toughness;
  • the second stage adopts non-recrystallization control rolling, the rolling temperature is 780 °C ⁇ 840, the rolling pass reduction rate is ⁇ 7%, the cumulative reduction ratio is ⁇ 50%, and the finishing rolling temperature is 760 °C ⁇ 800 °C;
  • the steel plate After the controlled rolling, the steel plate is immediately transported to the accelerated cooling equipment to accelerate the cooling of the steel plate.
  • the cooling temperature of the steel plate is 690 ° C ⁇ 730 ° C
  • the cooling rate is ⁇ 61 ⁇
  • the cooling temperature is 350 ° C ⁇ 600 ° C.
  • the cold process is maintained for at least 24 hours under conditions where the steel sheet temperature surface is greater than 300 °C.
  • the slab heating temperature is controlled between 1050 ° C ⁇ 1150 ° C to ensure that Nb in the steel is completely dissolved in the austenite during the heating process of the slab. At the same time, the slab austenite grains do not grow abnormally;
  • the total compression ratio of the steel plate (slab thickness / finished steel plate thickness) ⁇ 4.0, to ensure that the rolling deformation penetrates into the core of the steel plate, improving the structure and performance of the central part of the steel plate;
  • the first stage is the rough rolling deformation stage, which uses the maximum rolling capacity of the rolling mill for uninterrupted rolling.
  • the control pass reduction rate is ⁇ 8%
  • the cumulative reduction ratio is 50%
  • the final rolling temperature is ⁇ 1000, ensuring the dynamics of the deformed metal. / static recrystallization, refining the austenite grains of the intermediate billet;
  • the intermediate billet is cooled rapidly by forced water cooling to ensure that the intermediate billet is reduced to ⁇ 10 min to the rolling temperature of the unrecrystallized controlled rolling.
  • the second stage adopts non-recrystallization control rolling.
  • the controlled rolling and rolling temperature is controlled at 780 ° C ⁇ 840 ° C, rolling pass pressure Rate ⁇ 7%, cumulative The reduction ratio is ⁇ 50%, and the finishing temperature is 760 °C ⁇ 800 °C;
  • the steel plate is oscillated and cooled on the roller table, and cooled to the cold-opening temperature of the steel plate.
  • the cold-opening temperature of the steel plate is 690 ° C ⁇ 730 ° C
  • the cooling rate is ⁇ 61 ⁇
  • the cooling temperature is 350 ° C ⁇ 600 ° C.
  • the slow cooling process is maintained for at least 24 hours under the condition that the steel plate temperature surface is greater than 300 ° C. Therefore, the steel plate is cooled in the ferritic + austenitic two-phase region to ensure that the final microstructure of the steel plate is fine ferrite + self-tempered bainite, and the yield ratio of the steel plate is ⁇ 0.85.
  • the invention combines the design of simple components and combines with the TMCP manufacturing process to not only produce TMCP steel sheets with excellent comprehensive performance at low cost, but also greatly shortens the manufacturing cycle of the steel sheets, creating great value for the enterprise and realizing manufacturing.
  • the process is green.
  • the high-performance and high added value of the steel plate is concentrated in the steel sheet with excellent toughness and strong plasticity matching.
  • the weldability of the steel sheet (especially the heat input weldability) and the ultra-low temperature toughness are also excellent, eliminating the local brittle zone of the welded joint.
  • Fig. 1 shows the microstructure (1/4 thickness) of the steel 3 of the embodiment of the invention.
  • composition of the steel of the embodiment of the present invention is shown in Table 1.
  • Table 2 For the manufacturing process of the steel of the embodiment, see Table 2, Table 3, and Table 4 are the properties of the steel of the embodiment of the present invention.
  • the final microstructure of the steel sheet of the present invention is fine ferrite + self-tempered bainite, and the average grain size is 15 ⁇ or less.
  • the steel sheet of the invention is designed by a simple component combination and combined with the TMCP manufacturing process to produce a TMCP steel sheet with excellent comprehensive performance at a low cost, and greatly shortens the manufacturing cycle of the steel sheet, thereby creating enormous value for the enterprise and realizing the realization.
  • the greenness of the manufacturing process High-performance, high value-added concentration table for steel plates
  • the steel plate has excellent toughness and strong plasticity matching, and the weldability (especially large heat input weldability) and ultra-low temperature toughness of the steel plate are also excellent, eliminating the local brittle zone of the welded joint, and successfully solved the problem.
  • the steel plate of the invention is mainly used as a key material for a sea-crossing bridge structure, an ocean wind tower structure, an offshore platform structure and a hydroelectric structure.
  • the steel plates produced by major domestic steel mills (except Baosteel) cannot fully meet the requirements of ultra-low temperature toughness, especially the thickness exceeds 80 mm.
  • the ultra-low temperature toughness of the center of the extra-thick steel plate is not guaranteed at -50 °C.
  • the area of the brittle area of the welded joint is large, and the requirements for on-site welding process and welding construction management are very high.
  • the steel construction period cannot meet the requirements of the project schedule. Forcing users to order a certain number of steel plates in advance, carry out a full set of welding process evaluation and field welding process adaptability test, resulting in longer steel manufacturing cycle and high manufacturing costs.

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Abstract

超高韧性、优良焊接性HT550钢板及其制造方法，采用超低C－高Mn－Nb微合金化－超微Ti处理的成分体系作为基础，控制Mn/C在15～30、 (%Si)×(%Ceq)≤0.050、(%C)×(%Si)≤0.010、(%Mo)×[(%C)＋0.13(%Si)]在0.003～ 0.020、Ti/N=2.0～4.0、(Cu＋Ni＋Mo)合金化，Ni/Cu≥1.0、Ca处理，Ca/S比在0.80～ 3.00，通过优化TMCP工艺，使钢板显微组织为细小铁素体+自回火贝氏体，平均晶粒尺寸15μm以下，屈服强度≥460MPa、抗拉强度550MPa～700MPa、屈强比≤0.85、－60℃的Charpy冲击功（单个值）≥60J；在获得均匀优良的强韧性、强塑性匹配的同时，钢板可承受大热输入焊接，特别适用于跨海桥梁结构、海洋风塔结构、海洋平台结构及水电结构。

Description

超高韧性、 优良焊接性 HT550钢板及其制造方法 技术领域
本发明涉及一种超高韧性、优良焊接性 HT550钢板及其制造方法，通过 TMCP 工艺获得屈服强度≥460MPa、 抗拉强度 550MPa ~ 700MPa之间、 屈强比≤0.85、 - 60°C的 Charpy冲击功 (单个值)≥60J、 优良焊接性的钢板， 钢板的显微组织为细小铁 素体 +自回火贝氏体， 平均晶粒尺寸在 15μηι以下。 背景技术
众所周知， 低碳 (高强度)低合金钢是最重要工程结构材料之一， 广泛应用于石 油天然气管线、 海洋平台、 造船、 桥梁结构、 锅炉容器、 建筑结构、 汽车工业、 铁 路运输及机械制造之中。
低碳 (高强度)低合金钢性能取决于其化学成分、 制造过程的工艺制度， 其中强 度、 塑性、 韧性和焊接性是低碳 (高强度)低合金钢最重要的性能， 它最终决定于成 品钢材的显微组织状态。 随着科技不断地向前发展， 人们对高强钢的强韧性、 强塑 性匹配提出更高的要求， 即在维持较低的制造成本的同时， 大幅度地提高钢板的综 合机械性能和使用性能， 以减少钢材的用量节约成本， 减轻钢结构的自身重量、 稳 定性和安全性， 更为重要的是为进一步提高钢结构安全稳定性、 耐久性及冷热加工 性， 适应不同施工环境、 不同加工工艺的要求。
目前， 日韩、 欧盟掀起了发展新一代高性能钢铁材料的研究高潮， 力图通过合 金组合设优化计和革新制造工艺技术获得更好的组织匹配，使高强钢获得更优良的 强韧性、 强塑性匹配。
传统的抗拉强度强度大于 590MPa的厚钢板主要通过再加热淬火 +回火 (RQ+T) 工艺， 即所谓离线调质方法来生产， 这就要求钢板中心部位必须具有足够高的淬透 性，即淬透性指数 DI≥1.0x钢板厚度，其中 DI = 0.311C1/2(1 + 0.64Si)x(l + 4.10Μη)χ(1 + 0.27Cu)x(l + 0.52Ni)x(l + 2.33Cr)x(l + 3.14Mo) 25.4(mm), 以确保钢板具有足够 高的强度、 优良的超低温韧性及沿钢板厚度方向的显微组织与性能的均匀， 因此不 可避免地向钢中加入一定数量的 Cr、 Mo、 Ni、 Cu等合金元素 （日本专利昭 59 - 129724、 平 1 - 219121 ) , 因为 Ni元素不但能够提高钢板的强度和淬透性， 降低相 变温度细化贝氏体 /马氏体板条团晶粒尺寸； 更重要的是 Ni唯一能够改善贝氏体 / 马氏体板条本征低温韧性的元素， 增大贝氏体 /马氏体板条之间的位向角， 增加裂 紋在贝氏体 /马氏体晶团中的扩展阻力。 如此， 钢板的合金含量较高， 不仅导致钢 板制造成本较高， 而且碳当量 Ceq、 焊接冷裂紋敏感指数 Pcm也较高， 这给现场焊 接带来较大的困难， 焊前需要预热， 焊后需要热处理， 焊接成本升高、 焊接效率降 低、 焊接现场工作环境恶化； 现有大量专利文献只是说明如何实现母材钢板的强度 和低温韧性， 就改善钢板焊接能性， 获得优良焊接热影响区 HAZ低温韧性说明较 少， 更没有涉及如何确保调质钢板中心部位淬透性， 以保证钢板强度、 韧性及沿钢 板厚度方向强度、 韧性均匀性（日本专利昭 63 - 93845、 昭 63 - 79921、 昭 60 - 258410、 特平开 4 - 285119、 特平开 4 - 308035、 平 3 - 264614、 平 2 - 250917、 平 4 - 143246、 US Patent4855106、 US Patent5183198、 US Patent4137104 ) 。
目前改善超大热输入焊接钢板热影响区（HAZ)低温韧性的只有日本新日铁公 司采用氧化物冶金技术（美国专利 US Patent 4629505、 WO 01/59167 Al ) , 即在大 热输入焊接过程中， 在熔合线附近， 由于强烈的高温作用， TiN粒子发生溶解而失 去作用， Ti2O3比 TiN更加稳定， 即使到达钢的熔点， 也不会发生溶解。 Ti2O3粒子 可成为奥氏体晶内针状铁素体形核位置，促进奥氏体晶内针状铁素体 (acicular ferrite - AF)形核， 有效地分割奥氏体晶粒， 细化 HAZ组织， 形成高强高韧性的针状铁素 体组织； 日本住友金属采用添加^ 控制 B/N≥0.5、 低硅、 超低铝、 中等含 N量等 技术手段， 解决 60公斤级钢板大热输入焊接性的问题， 取得良好的效果并成功用 于工程实绩 （ 《铁 ά钢》 ， 1978, Vol.64, P2205 ) 。 发明内容
本发明的目的在于提供一种超高韧性、 优良焊接性 HT550钢板及其制造方法， 通过优化 TMCP工艺， 使成品钢板的显微组织为细小铁素体 +自回火贝氏体， 平均 晶粒尺寸在 15μηι以下， 屈服强度≥460MPa、 抗拉强度 550MPa ~ 700MPa之间、 屈 强比≤0.85、 - 60°C的 Charpy冲击功 (单个值)≥60J; 在获得均匀优良的强韧性、 强 塑性匹配的同时， 钢板可以承受大热输入焊接， 特别适用于跨海桥梁结构、 海洋风 塔结构、 海洋平台结构及水电结构， 并且能够实现低成本稳定批量工业化生产。
为达到上述目的， 本发明的技术方案是：
本发明采用超低 C -高 Mn - Nb微合金化 -超微 Ti处理的成分体系作为基础， 控制 Mn/C在 15 ~ 30之间、（％Si)x(%Ceq)≤0.050、（％C)x(%Si)≤0.010、 (%Mo)x[(%C) + 0.13(%Si)]在 0.003 ~ 0.020之间、 Ti/N在 2.0 ~ 4.0之间、 （Cu + Ni + Mo)合金化且 Ni/Cu≥1.0、 Ca处理且 Ca/S比在 0.80 ~ 3.00之间等冶金技术手段。
具体的， 本发明的超高韧性、 优良焊接性 HT550钢板， 其成分的重量百分比 为： C: 0.04% ~ 0.09%、 Si: ≤0.15%、 Mn: 1.25% ~ 1.55%, P: ≤0.013%、 S: ≤0.003%、 Cu: 0.10% ~ 0.30%、 Ni: 0.20% ~ 0.60%、 Mo: 0.05% ~ 0.25%、 Als: 0.030% ~ 0.060%、 Ti: 0.006% ~ 0.014%、 Nb: 0.015% ~ 0.030%, N: ≤0.0050%、 Ca: 0.001% ~ 0.004%、 其余为 Fe和不可避免的夹杂； 且上述元素含量必须同时满足如下关系：
C、 Mn之间的关系： 15≤Mn/C≤30, 确保钢板在 -60 °C条件下钢板处于韧性断裂 区， 即夏比冲击试样断口剪切面积≥50%,保证钢板具有优良的超低温韧性， - 60。C 的 Charpy冲击功 (单个值)≥60 J。
(%Si)x(%Ceq)<0.050,其中 Ceq = C + Mn/6 + (Cu + Ni)/15 + (Cr + Mo + V)/5 ,保 证钢板具有优良的焊接性， 抑制大热输入焊接性 HAZ内 M-A岛形成， 改善大热输 入焊接性 HAZ超低温韧性， 消除焊接接头局部脆性区， 改善钢结构安全可靠性。
(%Si)x(%C)<0.010, 增加贝氏体相变临界冷却速度， 减少中温相变温度区间， 促进先共析铁素体形成， 增加未相变的奥氏体淬透性而促进下贝氏体形成， 确保 TMCP后钢板显微组织为铁素体 +自回火贝氏体， 保证钢板超氐温冲击韧性; 其次 抑制大热输入焊接 HAZ中 M-A岛析出， 改善焊接性及焊接 HAZ超低温韧性。
上述两点保证了本发明钢板优良焊接性。
通过 TMCP工艺获得屈服强度≥460MPa、 抗拉强度 550MPa ~ 700MPa之间、 屈强比≤0.85、 - 60°C的 Charpy冲击功 (单个值)≥60J、 优良焊接性的钢板， 钢板的 显微组织为细小铁素体 +自回火贝氏体， 平均晶粒尺寸在 15μηι以下。
(%Mo)x[(%C) + 0.13(%Si)]在 0.003 ~ 0.020之间， 保证通过添加 Mo元素来抵 消降低 C、 Si含量造成的强度降低， 通过 C-Si-Mo元素之间的匹配设计， 平衡钢板 强度、 塑性、 焊接性及超低温韧性， 确保钢板具有优良的超低温韧性、 焊接性的同 时， 钢板强度、 塑性达到开发目标， 且后续工艺窗口较大， 现场实现容易。
Ti/N在 2.0 ~ 4.0之间， 保证形成的 TiN粒子均匀细小， 抗奥斯瓦尔德熟化能 力强， 保证板坯加热轧制过程中奥氏体晶粒均匀细小， 且抑制焊接 HAZ晶粒长大， 改善大热输入焊接 HAZ的氏温韧性。
Cu与 Ni之间的关系： Ni/Cu≥1.0,降低 TMCP钢板 Ar3、 A 点温度，细化 TMCP 钢板显微组织， 保证钢板母材低温韧性优良的同时， 防止板坯产生铜脆。 Ca与 S之间的关系： Ca/S在 0.80 ~ 3.0之间， 保证钢中硫化物球化， 防止大热 输入焊接过程中热裂紋产生的同时， 改善钢板大热输入焊接性。
在本发明成分设计中：
C对 TMCP钢板的强度、 低温韧性、 延伸率及焊接性影响很大， 从改善 TMCP 钢板低温韧性和焊接性角度，希望钢中 C含量控制得较低；但是从钢板钢的淬透性、 强韧性、 强塑性匹配、 超低温韧性及生产制造过程中显微组织控制与制造成本的角 度， C含量不宜控制得过低， 过低 C含量易导致晶界迁移率过高， 母材钢板与焊接 HAZ晶粒粗大， 严重劣化母材钢板与焊接 HAZ的低温韧性； 因次 C含量合理范围 为 0.04% ~ 0.09%„
Si促进钢水脱氧并能够提高钢板强度， 但是采用 A1脱氧的钢水， Si的脱氧作 用不大， Si虽然能够提高钢板的强度， 但是 Si严重损害钢板的超低温韧性、 延伸 率及焊接性， 尤其在较大热输入焊接条件下， Si不仅促进 M-A岛形成， 而且形成 的 M-A 岛尺寸较为粗大、 数量增多且分布不均匀， 严重损害焊接热影响区 (HAZ) 的韧性， 因此钢中的 Si含量应尽可能控制得低， 考虑到炼钢过程的经济性和可操 作性， Si含量控制在 0.15%以下。
Mn作为最重要的合金元素在钢中除提高钢板的强度外， 还具有扩大奥氏体相 区、 降低 A 、 Ar3点温度、 细化 TMCP钢板显微组织而改善钢板低温韧性的作用、 促进低温相变组织形成而提高钢板强度的作用； 但是 Mn在钢水凝固过程中容易发 生偏析， 尤其 Mn含量较高时， 不仅会造成浇铸操作困难， 而且容易与 C、 P、 S等 元素发生共轭偏析现象， 尤其钢中 C含量较高时， 加重铸坯中心部位的偏析、 疏松 及氧硫夹杂物的富集， 严重的铸坯中心区域偏析在后续的轧制、 焊接过程中易形成 异常组织， 导致钢板低温韧性低下和焊接接头出现裂紋； 因此根据 C含量范围， 选 择适宜的 Mn含量范围对于 TMCP钢板极其重要， 根据本发明钢成分体系及 C含 量，适合 Mn含量为 1.25% ~ 1.55%,且 C含量高时， Mn含量适当降低；反之亦然， 即 C含量低时， Mn含量适当提高。
P作为钢中有害夹杂对钢的机械性能， 尤其超低温冲击韧性、 延伸率、 焊接性 (尤其大热输入焊接性)及焊接接头性能具有巨大的损害作用，理论上要求越低越好； 但考虑到炼钢可操作性和炼钢成本， 对于要求可大热输入焊接、 - 60°C韧性及优良 强韧性 /强塑性匹配的 TMCP钢板， P含量需要控制在≤0.013%。
S作为钢中有害夹杂对钢的低温韧性具有很大的损害作用， 更重要的是 S在钢 中与 Mn结合， 形成 MnS夹杂物， 在热轧过程中， MnS的可塑性使 MnS沿轧向延 伸， 形成沿轧向 MnS 夹杂物带， 严重损害钢板的低温冲击韧性、 延伸率、 Z向性 能、 焊接性及焊接接头性能， 同时 S还是热轧过程中产生热脆性的主要元素， 理论 上要求越低越好； 但考虑到炼钢可操作性、 炼钢成本和物流顺畅原则， 对于要求优 良焊接性、 - 60°C韧性及优良强韧性 /强塑性匹配的 TMCP钢板， S含量需要控制 在≤0.003%。
Cu也是奥氏体稳定化元素， 添加 Cu也可以降低 ΑΓι、 Ar3点温度， 提高钢板 的淬透性和钢板的耐大气腐蚀性， 细化 TMCP钢板显微组织， 改善 TMCP钢板超 低温韧性； 但是 Cu添加量过多， 高于 0.30%, 容易造成铜脆、 铸坯表面龟裂、 内 裂问题及尤其厚钢板焊接接头性能劣化； Cu添加量过少， 低于 0.10%, 所起任何作 用很小； 因此 Cu含量控制在 0.10% ~ 0.30%之间； Cu、 Ni复合添加除降低含铜钢 的铜脆现象、 减轻热轧过程的晶间开裂之作用外， 更重要的是 Cu、 Ni均为奥氏体 稳定化元素， Cu、 Ni复合添加可以大幅度降低 ΑΓι、 Ar3点温度， 提高奥氏体向铁 素体相变的驱动力， 导致奥氏体在更低温度下发生相变， 大幅度细化细化 TMCP 钢板显微组织， 增大贝氏体板条之间的位向角， 提高裂紋在贝氏体晶团中的扩展阻 力， 大幅度提高 TMCP钢板超低温韧性。
添加 Ni不仅可以提高铁素体相中位错可动性， 促进位错交滑移， 改善铁素体 晶粒和贝氏体板条的本征塑韧性； 此外， Ni作为强奥氏体稳定化元素， 大幅度降低 Arj, Ar3点温度， 提高奥氏体向铁素体相变的驱动力， 导致奥氏体在更低温度下发 生相变， 大幅度细化细化 TMCP钢板显微组织， 增大贝氏体板条之间的位向角， 提 高裂紋在贝氏体晶团中的扩展阻力， 大幅度提高 TMCP钢板超低温韧性， 因此 Ni 具有同时提高 TMCP钢板强度、 延伸率和低温韧性的功能； 钢中加 Ni还可以降低 含铜钢的铜脆现象， 减轻热轧过程的晶间开裂， 提高钢板的耐大气腐蚀性。 因此从 理论上讲， 钢中 Ni含量在一定范围内越高越好， 但是过高的 Ni含量会硬化焊接热 影响区， 对钢板的焊接性及焊接接头 SR性能不利； 同时 Ni是一种很贵重元素， 从 性能价格比考虑， Ni含量控制在 0.20% ~ 0.60%之间。
添加 Mo可以大幅度地提高钢板的淬透性，在加速冷却过程中促进贝氏体形成， 但是 Mo作为强碳化物形成元素， 在促进贝氏体形成的同时， 增大贝氏体晶团的尺 寸且形成的贝氏体板条间位向差很小， 减小裂紋穿过贝氏体晶团的阻力； 因此 Mo 在大幅度提高调质钢板强度的同时， 降低了 TMCP钢板的低温韧性和延伸率； 并且 当 Mo添加过多时，不仅严重损害钢板的延伸率、大热输入焊接性及焊接接头性能， 而且增加钢板的生产成本；但是通过添加 Mo元素，降低 C含量来平衡钢板强韧性、 强塑性匹配， 改善钢板超低温韧性、 焊接性非常有效； 因此， 综合考虑 Mo的相变 强化作用、 对母材钢板低温韧性、 延伸率和焊接性的影响及成本因素， Mo含量控 制在 0.05% ~ 0.25%之间。
钢中的 Als能够固定钢中的自由 [N] , 降低焊接热影响区 (HAZ)自由 [N] , 改善 焊接 HAZ的低温韧性作用； 因此 Als下限控制在 0.030%;但是钢中加入过量的 Als 不但会造成浇铸困难， 而且会在钢中形成大量弥散的针状 Α12Ο3夹杂物， 损害钢板 内质健全性、 低温韧性和大热输入焊接性， 因此 Als上限控制在 0.060%。
Ti含量在 0.006% ~ 0.014%之间， 抑制板坯加热和热轧过程中奥氏体晶粒过分 长大， 改善钢板低温韧性， 更重要的是抑制焊接过程中 HAZ晶粒长大， 改善 HAZ 韧性； 其次， Ti与 N亲合力远大于 A1与 N的亲合力， 当钢中添加 Ti时， N优先 与 Ti结合， 生成弥散分布的 TiN粒子， 大幅度降低焊接热影响区 (HAZ)自由 [N], 改善焊接 HAZ的低温韧性。
钢中添加微量的 Nb元素目的是进行未再结晶控制轧制、提高 TMCP钢板强度 和韧性， 当 Nb添加量低于 0.015%时， 除不能有效发挥的控轧作用之外， 对 TMCP 钢板强化能力也不足； 当 Nb添加量超过 0.030%时， 大热输入焊接条件下诱发上贝 氏体 (Bu)形成和 Nb(C, N)二次析出脆化作用，严重损害大热输入焊接热影响区 (HAZ) 的低温韧性， 因此 Nb含量控制在 0.015% ~ 0.030%之间， 获得最佳的控轧效果、 实 现 TMCP钢板强韧性 /强塑性匹配的同时， 又不损害大热输入焊接 HAZ的韧性。
钢中的 N含量控制难度较大， 为了确保钢板中固溶 [B]的存在及防止大量 A1N 沿原奥氏体晶界析出， 损害钢板的冲击韧性， 钢中的 N含量不得超过 0.005%。
对钢进行 Ca处理， 一方面可以进一步純洁钢液， 另一方面对钢中硫化物进行 变性处理， 使之变成不可变形的、 稳定细小的球状硫化物、 抑制 S的热脆性、 提高 钢板的低温韧性、 延伸率及 Z向性能、 改善钢板韧性的各向异性。 Ca加入量的多 少， 取决于钢中 S含量的高低， Ca加入量过低， 处理效果不大； Ca加入量过高， 形成 Ca(O, S)尺寸过大， 脆性也增大， 可成为断裂裂紋起始点， 降低钢的低温韧 性和延伸率， 同时还降低钢质純净度、 污染钢液。 一般控制 Ca含量按 ESSP = (wt%Ca)[ 1- 1.24(wt%O)]/l .25(wt%S), 其中 ESSP为硫化物夹杂形状控制指数， 取值 范围 0.5 ~ 5之间为宜， 因此 Ca含量的合适范围为 0.0010% ~ 0.0040%。 本发明的超高韧性、 优良焊接性 HT550钢板的制造方法， 包括如下步骤：
1) 冶炼、 铸造
按上述成分冶炼、 铸造成板坯；
2) 加热
板坯加热温度控制在 1050°C ~ 1150°C之间；
3) 控制轧制， 钢板总压缩比即板坯厚度 /成品钢板厚度≥4.0；
第一阶段为粗轧变形阶段， 采用轧机最大轧制能力进行不间断地轧制， 控制道次压下率≥8%、 累计压下率 50%、 终轧温度≥1000°〇；
粗轧结束后中间坯采用强制水冷快速降温， 保证中间坯在≤10min内降 低至采用未再结晶控制轧制的开轧温度， 防止中间坯出现混晶， 保证钢板 的显微组织均匀细小， 以获得 - 60°C超低温韧性；
第二阶段采用未再结晶控制轧制， 开轧温度 780°C ~ 840 , 轧制道次 压下率≥7%, 累计压下率≥50%, 终轧温度 760°C ~ 800°C ;
4) 控制冷却
控轧结束后， 钢板立即运送到加速冷却设备处对钢板进行加速冷却， 钢板 开冷温度 690°C ~ 730°C冷却速度≥61^, 停冷温度为 350°C ~ 600°C , 随后 緩冷工艺为钢板温度表面大于 300°C的条件下至少保温 24小时。
在本发明制造方法中：
根据上述 C、 Mn、 Nb、 N及 Ti含量范围，板坯加热温度控制在 1050°C ~ 1150°C 之间， 确保钢中 Nb在板坯加热过程中全部固溶到奥氏体中去的同时， 板坯奥氏体 晶粒不发生反常长大；
钢板总压缩比 (板坯厚度 /成品钢板厚度)≥4.0, 保证轧制形变穿透到钢板芯部， 改善钢板中心部位显啟组织与性能；
第一阶段为粗轧变形阶段， 采用轧机最大轧制能力进行不间断地轧制， 控制道 次压下率≥8%、 累计压下率 50%、 终轧温度≥1000 ， 确保形变金属发生动态 /静态 再结晶， 细化中间坯奥氏体晶粒；
粗轧结束后中间坯采用强制水冷快速降温， 保证中间坯在≤10min 内降低至采 用未再结晶控制轧制的开轧温度。
第二阶段采用未再结晶控制轧制， 根据上述钢中 Nb元素含量范围， 为确保未 再结晶控轧效果， 控轧开轧温度控制在 780°C ~ 840°C , 轧制道次压下率≥7%, 累计 压下率≥50%, 终轧温度 760 °C ~ 800 °C ;
控轧结束后， 钢板在辊道上摆动冷却， 冷却至钢板开冷温度， 钢板开冷温度 690°C ~ 730°C , 冷却速度≥61^, 停冷温度为 350°C ~ 600°C , 随后緩冷工艺为钢板 温度表面大于 300°C的条件下至少保温 24小时。 从而保证钢板处于铁素体 +奥氏体 两相区开始冷却， 确保钢板的最终显微组织为细小铁素体 +自回火贝氏体， 实现钢 板的屈强比 < 0.85。
本发明的有益效果：
本发明通过简单成分组合设计， 并与 TMCP 制造工艺相结合， 不仅低成本地 生产出综合性能优良的 TMCP钢板， 而且大幅度地缩短了钢板的制造周期，为企业 创造巨大的价值， 实现了制造过程的绿色环保。 钢板的高性能高附加值集中表现在 钢板具有优异的强韧性、强塑性匹配的同时，钢板的焊接性 (尤其大热输入焊接性)、 超低温韧性也同样优异， 消除了焊接接头的局部脆性区， 并成功地解决了 TMCP 钢板沿钢板厚度方向性能不均句的问题， 极大地提高了大型重钢结构的安全稳定 性、 抗疲劳性能； 良好的焊接性节省了用户钢构件制造的成本， 缩短了用户钢构件 制造的时间， 为用户创造了巨大的价值， 因而此类钢板不仅是高附加值、 绿色环保 性的产品， 更重要的是形成了具有宝钢特色的高技术、 高附加值 TMCP厚板核心制 造技术， 提升了宝钢的品牌形象和核心竟争力。 附图说明
图 1本发明实施例钢 3的显微组织（1/4厚度)。 具体实施方式
下面结合实施例和附图对本发明做进一步说明。
本发明实施例钢的成分参见表 1 , 实施例钢的制造工艺参见表 2、 表 3 , 表 4 为本发明实施例钢的性能。
如图 1所示， 本发明钢板的最终显微组织为细小铁素体 +自回火贝氏体， 平均 晶粒尺寸在 15μηι以下。
本发明钢板通过简单成分组合设计， 并与 TMCP 制造工艺相结合， 不仅低成 本地生产出综合性能优良的 TMCP钢板， 而且大幅度地缩短了钢板的制造周期， 为 企业创造巨大的价值， 实现了制造过程的绿色环保。 钢板的高性能高附加值集中表 现在钢板具有优异的强韧性、 强塑性匹配的同时， 钢板的焊接性 (尤其大热输入焊 接性)、 超低温韧性也同样优异， 消除了焊接接头的局部脆性区， 并成功地解决了
TMCP钢板沿钢板厚度方向性能不均匀的问题，极大地提高了大型重钢结构的安全 稳定性、 抗疲劳性能； 良好的焊接性节省了用户钢构件制造的成本， 缩短了用户钢 构件制造的时间， 为用户创造了巨大的价值， 因而此类钢板不仅是高附加值、 绿色 环保性的产品。
本发明钢板主要用作跨海桥梁结构、 海洋风塔结构、 海洋平台结构及水电结构 关键材料， 目前国内各大钢厂（除宝钢以外)生产的钢板不能完全满足超低温韧性要 求， 尤其厚度超过 80mm的特厚钢板中心部位 -50°C超低温韧性无法保证， 焊接接 头局部脆性区面积较大， 对现场焊接工艺及焊接施工管理要求很高， 钢结构制作工 期也无法满足工程进度多变之要求， 迫使用户提前订购一定数量的钢板， 进行全套 焊接工艺评定与现场焊接工艺适应性试验， 导致钢结构制造周期加长、 制造成本居 高不下。
随着我国国民经济发展， 建设节约型和谐社会的要求， 基础工程建设、 清洁能 源开发已摆到日事议程， 目前我国基础工程建设、 清洁能源建设方兴未艾， 基础工 程建设、 清洁能源的关键材料——超高韧性、 优良焊接性 HT550用 TMCP钢板具 有广阔的市场前景。
表 1 单位： 重量百分比
Figure imgf000012_0001
Figure imgf000012_0002
表 3
Figure imgf000013_0001
表 4
Figure imgf000013_0002

Claims

权 利 要 求 书
1. 超高韧性、 优良焊接性 HT550钢板， 其成分的重量百分比为：
C: 0.04% - 0.09%
Si: <0.15%
Mn: 1.25% ~ 1.55%
P: <0.013%
S: <0.003%
Cu: 0.10% ~ 0.30%
Ni: 0.20% - 0.60%
Mo: 0.05% - 0.25%
Als: 0.030% - 0.060%
Ti: 0.006% ~ 0.014%
Nb: 0.015% ~ 0.030%
N: <0.0050%
Ca: 0.001% ~ 0.004%
其余为 Fe和不可避免的夹杂；
且上述元素含量必须同时满足如下关系：
C、 Mn之间的关系： 15≤Mn/C≤30;
(%Si)x(%Ceq)<0.050, 其中， Ceq = C + Mn/6 + (Cu + Ni)/15 + (Cr + Mo + V)/5;
(%Si)x(%C)<0.010;
(%Mo)x[(%C) + 0.13(%Si)]在 0.003 ~ 0.020之间；
Ti/N在 2.0— 4.0之间；
Cu与 Ni之间的关系： Ni/Cu≥l .0;
Ca与 S之间的关系： Ca/S在 0.80 ~ 3.0之间；
钢板的屈服强度≥460MPa、 抗拉强度 550MPa ~ 700MPa之间、 屈强比≤0.85、 - 60°C的 Charpy冲击功 (单个值)≥60J, 钢板的显微组织为细小铁素体 +自回火贝氏 体， 平均晶粒尺寸在 15μηι以下。
2. 如权利要求 1所述的超高韧性、 优良焊接性 ΗΤ550钢板的制造方法， 包括 如下步骤： 1 ) 冶炼、 铸造
按上述成分冶炼、 铸造成板坯；
2 ) 力口热
板坯加热温度控制在 1050°C ~ 1150°C之间；
3 )控制轧制， 钢板总压缩比即板坯厚度 /成品钢板厚度≥4.0；
第一阶段为粗轧变形即再结晶轧制阶段，采用轧机最大轧制能力进行不间断地 轧制， 控制道次压下率≥8%、 累计压下率 50%、 终轧温度≥1000°〇；
粗轧结束后中间坯采用强制水冷快速降温， 保证中间坯在≤10min 内降低至采 用未再结晶控制轧制的开轧温度；
第二阶段采用未再结晶控制轧制， 开轧温度 780°C ~ 840°C , 轧制道次压下率
>7%, 累计压下率≥50%, 终轧温度 760 °C ~ 800 °C；
4 )控制冷却
控轧结束后， 钢板在辊道上摆动冷却， 冷却至钢板开冷温度， 钢板开冷温度 690°C ~ 730°C ,保证钢板处于铁素体加奥氏体两相区冷却，确保钢板的最终显微组 织为细小铁素体 +自回火贝氏体； 冷却速度≥61^, 停冷温度为 350°C ~ 600°C , 随 后緩冷工艺为钢板温度表面大于 300°C的条件下至少保温 24小时； 最终获得的成 品钢板的屈服强度≥460MPa、 抗拉强度 550MPa ~ 700MPa之间、 屈强比≤0.85、 - 60°C的 Charpy冲击功 (单个值)≥60J,钢板的显微组织为细小铁素体 +自回火贝氏体， 平均晶粒尺寸在 15μηι以下。
PCT/CN2014/074084 2013-06-19 2014-03-26 超高韧性、优良焊接性ht550钢板及其制造方法 Ceased WO2014201887A1 (zh)

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US14/889,052 US10208362B2 (en) 2013-06-19 2014-03-26 HT550 steel plate with ultrahigh toughness and excellent weldability and manufacturing method of the same
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EP14813459.6A EP3012340B1 (en) 2013-06-19 2014-03-26 Ht550 steel plate with ultrahigh toughness and excellent weldability and manufacturing method therefor
ES14813459T ES2790421T3 (es) 2013-06-19 2014-03-26 Plancha de acero HT550 con tenacidad ultraalta y soldabilidad excelente y método de fabricación de la misma

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