WO2023284128A1 - 低成本抗大线能量焊接420MPa级桥梁钢及生产方法 - Google Patents

低成本抗大线能量焊接420MPa级桥梁钢及生产方法 Download PDF

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WO2023284128A1
WO2023284128A1 PCT/CN2021/121052 CN2021121052W WO2023284128A1 WO 2023284128 A1 WO2023284128 A1 WO 2023284128A1 CN 2021121052 W CN2021121052 W CN 2021121052W WO 2023284128 A1 WO2023284128 A1 WO 2023284128A1
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low
steel
cost high
bridge steel
high heat
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French (fr)
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丁叶
洪君
王青峰
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南京钢铁股份有限公司
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—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 the technical field of iron and steel production, in particular to a low-cost high heat resistance welding 420MPa bridge steel and a production method.
  • the characteristic of general double electric double wire submerged arc welding is continuous input High (60 ⁇ 150KJ/cm, deposition efficiency is more than 50kg/h), low heat energy and welding material consumption, and has the advantages of high efficiency and energy saving, and can be adapted to butt welds, edge welds and flat fillet welds of medium and thick cross-section members , especially the advantages of welding thick-section long members (thickness ⁇ 40mm) are greater, so it has been widely used in the above-mentioned industries at home and abroad.
  • the bridge industry is subject to special reasons such as dynamic load, high fatigue requirements, and strict standards. , The development of high-efficiency submerged arc welding technology is slow. There is no batch supply performance of steel mills in China. Therefore, it is particularly important and urgent to research and develop low-cost, high-efficiency, high-efficiency and easy-to-weld bridge steels that resist large heat input.
  • the present invention aims at the above technical problems, overcomes the shortcomings of the prior art, and provides a low-cost anti-large heat input welding 420MPa grade bridge steel.
  • Its chemical composition and mass percentage are as follows: C: 0.03% ⁇ 0.10%, Si: 0.20% ⁇ 0.40%, Mn: 1.40% ⁇ 1.70%, P ⁇ 0.015%, S ⁇ 0.005%, Nb: 0.020% ⁇ 0.050%, Al: 0.015% ⁇ 0.045%, Ti: 0.008% ⁇ 0.020%, B: 0.0005% ⁇ 0.0020%, N: 0.0040% to 0.0080%, and the balance is Fe and unavoidable impurities.
  • the present invention aims at the high heat input and high efficiency welding technical requirements of bridge steel, and designs the metallurgical composition of high heat input and high efficiency welding bridge structural steel, adopts B, N and Nb, Ti composite microalloying, and uses B-N composite effect to control nano /Micro particle precipitation, micron and nano particles account for 20% and 80% respectively, control the precipitation and size of acicular ferrite, use Ti-B treatment to increase the number of intragranular ferrite, form intragranular ferrite and The mixed structure of granular bainite ensures the low-temperature toughness of the welding heat-affected zone.
  • the structure of the steel plate is uniform, the yield ratio is low, and the performance indicators are good.
  • the chemical composition and mass percentage of the aforementioned low-cost high heat resistance welding 420MPa grade bridge steel are as follows: C: 0.035% to 0.085%, Si: 0.22% to 0.38%, Mn: 1.45% to 1.65%, P ⁇ 0.014%, S ⁇ 0.004%, Nb: 0.025% ⁇ 0.045%, Al: 0.018% ⁇ 0.043%, Ti: 0.009% ⁇ 0.018%, B: 0.0005% ⁇ 0.0018%, N: 0.0042% ⁇ 0.0076%, balance For Fe and unavoidable impurities.
  • the chemical composition and mass percentages of the aforementioned low-cost high heat resistance welding 420MPa grade bridge steel are as follows: C: 0.035%-0.084%, Si: 0.22%-0.38%, Mn: 1.50%-1.68%, P ⁇ 0.014%, S ⁇ 0.004%, Nb: 0.030% ⁇ 0.048%, Al: 0.017% ⁇ 0.043%, Ti: 0.010% ⁇ 0.01820%, B: 0.0005% ⁇ 0.0018%, N: 0.0043% ⁇ 0.0076%, balance For Fe and unavoidable impurities.
  • the chemical composition and mass percentage of the aforementioned low-cost high heat resistance welding 420MPa grade bridge steel are as follows: C: 0.035% to 0.085%, Si: 0.24% to 0.38%, Mn: 1.50% to 1.67%, P ⁇ 0.014%, S ⁇ 0.004%, Nb: 0.030% ⁇ 0.047%, Al: 0.017% ⁇ 0.043%, Ti: 0.008% ⁇ 0.017%, B: 0.0005% ⁇ 0.0018%, N: 0.0044% ⁇ 0.0078%, balance For Fe and unavoidable impurities.
  • Another object of the present invention is to provide a low-cost production method for high-energy-resistance welding 420MPa grade bridge steel, including smelting, steelmaking, and rolling processes.
  • RH vacuum treatment controls the high vacuum degree below 5mbar, the vacuum time between 10 and 18 minutes, and cooperates with static argon blowing and stirring to stably control the N content in molten steel at 0.0040% to 0.0080%;
  • Rolling process the total time in the furnace is 8-16min/cm, the soaking time is ⁇ 1.4min/cm, and micron-sized Ti/B-rich particles are formed by low-temperature heating; Two-stage controlled rolling in the recrystallization zone. After rolling, DQ ultra-fast cooling is used for rapid cooling. The first stage rolling temperature is controlled at 1040 ⁇ 1120°C, the second stage finish rolling is at 750 ⁇ 850°C, and the water inlet temperature is controlled at 700 ⁇ Nano-scale Nb-rich particles are formed at 800°C, and the red-return temperature is controlled between 500-600°C through ultra-fast cooling technology, and the obtained micron and nano-particles account for 20% and 80% respectively.
  • the low-temperature heating temperature is 1100-1200°C.
  • the ultra-fast cooling rate is 1-10°C/s.
  • the thickness of the steel plate is 20-60 mm.
  • the TMCP microstructure of the steel plate is 85% bainite and 15% ferrite.
  • the carbon equivalent Ceq is 0.32% to 0.38%, controlling the smelting process, and through a reasonable TMCP process, the final rolled steel plate has high strength and excellent low-temperature impact performance, and other properties Good indicators, yield strength ReL460 ⁇ 520MPa, tensile strength Rm ⁇ 570MPa, elongation A% ⁇ 18%, -40°C longitudinal impact energy single value ⁇ 150J, transverse bending without cracks;
  • the steel plate produced by the present invention has good thermal processing processability, low sensitivity to welding cold cracks, the steel plate can be welded without preheating, and the welding line energy is increased from 20-45kJ/cm of ordinary bridge steel to 100-150kJ/cm ;
  • Carbon increases the yield strength and tensile strength at the same time, but the tensile strength increases even more.
  • Properly increasing the carbon content in the steel is beneficial to reduce the yield strength ratio of the test steel; however, as the carbon content increases, the low temperature of the test steel The toughness decreases, Ceq and Pcm increase significantly, and the welding performance deteriorates. Therefore, the C content of the test steel is controlled within the range of 0.03% to 0.10%, and the influence of the C content on the properties of the test steel is focused on;
  • Si increases the number of residual A or M-A islands in bainitic steel, which is beneficial to reduce the yield ratio, but too high Si content reduces the low-temperature toughness of steel and its welding heat-affected zone.
  • Si content of the test steel should be controlled within the range of 0.20% to 0.40%;
  • Mn promotes the transformation of medium-temperature structures such as quasi-polygonal ferrite, acicular ferrite, and bainite in steel, refines ferrite grains, and significantly increases yield strength, which is beneficial to improving the strength and low-temperature toughness of steel , but with the increase of Mn content, the yield ratio tends to increase. In addition, too high Mn is easy to form center segregation, and Mn significantly increases Ceq and Pcm. The upper limit of Mn content should be limited. Therefore, the test steel Mn content is controlled within the range of 1.40% to 1.70%;
  • Niobium is the most important microalloying element in low-alloy steel and low-carbon bainitic steel produced by TMCP process. It plays the role of fine-grain strengthening and precipitation strengthening in steel plate. Niobium can play a pinning dislocation through strain-induced precipitation. Above 1000°C, niobium mainly exists in solid solution form in steel, which hinders dislocation movement and inhibits recrystallization through solute dragging effect. Because of its high precipitation temperature, it can prevent the growth of austenite crystals, delay the occurrence of recrystallization, increase the recrystallization temperature of steel, and refine the grains through controlled rolling.
  • Titanium After the micro-Ti treatment of the steel, the formed TiN can effectively inhibit the coarsening of the original austenite grains in the welding heat-affected zone, improve the low-temperature toughness, and help improve the welding performance of the steel. Too little titanium is not conducive to exerting the The above effect, its content should not be less than 0.008%, but too much titanium is easy to form TiN inclusions with sharp corners and reduce low temperature toughness, its content should not exceed 0.020%, therefore, the appropriate titanium content in the test steel is controlled at 0.008% ⁇ 0.020% range;
  • Aluminum Adding aluminum in the steelmaking process can reduce the content of inclusions in steel and refine grains, but too much aluminum, on the one hand, promotes type B inclusions in steel, and "takes away” too much in steel Nitrogen weakens the precipitation strengthening effect of vanadium. On the other hand, it transitions into the weld during the welding process, promotes the transformation of granular bainite, inhibits the formation of acicular ferrite, and significantly deteriorates the low-temperature toughness of the weld. Therefore, the test The aluminum content in steel should be controlled within the range of 0.015% to 0.045%;
  • N there is a complex relationship between N and the yield ratio of steel. A small amount of N acts similarly to C, which reduces the yield ratio. Increasing N in an appropriate amount increases the amount of ferrite, reduces the amount of hard phases, and increases the yield ratio. Increase N, increase the number of residual A or M-A islands, and reduce the yield ratio, but it is not conducive to the low-temperature toughness of the welding heat-affected zone. Therefore, the nitrogen content in the test steel is controlled within the range of 0.0040% to 0.0080%;
  • Sulfur and phosphorus Due to the high strength of low-carbon bainite steel and the requirement of good toughness and plasticity, the requirements for the control of sulfur and phosphorus content in the steel are relatively high, so as to ensure the plasticity and toughness of the steel and prevent the grain boundary segregation of copper and CuS (or Cu2S, etc.) precipitation will cause cracks on the surface of copper-containing steel slabs and rolled products, and the existence of S and P will also deteriorate the weldability of steel. Therefore, the sulfur and phosphorus contents in the test steel are controlled at S ⁇ 0.005%, Within the range of P ⁇ 0.015%;
  • Boron a strong grain boundary segregation element, which can preferentially occupy the grain boundary position and avoid the segregation of impurity elements.
  • boron can also reduce the interface energy, control the precipitation of proeutectoid ferrite, and act as a composite of B-N in steel , regulate the precipitation of two types of particles of 10-100nm level and 0.1-2 ⁇ m level in the steel, nano-sized particles induce the nucleation of acicular ferrite, and micron-sized particles control the grain size, therefore, the boron content in the test steel is controlled at 0.0005% ⁇ 0.0020% range.
  • Fig. 1 is the original tissue morphology at 1/4 of the thickness of the 40mm thick steel plate in embodiment 2;
  • Fig. 2 is the structure morphology of the 40mm thick steel in Example 2 under the simulated 100KJ/cm welding input energy.
  • This embodiment provides a low-cost anti-large heat input welding 420MPa grade bridge steel, Q420qE with a thickness of 20mm, its chemical composition and mass percentage are as follows: C: 0.09%, Si: 0.33%, Mn: 1.44%, P: 0.011 %, S: 0.003%, Nb: 0.023%, Al: 0.037%, Ti: 0.009%, B: 0.0009%, N: 0.0065%, and the balance is Fe and unavoidable impurities.
  • RH vacuum treatment controls the N content in molten steel at 0.0065% to 0.0072% by controlling the high vacuum degree below 5mbar and the vacuum time between 15min, combined with static argon blowing and stirring;
  • Rolling process the total time in the furnace is 268min, the soaking time is 50min, and micron-sized (0.1-2 ⁇ m) Ti/B-rich particles are formed by heating at a low temperature of 1198°C; Two-stage controlled rolling in the crystallization zone. After rolling, DQ ultra-fast cooling is used for rapid cooling. The starting temperature of the first stage is controlled at 1080°C. The starting temperature of the second stage of finish rolling is 850°C. After the rolling, the water temperature is controlled at 765°C to form nano-scale (10-100nm) Nb-rich particles, and the temperature of reddening is controlled between 550-575°C through a 5°C/s ultra-fast cooling process to obtain micron and nano-particles, respectively. Accounted for 20% and 80%.
  • the mechanical properties of the steel plate obtained under this process are: yield strength 472MPa, tensile strength 585MPa, elongation 22.5%, 1/4 plate thickness - 40 °C longitudinal impact average value 322J.
  • the difference between the low-cost high heat resistance welding 420MPa grade bridge steel provided in this example and Example 1 is that the chemical composition and mass percentage of Q420qE with a thickness of 40mm are as follows: C: 0.09%, Si: 0.32%, Mn: 1.43%, P: 0.011%, S: 0.003%, Nb: 0.027%, Al: 0.037%, Ti: 0.009%, B: 0.0014%, N: 0.0062%, and the balance is Fe and unavoidable impurities.
  • RH vacuum treatment controls the high vacuum degree below 5mbar and the vacuum time between 14min, combined with static argon blowing and stirring, to stably control the N content in molten steel at 0.0040% to 0.0056%;
  • Rolling process the total time in the furnace is 232min, the soaking time is 33min, and micron-sized (0.1-2 ⁇ m) Ti/B-rich particles are formed by heating at a low temperature of 1193°C; Two-stage controlled rolling in the crystallization zone. After rolling, DQ ultra-fast cooling is used for rapid cooling.
  • the starting temperature of the first stage is controlled at 1042°C.
  • the starting temperature of the second stage of finish rolling is 840°C.
  • the entering water temperature is 773°C to form nanoscale (10-100nm) Nb-rich particles, and the temperature of reddening is controlled between 525°C and 545°C through a 6°C/s ultra-fast cooling process, and the obtained micron and nano-particles account for 20% and 100% respectively. 80%.
  • the mechanical properties of the steel plate obtained under this process are: yield strength 505MPa, tensile strength 604MPa, elongation 19.5%, 1/4 plate thickness - 40 °C longitudinal impact average value 285J.
  • Welding heat simulation Gleeble3500 testing machine was used to simulate the thermal cycle process of the test steel under 100kJ/cm line energy.
  • the welding thermal cycle curve was also generated by the HAZ software package Rykalin-2D heat transfer model.
  • the difference between the low-cost high heat resistance welding 420MPa bridge steel provided in this example and Example 1 is that the chemical composition and mass percentage of Q420qE with a thickness of 60mm are as follows: C: 0.09%, Si: 0.32%, Mn: 1.43%, P: 0.011%, S: 0.003%, Nb: 0.027%, Al: 0.037%, Ti: 0.009%, B: 0.0014%, N: 0.0062%, and the balance is Fe and unavoidable impurities.
  • RH vacuum treatment controls the high vacuum degree below 5mbar and the vacuum time between 14min, combined with static argon blowing and stirring, to stably control the N content in molten steel at 0.0040% to 0.0044%;
  • Rolling process the total time in the furnace is 218min, the soaking time is 36min, and micron-sized (0.1-2 ⁇ m) Ti/B-rich particles are formed by heating at a low temperature of 1160°C; Two-stage controlled rolling in the crystallization zone. After rolling, DQ ultra-fast cooling is used for rapid cooling.
  • the starting temperature of the first stage is controlled at 1050°C.
  • the starting temperature of the second stage of finish rolling is 830°C.
  • the entering water temperature is 787°C to form nano-scale (10-100nm) Nb-rich particles, and the temperature of reddening is controlled between 506-534°C through a 5°C/s ultra-fast cooling process, and micron and nano-particles account for 20% and 100% respectively. 80%.
  • the mechanical properties of the steel plate obtained under this process are: yield strength 481MPa, tensile strength 585MPa, elongation 24%, 1/4 plate thickness - 40 °C longitudinal impact average value 299J.
  • Example 1 The mechanical properties of the steel plates obtained in Example 1, Example 2, and Example 3 all meet the performance requirements of Q420qE in the relevant technical conditions of the enterprise standard Q/320116NJGT 272-2020 "Bridge steel plates for high-efficiency welding with large heat input", and the mechanical properties are excellent and It has strong operability.
  • the present invention produces Q420qE with a thickness of 20-60mm
  • the steel plate produced by the TMCP production process has a carbon equivalent of ⁇ 0.38%, a yield strength of ⁇ 420MPa, a longitudinal low-temperature impact of -40°C ⁇ 120J, and a large wire of ⁇ 100KJ/cm Longitudinal low-temperature impact at -40°C of the welded joint after energy welding ⁇ 47J.
  • the benefit per ton of steel is about 800 yuan/ton
  • the annual production of Nangang is about 10,000 tons, and the annual benefit can reach 8 million yuan.
  • the present invention can also have other implementations. All technical solutions formed by equivalent replacement or equivalent transformation fall within the scope of protection required by the present invention.

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Abstract

一种低成本抗大线能量焊接420MPa级桥梁钢及生产方法，涉及钢铁生产技术领域，其化学成分及质量百分比如下：C：0.03％～0.10％，Si：0.20％～0.40％，Mn：1.40％～1.70％，P≤0.015％，S≤0.005％，Nb：0.020％～0.050％，Al：0.015％～0.045％，Ti：0.008％～0.020％，B：0.0005％～0.0020％，N：0.0040％～0.0080％，余量为Fe和不可避免的杂质。保证焊接热影响区低温韧性，钢板组织均匀，屈强比低，各项性能指标良好。

Description

低成本抗大线能量焊接420MPa级桥梁钢及生产方法 技术领域
本发明涉及钢铁生产技术领域，特别是涉及一种低成本抗大线能量焊接420MPa级桥梁钢及生产方法。
背景技术
目前，我国铁路钢桥建设正在向适应重载、高速、大跨度、轻量化、全焊接节点钢结构的方向发展。为适应桥梁技术进步要求，集高强度、高韧性、低屈强比、易焊接等多项性能为一体的新一代高性能桥梁钢是大跨重载铁路钢桥关键构件的首选材料，需求明确而迫切。
随着现代桥梁、建筑、船舶、管线、容器等钢结构向大型化、高参数、安全性、耐久性方向发展，高效焊接技术重要性愈显突出。在多丝埋弧焊、窄间隙埋弧焊、气电立焊和电渣焊等几种常见的高效焊接方法中，多丝埋弧焊的使用较多，其中又以双丝埋弧焊的应用较为普遍。与单电单丝或单电双细丝埋弧焊(热输入为25～45KJ/cm，熔敷效率为8～15kg/h)相比，一般双电双丝埋弧焊的特点是连续输入高(60～150KJ/cm，熔敷效率为50kg/h以上)、热能和焊材消耗少而具有高效节能的优势，可适应于中厚截面构件的对接焊缝、棱角焊缝和平角焊缝，特别是焊接厚截面长构件(板厚≥40mm)的优势更大，从而在国内外上述多个行业都得到了广泛的应用，桥梁行业受其动载、疲劳要求高、标准严等特殊原因，高效埋弧焊技术发展缓慢。国内暂无钢厂批量供货业绩。因此，研制开发出低成本抗大线能量高效易焊接桥梁钢，已显得尤为重要和迫切。
发明内容
本发明针对上述技术问题，克服现有技术的缺点，提供一种低成本抗大线能量焊接420MPa级桥梁钢，其化学成分及质量百分比如下：C：0.03％～0.10％，Si：0.20％～0.40％，Mn：1.40％～1.70％，P≤0.015％，S≤0.005％，Nb：0.020％～ 0.050％，Al：0.015％～0.045％，Ti：0.008％～0.020％，B：0.0005％～0.0020％，N：0.0040％～0.0080％，余量为Fe和不可避免的杂质。
技术效果：本发明针对桥梁钢大热输入高效焊接技术要求，设计了大热输入高效焊接桥梁用结构钢的冶金成分，采用B、N与Nb、Ti复合微合金化，利用B-N复合作用调控纳米/微米粒子析出，得到微米与纳米粒子分别占20％与80％，控制针状铁素体析出及尺寸，利用Ti-B处理使晶内铁素体的数量增加，形成晶内铁素体和粒状贝氏体的混合组织，保证焊接热影响区低温韧性。钢板组织均匀，屈强比低，各项性能指标良好。
本发明进一步限定的技术方案是：
前所述的低成本抗大线能量焊接420MPa级桥梁钢，其化学成分及质量百分比如下：C：0.035％～0.085％，Si：0.22％～0.38％，Mn：1.45％～1.65％，P≤0.014％，S≤0.004％，Nb：0.025％～0.045％，Al：0.018％～0.043％，Ti：0.009％～0.018％，B：0.0005％～0.0018％，N：0.0042％～0.0076％，余量为Fe和不可避免的杂质。
前所述的低成本抗大线能量焊接420MPa级桥梁钢，其化学成分及质量百分比如下：C：0.035％～0.084％，Si：0.22％～0.38％，Mn：1.50％～1.68％，P≤0.014％，S≤0.004％，Nb：0.030％～0.048％，Al：0.017％～0.043％，Ti：0.010％～0.01820％，B：0.0005％～0.0018％，N：0.0043％～0.0076％，余量为Fe和不可避免的杂质。
前所述的低成本抗大线能量焊接420MPa级桥梁钢，其化学成分及质量百分比如下：C：0.035％～0.085％，Si：0.24％～0.38％，Mn：1.50％～1.67％，P≤0.014％，S≤0.004％，Nb：0.030％～0.047％，Al：0.017％～0.043％，Ti：0.008％～0.017％，B：0.0005％～0.0018％，N：0.0044％～0.0078％，余量为Fe和不可避免的杂质。
本发明的另一目的在于提供一种低成本抗大线能量焊接420MPa级桥梁钢的生产方法，包括冶炼、炼钢、轧制工序，
冶炼：钢水经脱硫预处理、转炉冶炼、LF精炼、RH真空处理，然后通过 连铸浇铸成连铸坯；
炼钢：RH真空处理通过控制高真空度在5mbar以下、真空时间在10～18min之间，配合静置吹氩搅拌，将钢水中的N含量稳定控制在0.0040％～0.0080％；
轧制工序：总在炉时间8～16min/cm，均热时间≥1.4min/cm，经低温加热形成微米级富Ti/B粒子；连铸坯出炉后，采用奥氏体再结晶区+未再结晶区两阶段控制轧制，轧后采用DQ超快冷进行快速冷却，第一阶段开轧温度控制为1040～1120℃，第二阶段精轧在750～850℃，控制入水温度为700～800℃之间形成纳米级的富Nb粒子，通过超快冷工艺使返红温度控制在500～600℃之间，得到微米与纳米粒子分别占20％与80％。
前所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，低温加热温度为1100～1200℃。
前所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，超快冷冷却速度为1～10℃/s。
前所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，钢板厚度为20～60mm。
前所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，钢板TMCP态组织为85％贝氏体和15％铁素体。
本发明的有益效果是：
(1)本发明通过优化成分设计，碳当量Ceq为0.32％～0.38％，控制冶炼工序，并通过合理的TMCP工艺，最终轧制的钢板具有高强度及优异的低温冲击性能，其它各项性能指标良好，屈服强度ReL460～520MPa、抗拉强度Rm≥570MPa、延伸率A％≥18％、-40℃纵向冲击功单值≥150J、横向弯曲无裂纹；
(2)本发明生产的钢板热加工工艺性良好，焊接冷裂纹敏感性较低，钢板 可实现免预热焊接，焊接线能量由普通桥梁钢的20～45kJ/cm提升至100～150kJ/cm；
(3)本发明中设计试验钢的化学成分时，综合考虑了C、Si、Mn、B、Nb、Ti、Al、N等合金元素对屈强比、碳当量、多相组织制备的ACC控冷工艺窗口、强度与屈强比匹配、强度与韧性匹配、焊接性等多方面因素的影响：
碳：C同时提高屈服强度和抗拉强度，但对抗拉强度提升更大，适当增加钢中的碳含量，有利于降低试验钢的屈强比；然而，随着碳含量增加，试验钢的低温韧性下降，Ceq和Pcm显著提高，焊接性能恶化，因此，将试验钢的C含量控制在0.03％～0.10％的范围内，并重点研究C含量对试验钢各项性能的影响；
硅：Si在贝氏体钢中增加残A或M-A岛数量，有利于降低屈强比，但过高的Si含量降低钢及其焊接热影响区的低温韧性，在设计和制备大跨重载焊接桥梁用钢时，不适于在钢中添加过高的Si，因此，将试验钢的Si含量控制在0.20％～0.40％的范围内；
锰：Mn在钢中促进准多边形铁素体、针状铁素体、贝氏体等中温组织转变，细化铁素体晶粒，使屈服强度显著提高，有利于提高钢的强度和低温韧性，但随Mn含量增加，屈强比呈增大的趋势，另外，过高的Mn易形成中心偏析，且Mn显著提高Ceq和Pcm，对Mn含量的上限应加以限定，因此，将试验钢的Mn含量控制在1.40％～1.70％的范围内；
铌：Nb是TMCP工艺生产低合金钢和低碳贝氏体钢中最主要的微合金元素，在钢板中起细晶强化和沉淀强化的作用，铌通过应变诱导析出可起到钉扎位错的运动作用，在1000℃以上铌主要以固溶形式存在于钢中，其通过溶质拖曳作用阻碍位错运动，抑制再结晶的进行，在900～1000℃时Nb以NbC或者Nb(NC)的形式析出，由于其析出温度较高，因此可以阻止奥氏体晶体的长大，起到推迟再结晶发生的作用，提高钢的再结晶温度，进而通过控制轧制来细化晶粒， 铌在再加热时可以抑制奥氏体晶粒的长大，提高其粗化温度，并在热变形过程中阻止再结晶后的晶粒长大，使晶粒细化并扩大奥氏体未再结晶区，增加未再结晶区的变形量和变形道次，使相变后晶粒细，但是，有焊接试验表明，过高的Nb含量，有可能使焊接接头产生热裂纹，因此，试验钢中的Nb控制在0.020％～0.050％的范围内，并重点研究Nb含量对试验钢各项性能的影响；
钛：对钢进行微Ti处理后，形成的TiN可以有效抑制焊接热影响区原奥氏体晶粒的粗化，提高低温韧性，有利于改善钢的焊接性能，过少的钛不利于发挥所述作用，其含量不宜低于0.008％，但过多的钛易形成带尖角方形的TiN夹杂，降低低温韧性，其含量不宜超过0.020％，因此，试验钢中合适的钛含量控制在0.008％～0.020％范围内；
铝：在炼钢过程中加入铝，可以减少钢中的夹杂物含量，细化晶粒，但过多的铝，一方面，在钢中促进B类夹杂，在钢中“夺走”过多的氮，弱化钒的沉淀强化效果，另一方面，在焊接过程中过渡到焊缝中，促进粒状贝氏体转变、抑制针状铁素体形成，显著恶化焊缝的低温韧性，因此，试验钢中的铝含量应控制在0.015％～0.045％范围内；
氮：N与钢的屈强比之间存在复杂关系，微量的N作用类似于C，使屈强比降低，适量增N，铁素体数量增多，硬相数量降低，屈强比提高，大量增N，增加残A或M-A岛数量，屈强比降低，但不利于焊接热影响区的低温韧性，因此，试验钢中的氮含量控制在0.0040％～0.0080％范围内；
硫、磷：由于低碳贝氏体钢强度高，同时要求韧塑性好，因此对钢中的硫、磷含量控制要求较高，以保证钢材的塑性与韧性，并防止由于铜的晶界偏析及CuS(或Cu2S等)析出引起含铜钢铸坯及轧材表面开裂，S、P的存在也会恶化钢材的焊接性能，因此，试验钢中的硫、磷含量控制在S≤0.005％、P≤0.015％的范围内；
硼：强烈的晶界偏聚元素，能优先占据晶界位置，避免杂质元素的偏聚，同时硼元素还可以降低界面能，控制先共析铁素体的析出，在钢中以B-N复合作用，调控钢中10～100nm级别与0.1～2μm级别两类粒子的析出，纳米级微粒诱导针状铁素体形核，微米级粒子控制晶粒大小，因此，试验钢中的硼含量控制在0.0005％～0.0020％范围内。
附图说明
图1为实施例2中40mm厚钢板厚度1/4处原始组织形貌；
图2为实施例2中40mm厚钢模拟100KJ/cm焊接线能量下组织形貌。
具体实施方式
实施例1
本实施例提供的一种低成本抗大线能量焊接420MPa级桥梁钢，厚度20mm的Q420qE，其化学成分及质量百分比如下：C：0.09％，Si：0.33％，Mn：1.44％，P：0.011％，S：0.003％，Nb：0.023％，Al：0.037％，Ti：0.009％％，B：0.0009％，N：0.0065％，余量为Fe和不可避免的杂质。
其生产方法包括冶炼、炼钢、轧制工序，
冶炼：钢水经脱硫预处理、转炉冶炼、LF精炼、RH真空处理，然后通过连铸浇铸成260mm厚的连铸坯；
炼钢：RH真空处理通过控制高真空度在5mbar以下、真空时间在15min之间，配合静置吹氩搅拌，将钢水中的N含量稳定控制在0.0065％～0.0072％；
轧制工序：总在炉时间268min，均热时间50min，经1198℃低温加热形成微米级(0.1-2μm)富Ti/B粒子；连铸坯出炉后，采用奥氏体再结晶区+未再结晶区两阶段控制轧制，轧后采用DQ超快冷进行快速冷却，第一阶段开轧温度控制为1080℃，第二阶段精轧开轧温度850℃，终轧温度814～832℃，精轧结束后控制入水温度为765℃形成纳米级(10-100nm)的富Nb粒子，通过5℃/s 超快冷工艺使返红温度控制在550～575℃之间，得到微米与纳米粒子分别占20％与80％。
此工艺下所得钢板的力学性能为：屈服强度472MPa，抗拉强度585MPa，延伸率22.5％，1/4板厚-40℃纵向冲击均值为322J。
实施例2
本实施例提供的一种低成本抗大线能量焊接420MPa级桥梁钢，与实施例1的区别在于，厚度40mm的Q420qE，其化学成分及质量百分比如下：C：0.09％，Si：0.32％，Mn：1.43％，P：0.011％，S：0.003％，Nb：0.027％，Al：0.037％，Ti：0.009％，B：0.0014％，N：0.0062％，余量为Fe和不可避免的杂质。
其生产方法包括冶炼、炼钢、轧制工序，
冶炼：钢水经脱硫预处理、转炉冶炼、LF精炼、RH真空处理，然后通过连铸浇铸成260mm厚的连铸坯；
炼钢：RH真空处理通过控制高真空度在5mbar以下、真空时间在14min之间，配合静置吹氩搅拌，将钢水中的N含量稳定控制在0.0040％～0.0056％；
轧制工序：总在炉时间232min，均热时间33min，经1193℃低温加热形成微米级(0.1-2μm)富Ti/B粒子；连铸坯出炉后，采用奥氏体再结晶区+未再结晶区两阶段控制轧制，轧后采用DQ超快冷进行快速冷却，第一阶段开轧温度控制为1042℃，第二阶段精轧开轧温度840℃，终轧温度779～821℃，控制入水温度为773℃形成纳米级(10-100nm)的富Nb粒子，通过6℃/s超快冷工艺使返红温度控制在525～545℃之间，得到微米与纳米粒子分别占20％与80％。
此工艺下所得钢板的力学性能为：屈服强度505MPa，抗拉强度604MPa，延伸率19.5％，1/4板厚-40℃纵向冲击均值为285J。
焊接热模拟：采用Gleeble3500试验机模拟了试验钢在100kJ/cm线能量下的热循环工艺过程，焊接热循环曲线同样采用HAZ软件包Rykalin-2D传热模型 生成，基本参数为：加热速度100℃/s，最高加热温度Tp＝1350℃，终冷温度为200℃或至相变完全结束。
此模拟焊接工艺下-40℃纵向冲击均值为172J，板条贝氏体基本消失，Ti-B处理使晶内铁素体的数量增加，如图2，形成晶内铁素体和粒状贝氏体的混合组织。
实施例3
本实施例提供的一种低成本抗大线能量焊接420MPa级桥梁钢，与实施例1的区别在于，厚度60mm的Q420qE，其化学成分及质量百分比如下：C：0.09％，Si：0.32％，Mn：1.43％，P：0.011％，S：0.003％，Nb：0.027％，Al：0.037％，Ti：0.009％，B：0.0014％，N：0.0062％，余量为Fe和不可避免的杂质。
其生产方法包括冶炼、炼钢、轧制工序，
冶炼：钢水经脱硫预处理、转炉冶炼、LF精炼、RH真空处理，然后通过连铸浇铸成260mm厚的连铸坯；
炼钢：RH真空处理通过控制高真空度在5mbar以下、真空时间在14min之间，配合静置吹氩搅拌，将钢水中的N含量稳定控制在0.0040％～0.0044％；
轧制工序：总在炉时间218min，均热时间36min，经1160℃低温加热形成微米级(0.1-2μm)富Ti/B粒子；连铸坯出炉后，采用奥氏体再结晶区+未再结晶区两阶段控制轧制，轧后采用DQ超快冷进行快速冷却，第一阶段开轧温度控制为1050℃，第二阶段精轧开轧温度830℃，终轧温度794～821℃，控制入水温度为787℃形成纳米级(10-100nm)的富Nb粒子，通过5℃/s超快冷工艺使返红温度控制在506～534℃之间，得到微米与纳米粒子分别占20％与80％。
此工艺下所得钢板的力学性能为：屈服强度481MPa，抗拉强度585MPa，延伸率24％，1/4板厚-40℃纵向冲击均值为299J。
实施例1、实施例2、实施例3所得钢板的力学性能均满足Q/320116NJGT 272-2020《大热输入高效焊接用桥梁钢板》企业标准相关技术条件中Q420qE的性能要求，力学性能结果优异且具有较强的可操作性。
综上所述，本发明生产厚度为20～60mm的Q420qE，采用TMCP生产工艺生产的钢板，碳当量≤0.38％，屈服强度≥420MPa，-40℃纵向低温冲击≥120J，≥100KJ/cm大线能量焊接后焊接接头的-40℃纵向低温冲击≥47J。吨钢效益约800元/吨，南钢年生产量约10000吨，年效益可达800万元。
除上述实施例外，本发明还可以有其他实施方式。凡采用等同替换或等效变换形成的技术方案，均落在本发明要求的保护范围。

Claims (9)

  1. 一种低成本抗大线能量焊接420MPa级桥梁钢，其特征在于：其化学成分及质量百分比如下：C：0.03％～0.10％，Si：0.20％～0.40％，Mn：1.40％～1.70％，P≤0.015％，S≤0.005％，Nb：0.020％～0.050％，Al：0.015％～0.045％，Ti：0.008％～0.020％，B：0.0005％～0.0020％，N：0.0040％～0.0080％，余量为Fe和不可避免的杂质。
  2. 根据权利要求1所述的低成本抗大线能量焊接420MPa级桥梁钢，其特征在于：其化学成分及质量百分比如下：C：0.035％～0.085％，Si：0.22％～0.38％，Mn：1.45％～1.65％，P≤0.014％，S≤0.004％，Nb：0.025％～0.045％，Al：0.018％～0.043％，Ti：0.009％～0.018％，B：0.0005％～0.0018％，N：0.0042％～0.0076％，余量为Fe和不可避免的杂质。
  3. 根据权利要求1所述的低成本抗大线能量焊接420MPa级桥梁钢，其特征在于：其化学成分及质量百分比如下：C：0.035％～0.084％，Si：0.22％～0.38％，Mn：1.50％～1.68％，P≤0.014％，S≤0.004％，Nb：0.030％～0.048％，Al：0.017％～0.043％，Ti：0.010％～0.01820％，B：0.0005％～0.0018％，N：0.0043％～0.0076％，余量为Fe和不可避免的杂质。
  4. 根据权利要求1所述的低成本抗大线能量焊接420MPa级桥梁钢，其特征在于：其化学成分及质量百分比如下：C：0.035％～0.085％，Si：0.24％～0.38％，Mn：1.50％～1.67％，P≤0.014％，S≤0.004％，Nb：0.030％～0.047％，Al：0.017％～0.043％，Ti：0.008％～0.017％，B：0.0005％～0.0018％，N：0.0044％～0.0078％，余量为Fe和不可避免的杂质。
  5. 一种低成本抗大线能量焊接420MPa级桥梁钢的生产方法，其特征在于：应用于权利要求1-4任意一项，包括冶炼、炼钢、轧制工序，
    冶炼：钢水经脱硫预处理、转炉冶炼、LF精炼、RH真空处理，然后通过连铸浇铸成连铸坯；
    炼钢：RH真空处理通过控制高真空度在5mbar以下、真空时间在10～18min 之间，配合静置吹氩搅拌，将钢水中的N含量稳定控制在0.0040％～0.0080％；
    轧制工序：总在炉时间8～16min/cm，均热时间≥1.4 min/cm，经低温加热形成微米级富Ti/B粒子；连铸坯出炉后，采用奥氏体再结晶区+未再结晶区两阶段控制轧制，轧后采用DQ超快冷进行快速冷却，第一阶段开轧温度控制为1040～1120℃，第二阶段精轧在750～850℃，控制入水温度为700～800℃之间形成纳米级的富Nb粒子，通过超快冷工艺使返红温度控制在500～600℃之间，得到微米与纳米粒子分别占20％与80％。
  6. 根据权利要求5所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，其特征在于：低温加热温度为1100～1200℃。
  7. 根据权利要求5所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，其特征在于：超快冷冷却速度为1～10℃/s。
  8. 根据权利要求5所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，其特征在于：钢板厚度为20～60mm。
  9. 根据权利要求5所述的低成本抗大线能量焊接420MPa级桥梁钢的生产方法，其特征在于：钢板TMCP态组织为85％贝氏体和15％铁素体。
PCT/CN2021/121052 2021-07-12 2021-09-27 低成本抗大线能量焊接420MPa级桥梁钢及生产方法 WO2023284128A1 (zh)

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