CN118639141A - A gigapascal-grade offshore steel plate for extremely cold and ultra-deep environments and a manufacturing method thereof - Google Patents
A gigapascal-grade offshore steel plate for extremely cold and ultra-deep environments and a manufacturing method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 129
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- 238000010438 heat treatment Methods 0.000 claims abstract description 30
- 238000000034 method Methods 0.000 claims abstract description 28
- 238000005242 forging Methods 0.000 claims abstract description 27
- 238000005496 tempering Methods 0.000 claims abstract description 21
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- 230000000171 quenching effect Effects 0.000 claims abstract description 18
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- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
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- 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
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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
- 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
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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
- 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
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
- C22B9/18—Electroslag remelting
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- C—CHEMISTRY; METALLURGY
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract
本发明属于钢铁材料制备技术领域,具体涉及一种极寒超深环境用千兆帕级海工钢板及其制造方法。所述钢板按重量百分比计,包括以下组分:C:0.08%‑0.15%,Si:0.15%‑0.45%,Mn:0.6%‑1.15%,P≤0.02%,S≤0.01%,Als:0.005%‑0.05%,Ni:7.2%‑14%,Cr:0.46%‑0.64%,Mo:0.55%‑0.79%,Cu:0.42%‑0.76%,Co:0.1%‑10.0%,V:0.11%‑0.23%,Ti:0.01%‑0.5%,N:0.003%‑0.007%,其余为Fe和不可避免的杂质。本发明通过合金元素筛选与配比、冶炼、电渣重熔、锻造开坯、两阶段控制轧制以及多次调质热处理工艺的优化与参数选择,制得的钢板低温韧性优良、1000MPa超高强度、抗疲劳性能优良,其力学性能、高服役安全性能能够达到海洋工程设备服役条件,适用于极寒超深环境。
The present invention belongs to the technical field of steel material preparation, and specifically relates to a gigapascal-level marine engineering steel plate for extremely cold and ultra-deep environments and a manufacturing method thereof. The steel plate comprises the following components by weight percentage: C: 0.08%-0.15%, Si: 0.15%-0.45%, Mn: 0.6%-1.15%, P≤0.02%, S≤0.01%, Als: 0.005%-0.05%, Ni: 7.2%-14%, Cr: 0.46%-0.64%, Mo: 0.55%-0.79%, Cu: 0.42%-0.76%, Co: 0.1%-10.0%, V: 0.11%-0.23%, Ti: 0.01%-0.5%, N: 0.003%-0.007%, and the rest is Fe and unavoidable impurities. The present invention achieves excellent low-temperature toughness, 1000MPa ultra-high strength, and excellent fatigue resistance by optimizing and selecting alloy element screening and proportioning, smelting, electroslag remelting, forging and blanking, two-stage controlled rolling, and multiple quenching and tempering heat treatment processes. The steel plate has mechanical properties and high service safety performance that can meet the service conditions of marine engineering equipment and is suitable for extremely cold and ultra-deep environments.
Description
技术领域Technical Field
本发明涉及钢铁材料制备技术领域,具体而言,尤其涉及一种极寒超深环境用千兆帕级海工钢板及其制造方法。The present invention relates to the technical field of steel material preparation, and in particular to a gigapascal-level marine engineering steel plate for extremely cold and ultra-deep environments and a manufacturing method thereof.
背景技术Background Art
随着科技发展和人民生活水平提高,世界各国开始聚焦海洋中的大量资源。由于海工装备产业快速发展,市场对高强度特厚超低温韧性海工钢板的需求不断增加。传统油气能源日益枯竭,因此北极地区的石油、天然气和液化天然气储量变得越来越有价值。在全球温室效应的影响下,北极升温加剧,海冰覆盖面积不断减少,这促进了资源开发和船舶航行。俄罗斯和北欧国家明显加快了北极的油气勘探与开发,并推动了大型高技术极地海工装备的需求和发展。因此,高强度级别极地低温海工钢逐渐成为发展趋势。海洋工程平台服役环境恶劣,因此需要考虑多种因素影响,在选材方面必须能适应各种海况条件。同时,海洋平台钢板长期处于潮湿、高盐度的海洋环境中,受到潮湿空气、海水、海洋生物附着而造成漆膜脱落、钢板表面腐蚀、腐蚀疲劳等问题,严重影响使用寿命。为了使海洋工程平台能够在极地等复杂环境下安全使用,急需开发出高品质的海洋工程用超高强钢,这种钢板必须具有高强度、超低温韧性、抗疲劳、易焊接、耐海洋环境腐蚀以及耐海洋生物附着等优点。With the development of science and technology and the improvement of people's living standards, countries around the world have begun to focus on the vast resources in the ocean. Due to the rapid development of the offshore equipment industry, the market demand for high-strength, extra-thick, ultra-low temperature tough offshore steel plates has continued to increase. Traditional oil and gas energy is becoming increasingly depleted, so the reserves of oil, natural gas and liquefied natural gas in the Arctic region are becoming more and more valuable. Under the influence of the global greenhouse effect, the Arctic is warming up and the sea ice coverage area is decreasing, which has promoted resource development and ship navigation. Russia and Nordic countries have significantly accelerated the exploration and development of oil and gas in the Arctic, and promoted the demand and development of large-scale high-tech polar offshore equipment. Therefore, high-strength polar low-temperature offshore steel has gradually become a development trend. The service environment of offshore engineering platforms is harsh, so it is necessary to consider the influence of multiple factors, and the material selection must be able to adapt to various sea conditions. At the same time, the offshore platform steel plates are in a humid and high-salinity marine environment for a long time, and are affected by humid air, seawater, and marine organisms. The adhesion causes problems such as paint film shedding, steel plate surface corrosion, and corrosion fatigue, which seriously affects the service life. In order to enable offshore engineering platforms to be used safely in complex environments such as the polar regions, it is urgent to develop high-quality ultra-high-strength steel for offshore engineering. This steel plate must have the advantages of high strength, ultra-low temperature toughness, fatigue resistance, easy welding, resistance to marine environmental corrosion, and resistance to marine biological attachment.
目前,海洋工程用钢已能满足海工领域市场的大部分需求,但更低韧脆转变温度的综合性能优良的超高强度特殊钢材仍是世界各国的发展的目标,高服役安全性的高强钢板其科研问题难度高,生产工艺严格,对设备要求高,开发难度大。专利CN115786813A的公开了一种抗拉强度3000MPa的低温钢板,该钢板成分中加入了大量的Ni、Co、Mo配合微量Zr、Ce元素,虽然有助于提高钢质纯净度,成本也大幅度提高,且该成分需要经过热轧、冷轧以及时效处理,钢厂钢板厚度仅为0.5-2mm,无法生产最大厚度100mm、适用于极寒深海环境的千兆帕级低温海工钢。专利CN114622145A公开了一种双相结构马氏体时效钢,采用无C,无Si、Mn等合金元素的成分设计,只能通过电弧炉冶炼加冷轧工艺轧制生产,这种成分和工艺无法生产最大厚度100mm钢板,且低温韧性较差。At present, marine engineering steel can meet most of the needs of the marine engineering market, but ultra-high strength special steel with excellent comprehensive performance and lower ductile-brittle transition temperature is still the development goal of countries around the world. High-strength steel plates with high service safety have high scientific research difficulties, strict production processes, high equipment requirements, and great development difficulties. Patent CN115786813A discloses a low-temperature steel plate with a tensile strength of 3000MPa. A large amount of Ni, Co, and Mo combined with trace Zr and Ce elements are added to the steel plate composition. Although it helps to improve the purity of the steel, the cost is greatly increased. In addition, the composition needs to be hot-rolled, cold-rolled, and aging-treated. The thickness of the steel plate in the steel plant is only 0.5-2mm, and it is impossible to produce a maximum thickness of 100mm for the gigapascal low-temperature marine steel suitable for extremely cold deep-sea environments. Patent CN114622145A discloses a dual-phase maraging steel, which is designed to be free of C, Si, Mn and other alloying elements and can only be produced by electric arc furnace smelting and cold rolling. This composition and process cannot produce steel plates with a maximum thickness of 100 mm, and has poor low-temperature toughness.
发明内容Summary of the invention
本发明的目的是提供一种极寒超深环境用千兆帕级海工钢板及其制造方法,通过合金元素筛选与配比、冶炼、电渣重熔、锻造开坯、两阶段控制轧制以及多次调质热处理工艺的优化与参数选择,制得的钢板低温韧性优良、1000MPa超高强度,其力学性能、高服役安全性能能够达到海洋工程设备服役条件,适用于极寒超深环境。The purpose of the present invention is to provide a gigapascal marine engineering steel plate for extremely cold and ultra-deep environments and a method for manufacturing the same. Through the optimization and parameter selection of alloy element screening and proportioning, smelting, electroslag remelting, forging and blanking, two-stage controlled rolling and multiple tempering heat treatment processes, the obtained steel plate has excellent low-temperature toughness and 1000MPa ultra-high strength. Its mechanical properties and high service safety performance can meet the service conditions of marine engineering equipment and is suitable for extremely cold and ultra-deep environments.
为了实现上述目的,本发明的技术方案如下:In order to achieve the above object, the technical solution of the present invention is as follows:
本发明一方面提供一种极寒超深环境用千兆帕级海工钢板,所述钢板按重量百分比计,包括以下组分:In one aspect, the present invention provides a Gigapascal marine steel plate for use in extremely cold and ultra-deep environments, wherein the steel plate comprises the following components by weight percentage:
C:0.08%-0.15%,Si:0.15%-0.45%,Mn:0.6%-1.15%,P≤0.02%,S≤0.01%,Als:0.005%-0.05%,Ni:7.2%-14%,Cr:0.46%-0.64%,Mo:0.55%-0.79%,Cu:0.42%-0.76%,Co:0.1%-10.0%,V:0.11%-0.23%,Ti:0.01%-0.5%,N:0.003%-0.007%,其余为Fe和不可避免的杂质。C: 0.08%-0.15%, Si: 0.15%-0.45%, Mn: 0.6%-1.15%, P≤0.02%, S≤0.01%, Als: 0.005%-0.05%, Ni: 7.2%-14%, Cr: 0.46%-0.64%, Mo: 0.55%-0.79%, Cu: 0.42%-0.76%, Co: 0.1%-10.0%, V: 0.11%-0.23%, Ti: 0.01%-0.5%, N: 0.003%-0.007%, and the rest are Fe and unavoidable impurities.
采用上述成分设计理由如下:The reasons for adopting the above-mentioned components are as follows:
C作为钢中的最有效的强化元素,增加钢板强度和硬度。C元素可以固溶与Fe基体,也可以与合金元素形成碳化物,起到显著的晶粒细化作用,钢中C元素低于0.08%时钢板强度不足;而C高于0.15%时会产生大量淬硬组织,韧性和抗疲劳性能降低。因此应精确控制C元素在钢中含量,不影响其冲击韧性和抗疲劳性能。C含量为0.08%-0.15%。C is the most effective strengthening element in steel, increasing the strength and hardness of steel plates. C can be dissolved in the Fe matrix, or it can form carbides with alloy elements, playing a significant role in grain refinement. When the C content in steel is less than 0.08%, the strength of the steel plate is insufficient; when the C content is higher than 0.15%, a large amount of hardened structure will be produced, and the toughness and fatigue resistance will be reduced. Therefore, the content of C in steel should be precisely controlled without affecting its impact toughness and fatigue resistance. The C content is 0.08%-0.15%.
Si可提高钢板的强度,同时作为脱氧剂可减少O含量,在本发明中加入的Si含量可以帮助钢板的疲劳极限和疲劳寿命。当Si含量低于0.15%时,脱氧效果不太明显,钢中夹杂物含量高;而当Si含量大于0.45%时,会导致组织粗化,韧性降低。因此,为了保证钢板的强度和抗疲劳性能,在本发明方案中应控制Si含量在0.15%-0.45%。Si can improve the strength of the steel plate, and as a deoxidizer, it can reduce the O content. The Si content added in the present invention can help the fatigue limit and fatigue life of the steel plate. When the Si content is lower than 0.15%, the deoxidation effect is not obvious, and the inclusion content in the steel is high; and when the Si content is greater than 0.45%, it will cause the structure to coarsen and the toughness to decrease. Therefore, in order to ensure the strength and fatigue resistance of the steel plate, the Si content should be controlled at 0.15%-0.45% in the scheme of the present invention.
Mn元素可大量固溶于Fe基体中,提高钢板强度。Mn含量低于0.6%时对钢板无法有效提高钢板强度,Mn含量大于1.15%时,Mn元素会在炼钢凝固过程中向坯料芯部偏聚,降低厚板芯部的低温韧性,Mn含量为0.6%-1.15%。Mn can be dissolved in Fe matrix in large quantities to improve the strength of steel plate. When the Mn content is lower than 0.6%, it cannot effectively improve the strength of steel plate. When the Mn content is higher than 1.15%, the Mn element will concentrate towards the core of the billet during steelmaking solidification, reducing the low-temperature toughness of the core of the thick plate. The Mn content is 0.6%-1.15%.
P、S元素对钢板的力学性能特别是抗疲劳性能没有益处,应控制P≤0.02%,S≤0.01%。P and S elements have no benefit to the mechanical properties of steel plates, especially fatigue resistance. P should be controlled to be ≤ 0.02% and S ≤ 0.01%.
Al是钢中主要的脱氧元素,当Al含量过低时脱氧效果不佳,V、Ti等微合金元素因被氧化无法有效细化晶粒提高抗疲劳性能,超高强度钢板需要适当提高钢中Als含量;然而Al元素过高则形成大型夹杂物,Als含量为0.005%-0.05%。Al is the main deoxidizing element in steel. When the Al content is too low, the deoxidation effect is poor. Micro-alloying elements such as V and Ti cannot effectively refine the grains and improve fatigue resistance due to oxidation. Ultra-high strength steel plates need to appropriately increase the Als content in the steel; however, if the Al content is too high, large inclusions will be formed. The Als content is 0.005%-0.05%.
Ni的作用是改善钢板韧性,提高钢板抗疲劳性能。大量加入可以获得较低的韧脆转变温度,提高钢板低温韧性的同时提高抗疲劳性能,Ni含量为7.2%-14.0%。The role of Ni is to improve the toughness of the steel plate and improve the fatigue resistance of the steel plate. Adding a large amount of Ni can obtain a lower ductile-brittle transition temperature, improve the low-temperature toughness of the steel plate and improve the fatigue resistance. The Ni content is 7.2%-14.0%.
Cr元素在钢中可以有效的提高钢板强度;但是Cr含量过高会降低钢板冲击韧性,Cr与钢中Ni配合,可以有效提升钢板抗疲劳性能,Cr含量为0.46%-0.64%。The Cr element in steel can effectively improve the strength of the steel plate; however, too high a Cr content will reduce the impact toughness of the steel plate. Cr combined with Ni in steel can effectively improve the fatigue resistance of the steel plate. The Cr content is 0.46%-0.64%.
Mo元素在钢中可以形成细小碳化物,提高钢板强度,从而提高钢板疲劳性能。钢中加入一定Mo元素可以提高特厚钢板的淬透性,提高特厚钢板热处理效果。Mo元素还能配合Ni起到一定的耐蚀作用,Mo含量为0.55%-0.79%。Mo can form fine carbides in steel, improve the strength of steel plates, and thus improve the fatigue performance of steel plates. Adding a certain amount of Mo to steel can improve the hardenability of extra-thick steel plates and improve the heat treatment effect of extra-thick steel plates. Mo can also play a certain role in corrosion resistance in combination with Ni, and the Mo content is 0.55%-0.79%.
Co元素在钢中的作用主要是提高钢的强度和耐磨性。Co还能够提高钢的强度和韧性,并且改善钢的加工性能和焊接性能,通过Co降低基体的堆垛层错能和抑制马氏体中位错亚结构的回复,促进碳化物的形核和析出,从而提高钢的强度和抗疲劳性能。Co可以与C、Cr等元素形成高温下稳定的碳化物和硬质合金,从而提高钢的抗氧化、耐腐蚀和耐磨性能。但是,Co的添加量不能过高,否则会导致合金钢的冷脆性增大,韧性降低。因此,Co含量为0.1%-10.0%。The main function of Co in steel is to improve the strength and wear resistance of steel. Co can also improve the strength and toughness of steel, and improve the processing performance and welding performance of steel. Co reduces the stacking fault energy of the matrix and inhibits the recovery of dislocation substructure in martensite, promotes the nucleation and precipitation of carbides, thereby improving the strength and fatigue resistance of steel. Co can form carbides and hard alloys that are stable at high temperatures with elements such as C and Cr, thereby improving the oxidation resistance, corrosion resistance and wear resistance of steel. However, the addition amount of Co cannot be too high, otherwise it will increase the cold brittleness of the alloy steel and reduce the toughness. Therefore, the Co content is 0.1%-10.0%.
Cu元素在钢中可以提高钢板的强度,Cu元素可以在钢中与Ni元素共同作用,降低钢板韧脆转变温度。单独加入过量的Cu元素造成热脆性。Cu元素含量为0.42%-0.76%。Cu element can improve the strength of steel plate in steel, and Cu element can work together with Ni element in steel to reduce the tough-brittle transition temperature of steel plate. Adding excessive Cu element alone will cause hot brittleness. The Cu element content is 0.42%-0.76%.
V元素可以在冶炼过程中形成V(C,N)粒子,起到细化晶粒的作用。钢板中加入V元素可显著提高钢板强度和低温韧性。同时V元素可以有效提升钢板可焊性,V含量为0.11%-0.23%。V element can form V (C, N) particles during the smelting process, which plays a role in refining grains. Adding V element to steel plate can significantly improve the strength and low-temperature toughness of steel plate. At the same time, V element can effectively improve the weldability of steel plate, and the V content is 0.11%-0.23%.
Ti元素与N形成TiN,阻止钢坯在加热、轧制过程中晶粒的长大,改善钢板抗疲劳性能。大量的Ti元素可以与Ni元素形成稳定的金属间相,但是Ti的含量过高将导致钢的裂纹敏感性增加,提高钢的脆性破断倾向。故在本发明中Ti含量为0.01%-0.5%。Ti and N form TiN, which prevents the growth of grains during heating and rolling of the steel billet and improves the fatigue resistance of the steel plate. A large amount of Ti can form a stable intermetallic phase with Ni, but too high a Ti content will increase the crack sensitivity of the steel and increase the brittle fracture tendency of the steel. Therefore, in the present invention, the Ti content is 0.01%-0.5%.
N元素可以与Ti、V元素配合,形成细小弥散的N化物,可以有效促进晶内铁素体形核长达,有效控制原始奥氏体晶粒长大。N含量增高可使钢中的TiN增多。但是当固溶N含量过大时,钢板表面易出现大量微裂纹。因此,N含量为0.003%-0.007%。The N element can cooperate with the Ti and V elements to form fine dispersed N compounds, which can effectively promote the nucleation of ferrite in the grain and effectively control the growth of the original austenite grains. The increase of N content can increase the TiN in the steel. However, when the solid solution N content is too high, a large number of micro cracks are prone to appear on the surface of the steel plate. Therefore, the N content is 0.003%-0.007%.
上述技术方案中,进一步地,所述钢板屈服强度≥1000MPa,抗拉强度1050-1200MPa,横向延伸率≥11%,-80℃夏比冲击功≥90J,-196℃夏比冲击功≥60J。In the above technical solution, further, the steel plate has a yield strength ≥1000MPa, a tensile strength of 1050-1200MPa, a transverse elongation ≥11%, a Charpy impact energy at -80°C ≥90J, and a Charpy impact energy at -196°C ≥60J.
本发明另一方面提供一种上述极寒超深环境用千兆帕级海工钢板的制造方法,所述方法包括以下步骤:Another aspect of the present invention provides a method for manufacturing the above-mentioned GPa-grade offshore steel plate for extremely cold and ultra-deep environments, the method comprising the following steps:
(1)冶炼(1) Smelting
将钢水通过转炉、LF炉、RH或VD炉进行精炼,采用模铸或连铸的方式将钢水浇铸成钢坯;The molten steel is refined through a converter, LF furnace, RH or VD furnace, and the molten steel is cast into steel billets by die casting or continuous casting;
(2)电渣重熔(2) Electroslag remelting
以钢坯作为熔化电极进行电渣重熔,制备电渣坯,电渣坯下线进行1050±50℃均质化退火,堆垛缓冷≥72h;The steel billet is used as a melting electrode for electroslag remelting to prepare electroslag billets, which are then homogenized at 1050±50℃ and stacked for slow cooling for ≥72h.
(3)锻造开坯(3) Forging
将堆垛缓冷后的电渣坯进行锻造开坯,锻造加热温度1220-1280℃,终锻温度≥950℃,得到锻造坯;The electroslag billet after slow cooling is forged, the forging heating temperature is 1220-1280°C, and the final forging temperature is ≥950°C to obtain a forging billet;
(4)两阶段控制轧制(4) Two-stage controlled rolling
将锻造坯装入加热炉加热,加热后进行两阶段控制轧制,一阶段开轧温度为1000-1230℃,终轧温度900-1050℃,中间坯厚度100-200mm,二阶段开轧温度750-900℃,终轧温度700-800℃;The forging billet is loaded into a heating furnace for heating, and then subjected to two-stage controlled rolling. The first-stage rolling temperature is 1000-1230°C, the final rolling temperature is 900-1050°C, the intermediate billet thickness is 100-200mm, the second-stage rolling temperature is 750-900°C, and the final rolling temperature is 700-800°C.
(5)调质热处理(5) Quenching and tempering heat treatment
一次淬火温度700-900℃,加热时间1.4-2.5min/mm,二次淬火温度700-900℃,加热时间1.4-2.5min/mm,回火温度300-600℃,回火时间2-4min/mm。The primary quenching temperature is 700-900℃, the heating time is 1.4-2.5min/mm, the secondary quenching temperature is 700-900℃, the heating time is 1.4-2.5min/mm, the tempering temperature is 300-600℃, and the tempering time is 2-4min/mm.
上述技术方案中,进一步地,步骤(3)中,锻造坯的厚度与成品钢板的厚度比≥3.5。In the above technical solution, further, in step (3), the ratio of the thickness of the forged billet to the thickness of the finished steel plate is ≥3.5.
上述技术方案中,进一步地,步骤(3)中,锻造开坯的单道次压下量≤30mm。In the above technical solution, further, in step (3), the single pass reduction of forging is ≤30 mm.
上述技术方案中,进一步地,步骤(4)中,加热总时间为5.5-9小时,均热温度为1220-1280℃,均热保温时间为1-3小时。In the above technical solution, further, in step (4), the total heating time is 5.5-9 hours, the aquaporin temperature is 1220-1280°C, and the aquaporin insulation time is 1-3 hours.
上述技术方案中,进一步地,步骤(4)中,一阶段轧制的平均道次压下率为13-20%,二阶段轧制的平均道次压下率5-10%。In the above technical solution, further, in step (4), the average pass reduction rate of the first stage rolling is 13-20%, and the average pass reduction rate of the second stage rolling is 5-10%.
本发明的有益效果为:The beneficial effects of the present invention are:
1. 本发明结合C、Mn、Ni、Cr、Mo、Cu、Co、V、Ti等元素相配合成分设计和极寒超深环境用千兆帕级海工钢板关键生产技术,可以生产最大厚度100mm的超高强度1000MPa海工钢。1. The present invention combines the coordinated composition design of elements such as C, Mn, Ni, Cr, Mo, Cu, Co, V, Ti and the key production technology of gigapascal-grade marine steel plates for extremely cold and ultra-deep environments, and can produce ultra-high strength 1000MPa marine steel with a maximum thickness of 100mm.
2. 本发明通过合金元素筛选与配比、钢质洁净度控制、电渣重熔、锻造开坯、两阶段控制轧制以及多次调质热处理工艺的优化与参数选择,制得的钢板其屈服强度≥1000MPa,抗拉强度1050-1200MPa,横向延伸率≥11%,-80℃夏比冲击功≥90J,-196℃夏比冲击功≥60J,疲劳应力与屈服强度比≤0.9的应力循环下,疲劳循环≥107次。2. The present invention optimizes and selects parameters of alloy element screening and proportioning, steel cleanliness control, electroslag remelting, forging blanking, two-stage controlled rolling and multiple quenching and tempering heat treatment processes to obtain a steel plate with a yield strength ≥1000MPa, a tensile strength of 1050-1200MPa, a lateral elongation ≥11%, a Charpy impact energy of ≥90J at -80°C, a Charpy impact energy of ≥60J at -196°C, and a fatigue cycle of ≥10 7 times under a stress cycle with a fatigue stress to yield strength ratio of ≤0.9.
附图说明BRIEF DESCRIPTION OF THE DRAWINGS
图1为实施例1的钢板室温下的组织。FIG1 shows the structure of the steel plate of Example 1 at room temperature.
具体实施方式DETAILED DESCRIPTION
以下实施例可以使本领域的普通技术人员更全面地理解本发明,但不以任何方式限制本发明。The following examples may enable those skilled in the art to more fully understand the present invention, but are not intended to limit the present invention in any way.
如无特别说明,本发明的实施例中所用的材料均可通过商业途径得到或按照本领域技术人员熟知的常规方法制备即可。Unless otherwise specified, the materials used in the embodiments of the present invention can be obtained through commercial channels or prepared according to conventional methods well known to those skilled in the art.
实施例1-40Embodiment 1-40
本发明实施例1-40钢板的化学成分见表1。The chemical compositions of the steel plates of Examples 1-40 of the present invention are shown in Table 1.
表1 实施例1-40钢板化学成分(wt%)Table 1 Chemical composition of steel plates of Examples 1-40 (wt%)
上述极寒超深环境用千兆帕级海工钢板的制造方法,具体包括以下步骤:The manufacturing method of the above-mentioned Gigapascal marine steel plate for extremely cold and ultra-deep environment specifically comprises the following steps:
(1)冶炼(1) Smelting
将钢水通过转炉、LF炉、RH或VD炉进行精炼,通过控制钢质洁净度进一步降低P、S和非金属夹杂物含量,采用模铸或连铸的方式将钢水浇铸成钢坯,全程保护浇铸;The molten steel is refined through a converter, LF furnace, RH or VD furnace, and the content of P, S and non-metallic inclusions is further reduced by controlling the cleanliness of the steel. The molten steel is cast into billets by die casting or continuous casting, and the casting is protected throughout the whole process;
(2)电渣重熔(2) Electroslag remelting
以钢坯作为熔化电极进行电渣重熔,制备电渣坯,电渣坯下线进行1050±50℃均质化退火,堆垛缓冷≥72h;采用电渣坯轧制钢板的原因是电渣坯组织均匀致密,芯部偏析较小,能够保证轧制后的特厚钢板低温冲击韧性,电渣后的电渣坯进行均质化退火和堆垛缓冷可以进一步避免电渣坯冷却过程中造成的内应力过大及组织不均匀现象;The steel billet is used as a melting electrode for electroslag remelting to prepare an electroslag billet, which is then subjected to homogenization annealing at 1050±50℃ and stacking slow cooling for ≥72h. The reason for using electroslag billets to roll steel plates is that the electroslag billets have a uniform and dense structure and a small core segregation, which can ensure the low-temperature impact toughness of the extra-thick steel plates after rolling. The homogenization annealing and stacking slow cooling of the electroslag billets after electroslag can further avoid excessive internal stress and uneven structure caused by the cooling process of the electroslag billets.
(3)锻造开坯(3) Forging
将堆垛缓冷后的电渣坯进行锻造开坯,锻造加热温度1220-1280℃,锻造开坯的单道次压下量≤30mm,终锻温度≥950℃,得到锻造坯,锻造坯的厚度与成品钢板的厚度比≥3.5;采用锻造开坯的目的是利用锻造多方向压下变形最大限度的破碎钢锭芯部大尺寸微观组织,为轧制钢板做好组织准备,进一步提升成品钢板芯部低温韧性,控制单道次锻造压下量的目的是避免钢锭表面出现裂纹;The electroslag billet after slow cooling of the stack is forged, the forging heating temperature is 1220-1280℃, the single pass reduction of forging is ≤30mm, the final forging temperature is ≥950℃, and the forging billet is obtained, and the ratio of the thickness of the forging billet to the thickness of the finished steel plate is ≥3.5; the purpose of forging is to use the multi-directional forging reduction deformation to break the large-scale microstructure of the core of the steel ingot to the maximum extent, prepare the organization for the rolled steel plate, and further improve the low-temperature toughness of the core of the finished steel plate. The purpose of controlling the single pass forging reduction is to avoid cracks on the surface of the steel ingot;
(4)两阶段控制轧制(4) Two-stage controlled rolling
将锻造坯装入加热炉加热,加热总时间为5.5-9小时,均热温度为1220-1280℃,均热保温时间为1-3小时,保证加热的总时间的目的是使大厚度电渣坯芯部到达目标温度,避免均热温度过高,控制均热保温时间的目的是防止坯料奥氏体组织异常长大,影响轧制钢板低温韧性;加热后进行两阶段控制轧制,一阶段开轧温度为1000-1230℃,平均道次压下率为13-20%,终轧温度900-1050℃,中间坯厚度100-200mm,二阶段开轧温度750-900℃,平均道次压下率5-10%,终轧温度700-800℃;一阶段轧制的目的是在相对高温钢板硬度较低的条件下,最大限度的增大道次压下率,进一步破碎坯料铸态晶粒,增加形变储能和晶粒形核点位,100-200mm的中间坯厚度可以保证低温段轧制有足够的形变量,相对较低的二阶段轧制温度保证钢板在调质处理过程中有大量的形变储能,保证钢板性能;The forging billet is loaded into a heating furnace for heating. The total heating time is 5.5-9 hours, the soaking temperature is 1220-1280℃, and the soaking and holding time is 1-3 hours. The purpose of ensuring the total heating time is to make the core of the thick electroslag billet reach the target temperature and avoid excessive soaking temperature. The purpose of controlling the soaking and holding time is to prevent the abnormal growth of the austenite structure of the billet and affect the low-temperature toughness of the rolled steel plate; after heating, two-stage controlled rolling is carried out. The first stage has a starting rolling temperature of 1000-1230℃, an average pass reduction rate of 13-20%, a final rolling temperature of 900-1050℃, and a second stage has a rolling temperature of 1000-1230℃, an average pass reduction rate of 13-20%, and a final rolling temperature of 900-1050℃. The thickness of the intermediate billet is 100-200mm, the second-stage rolling temperature is 750-900℃, the average pass reduction rate is 5-10%, and the final rolling temperature is 700-800℃; the purpose of the first-stage rolling is to maximize the pass reduction rate under the condition of relatively low hardness of the high-temperature steel plate, further crush the cast grains of the billet, increase the deformation energy storage and grain nucleation points, the 100-200mm intermediate billet thickness can ensure sufficient deformation in the low-temperature rolling, and the relatively low second-stage rolling temperature ensures that the steel plate has a large amount of deformation energy storage during the quenching and tempering process, ensuring the performance of the steel plate;
(5)调质热处理(5) Quenching and tempering heat treatment
一次淬火温度700-900℃,加热时间1.4-2.5min/mm,二次淬火温度700-900℃,加热时间1.4-2.5min/mm,回火温度300-600℃,回火时间2-4min/mm;调质工艺是钢板制造过程中非常关键的一环,能够有效地影响钢板的性能表现,特别是对于钢板的低温韧性和抗疲劳性能有着至关重要的影响;在两次淬火过程中,高温淬火的主要目的是使钢板充分奥氏体化,并确保钢板奥氏体不过热也不欠热,在保证不开裂变形的前提下,提高冷却能力,加快组织转变,使组织大量转变为马氏体,增加淬硬组织,由于高温淬火可以得到更为均匀的奥氏体组织,从而提高了钢板的强度和硬度,因此具备了很好的抗疲劳拉断性能。在回火阶段,高温回火可以在调整基体组织的同时调整析出第二相的质量,从而优化钢板的组织结构,提高钢板的韧性;同时,在亚温淬火工艺中,可以通过形成残余奥氏体,提高钢板的低温韧性;最后,在充分回火的过程中,由于温度和时间充分的回火可以保证回火转变产物尽可能的转变,降低钢板的强度和硬度的同时,韧塑性得到提高。The primary quenching temperature is 700-900℃, the heating time is 1.4-2.5min/mm, the secondary quenching temperature is 700-900℃, the heating time is 1.4-2.5min/mm, the tempering temperature is 300-600℃, and the tempering time is 2-4min/mm; the quenching and tempering process is a very critical link in the steel plate manufacturing process, which can effectively affect the performance of the steel plate, especially the low-temperature toughness and fatigue resistance of the steel plate. In the two quenching processes, the main purpose of high-temperature quenching is to make the steel plate fully austenitized and ensure that the austenite of the steel plate is neither overheated nor underheated. Under the premise of ensuring no cracking and deformation, the cooling capacity is improved, the organizational transformation is accelerated, and the organization is transformed into martensite in large quantities to increase the hardened organization. Since high-temperature quenching can obtain a more uniform austenite organization, the strength and hardness of the steel plate are improved, so it has a good fatigue resistance and tensile strength. During the tempering stage, high-temperature tempering can adjust the quality of the precipitated second phase while adjusting the matrix structure, thereby optimizing the organizational structure of the steel plate and improving the toughness of the steel plate; at the same time, in the sub-temperature quenching process, the low-temperature toughness of the steel plate can be improved by forming residual austenite; finally, in the process of full tempering, due to the sufficient temperature and time of tempering, the tempering transformation products can be transformed as much as possible, reducing the strength and hardness of the steel plate while improving the toughness and plasticity.
电渣重熔、锻造开坯的工艺参数如表2所示,两阶段控制轧制的工艺参数如表3所示,调质热处理的工艺参数如表4所示。The process parameters of electroslag remelting and forging are shown in Table 2, the process parameters of two-stage controlled rolling are shown in Table 3, and the process parameters of quenching and tempering heat treatment are shown in Table 4.
表2 电渣重熔、锻造开坯的工艺参数Table 2 Process parameters of electroslag remelting and forging
表3 两阶段控制轧制的工艺参数Table 3 Process parameters of two-stage controlled rolling
表4 调质热处理的工艺参数Table 4 Process parameters of quenching and tempering heat treatment
实施例1-40钢板的拉伸及冲击性能见表5,疲劳性能见表6,金相组织含量及尺寸见表7。The tensile and impact properties of the steel plates of Examples 1-40 are shown in Table 5, the fatigue properties are shown in Table 6, and the metallographic structure content and dimensions are shown in Table 7.
表5 实施例1-40钢板力学性能Table 5 Mechanical properties of steel plates of Examples 1-40
表6 实施例1-40钢板疲劳性能Table 6 Fatigue properties of steel plates of Examples 1-40
表7 实施例1-40钢板金相组织含量及尺寸Table 7 Metallographic structure content and size of steel plate of Example 1-40
实施例1制得的钢板室温下的组织如图1所示,可以发现实验钢在室温下的基体组织为回火索氏体和铁素体。由表7可以看出,本发明制得的钢板回火索氏体组织与铁素体组织大多介于3-6μm之间,尺寸较小且均匀分布。此外组织中含有大量的残余奥氏体,其含量处于10.5%-16.8%之间。残余奥氏体的形貌主要为薄膜状及块状(马奥岛),稳定性较高的薄膜状残余奥氏体占残余奥氏体的绝大部分;稳定性较低的块状残余奥氏体含量较低,晶粒尺寸大多介于1-2μm之间。The structure of the steel plate obtained in Example 1 at room temperature is shown in Figure 1. It can be found that the matrix structure of the experimental steel at room temperature is tempered troostite and ferrite. It can be seen from Table 7 that the tempered troostite structure and ferrite structure of the steel plate obtained by the present invention are mostly between 3-6μm, small in size and evenly distributed. In addition, the structure contains a large amount of residual austenite, and its content is between 10.5% and 16.8%. The morphology of the residual austenite is mainly film-like and block-like (Mao Island), and the film-like residual austenite with higher stability accounts for the vast majority of the residual austenite; the content of the blocky residual austenite with lower stability is low, and the grain size is mostly between 1-2μm.
以上实施例仅仅是本发明的优选施例,并非对于实施方式的限定。本发明的保护范围应当以权利要求所限定的范围为准。在上述说明的基础上还可以做出其它不同形式的变化或变动。由此所引伸出的显而易见的变化或变动仍处于本发明创造的保护范围之中。The above embodiments are only preferred embodiments of the present invention and are not intended to limit the implementation methods. The protection scope of the present invention shall be subject to the scope defined in the claims. Other different forms of changes or modifications may be made based on the above description. Obvious changes or modifications derived therefrom are still within the protection scope of the present invention.
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