WO2021115263A1 - 一种基于异型坯轧制成型的热轧h型钢及其制备方法 - Google Patents

一种基于异型坯轧制成型的热轧h型钢及其制备方法 Download PDF

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WO2021115263A1
WO2021115263A1 PCT/CN2020/134563 CN2020134563W WO2021115263A1 WO 2021115263 A1 WO2021115263 A1 WO 2021115263A1 CN 2020134563 W CN2020134563 W CN 2020134563W WO 2021115263 A1 WO2021115263 A1 WO 2021115263A1
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rolling
cooling
controlled
temperature
rolled
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PCT/CN2020/134563
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French (fr)
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赵培林
王中学
王建军
韩文习
魏承志
马强
卢波
李超
吴会亮
路峰
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山东钢铁股份有限公司
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Priority to EP20899696.7A priority Critical patent/EP4074858A4/en
Priority to JP2022533226A priority patent/JP2023505172A/ja
Priority to KR1020227017370A priority patent/KR20220085820A/ko
Publication of WO2021115263A1 publication Critical patent/WO2021115263A1/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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/08—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling structural sections, i.e. work of special cross-section, e.g. angle steel
    • B21B1/088—H- or I-sections
    • 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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/221—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by cold-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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention belongs to the field of metallurgical technology. Specifically, the present invention relates to a hot-rolled H-shaped steel based on the rolling and forming of a profiled blank and a preparation method thereof. According to the preparation process and molding method.
  • the hot-rolled H-beam steel that must be used in the construction of the platform not only increases in demand, but also puts forward higher requirements for toughness under low-temperature environments.
  • the requirements for impact toughness of hot-rolled H-beams currently used at home and abroad are mainly for the longitudinal impact detected along the rolling direction. Due to the complex shape of the H-beam, the structure changes are complex, and the structure of the flange along the transverse position is quite different, and there is generally no specific requirement for the transverse impact.
  • the platform structure is more complex, combined with the changes in the conditions of use, the index of lateral impact toughness is gradually put forward higher requirements, and the use of profiles with good lateral impact toughness is promoted in some standards and projects.
  • Patent CN103556055B discloses a hot-rolled H-section steel used in the structure of an offshore natural gas mining platform and a production method thereof.
  • One aspect of the present invention provides a hot-rolled H-section steel used in the structure of the marine natural gas mining platform.
  • the composition of the hot-rolled H-section steel Calculated by weight percentage: C: 0.10 ⁇ 0.17, Si: 0.10 ⁇ 0.40, Mn: 1.00 ⁇ 1.60, P ⁇ 0.025, S ⁇ 0.015, Nb: 0.02 ⁇ 0.05, Ti ⁇ 0.025, the rest is iron and unavoidable impurities .
  • the mechanical properties, -20°C transverse and longitudinal impact energy, and surface quality of the hot-rolled H-shaped steel of the marine natural gas mining platform structure related to the invention can fully meet the technical requirements of the H-shaped steel used for the marine natural gas mining platform structure.
  • the invention mainly adopts medium carbon and Nb, Ti composite microalloying composition design. Due to the influence of the Nb, Ti composite microalloying mechanism, the rolling force in the actual rolling process is relatively large, and the requirements for rolling equipment are relatively high.
  • Patent application CN1421286A discloses a rolling method of niobium-containing H-section steel.
  • the method uses the principle of metal physical metallurgy to adjust and optimize the conventional process conditions, adopts controlled rolling in the recrystallization zone and controlled rolling in the unrecrystallized zone, and controls the amount of deformation in a single pass, so that the ferrite nucleates in the deformed zone.
  • the obtained H-shaped steel has a tensile strength of 490-610MPa and a transverse impact energy of 34-98J at -20°C, which meets the requirements of the American Petroleum Institute Platform Design Specification for Type II steel.
  • the invention has harsh control conditions for the deformation temperature and deformation amount, which will also increase the load of the rolling mill; real-time adjustment of the reduction amount is extremely difficult, has a greater impact on product performance, has volatility, and significantly reduces the pass rate of the product.
  • the smelting and rolling process of the H-shaped steel produced by the profile billet needs to be specifically designed to not only meet the smelting demand, reduce the rolling load, and at the same time, the microstructure after rolling meets certain low temperature conditions. Higher transverse impact toughness.
  • the present invention provides a hot-rolled H-shaped steel based on profiled billet rolling and forming and a preparation method thereof.
  • the technical scheme of the present invention is as follows:
  • a method for preparing hot-rolled H-shaped steel based on profiled billet rolling and forming the chemical composition of which is in weight percentage: C: 0.04 ⁇ 0.08; Si: ⁇ 0.25; Mn: 1.25 ⁇ 1.45; V: 0.04 ⁇ 0.10; Ni: 0.2 ⁇ 1.0; P ⁇ 0.02; S ⁇ 0.01; Nb: 0.02 ⁇ 0.06, Al: 0.02 ⁇ 0.06; N ⁇ 0.015; O ⁇ 0.005; the rest are Fe and unavoidable impurities.
  • the preferred chemical composition (wt%) of molten steel is: C: 0.05 ⁇ 0.07; Si: ⁇ 0.25; Mn: 1.25 ⁇ 1.45; V: 0.04 ⁇ 0.06; Ni: 0.2 ⁇ 0.7; P ⁇ 0.02; S ⁇ 0.01 ; Nb: 0.02 ⁇ 0.04, Al: 0.02 ⁇ 0.05; N ⁇ 0.015; O ⁇ 0.005;
  • the production preparation process mainly includes converter smelting, LF refining, continuous casting and hot rolling forming.
  • the steps are as follows:
  • the special-shaped continuous casting billet is heated in a digitally controlled heating furnace and then discharged with high-pressure water for descaling;
  • Rolling Rough rolling adopts water cooling for controlled cooling, and finishing rolling adopts warm rolling and water cooling controlled rolling.
  • the reduction rate of the unrecrystallized zone is greater than 30, preferably 30-45%; the cooling equipment before and after the machine is turned on , Forced cooling of the H-beam lower leg, and the final rolling temperature is controlled at 750°C ⁇ 820°C;
  • the rolled section steel is cooled by air or water and then enters the cooling bed for centralized cooling, so that the carbonitrides are charged and analyzed, and the grain size after rolling is guaranteed to be above 8.5. After the temperature of the section steel is lowered to below 100° C., it is straightened in a straightening machine, and finally the section steel is cut into cut-to-length materials, stacked, and bundled.
  • the heating temperature in the step 2) is controlled at 1220°C to 1260°C, and the heating time is 90 to 180 minutes.
  • the opening temperature of the rough rolling in the step 2) is controlled at 1030°C to 1130°C, and the rolling pass is 5 to 7 passes.
  • the start-up temperature of the finishing rolling is controlled at 900°C to 1000°C; the number of finishing rolling passes is 3 to 5 passes.
  • a water nozzle is used to forcibly cool the H-beam lower leg, and the temperature difference between the upper and lower legs is controlled within the range of ⁇ 10°C; the final rolling temperature is controlled at 780°C to 810°C.
  • the invention adopts low-carbon and V, Nb, Al microalloying process design, combined with section steel pass control rolling, realizes H-section steel products with good transverse impact toughness and low temperature resistance based on special-shaped billet rolling and realizes industrialized production of flange thickness 18mm ⁇ 24mm H-shaped steel products.
  • the preparation method of the H-shaped steel with good lateral impact toughness and low temperature resistance for marine engineering includes converter smelting, LF refining, full protection continuous casting, rough rolling and finishing rolling process and online water cooling control process.
  • the invention adopts low-carbon and V, Nb microalloy controlled rolling process to industrially prepare H-shaped steel products with flange thickness of 18mm-24mm, and refines the matrix structure through Nb controlled recrystallization rolling and temperature control during finishing rolling to obtain a fine and uniform
  • Nb controlled recrystallization rolling and temperature control during finishing rolling to obtain a fine and uniform
  • V relying on V to precipitate nano-scale carbonitrides in the cooling stage to improve the strength of the steel, and ultimately ensure that the hot-rolled H-beam of this specification has good transverse impact toughness.
  • fine-grain strengthening and precipitation strengthening mechanisms it has a composite microalloying composition design that is more suitable for preparing fine-grained structures, so as to obtain a tensile strength of 510MPa and Shanghai industrial hot-rolled H-beam steel;
  • the marine low-temperature resistant H-shaped steel product involved in the present invention has good mechanical properties, with a tensile strength greater than 510MPa, especially -40°C transverse impact energy greater than 34J, -60°C longitudinal impact energy greater than 120J, suitable for use in areas with extreme temperature conditions.
  • Fig. 1 is a microstructure diagram of the flange of the present invention with a thickness of 24 mm.
  • the continuous casting slabs in the following examples are prepared according to the following process flow: according to the set chemical composition range (Table 1), the chemical composition C, Si, Mn, S, P and Fe are used as raw materials for converter smelting and refining , Continuous casting, slab direct heating or soaking.
  • the preparation steps of Examples 1-4 are as follows:
  • the contents of As and Sn in the molten iron into the furnace are both less than 80ppm; the slag must be added 3 minutes before the end.
  • the alkalinity of the final slag is controlled within the range of 2.9 to 3.9.
  • Double-stop slag tapping technology is adopted to control the slag volume of the converter to 55mm.
  • Refining implements the bottom argon blowing stirring and argon blowing system to ensure that the inclusions are fully floated; the refining soft argon blowing is not less than 20 minutes. In order to ensure that the production runs smoothly, 100m of calcium line is fed into the refinery before leaving the station.
  • Continuous casting adopts full protection pouring process; the pulling speed is controlled at 0.7 ⁇ 1.3m/min.
  • Fig. 1 is a microstructure diagram of the flange of the present invention with a thickness of 24 mm. The chemical components and specific processes of Examples 1-4 are shown in the following table.
  • Example 1 0.05 0.25 1.40 0.02 0.006 0.02 0.08 0.25 0.020
  • Example 2 0.06 0.22 1.25 0.019 0.007 0.04 0.07 0.23 0.033
  • Example 3 0.07 0.23 1.45 0.018 0.008 0.04 0.05 0.28 0.028
  • Example 4 0.08 0.20 1.35 0.017 0.005 0.03 0.09 0.35 0.036
  • Example 1-4 The hot rolling process conditions of Examples 1-4 are shown in Table 2.
  • Table 2 According to the standard BS EN ISO 377-1997 "Sampling position and preparation of test specimens for mechanical properties"; the test methods for yield strength, tensile strength and elongation refer to the standard ISO6892-1-2009 "Metallic materials tensile test method at room temperature” ; The impact energy test method refers to the standard ISO 148-1 "Charpy Pendulum Impact Test of Metallic Materials", and the results are shown in Table 2.

Abstract

本发明公开一种基于异型坯轧制成型的热轧H型钢制造方法，其化学成分组成按重量百分比计，为：C：0.04～0.08；Si：≤0.25；Mn：1.25～1.45；V：0.04～0.10；Ni：0.2～1.0；P≤0.02；S≤0.01；Nb：0.02～0.06，Al：0.02～0.06；N≤0.015；O≤0.005；其余为铁Fe和不可避免杂质；所述H型钢上下翼缘屈服强度≥420MPa；-40℃横向冲击功≥34J，-60℃纵向冲击功≥120J。所述H型钢制备方法，包括以下步骤：1)冶炼及连铸工序：采用转炉冶炼、LF精炼并浇铸成异型连铸坯，2)轧制工序：加热；轧制；轧后冷却。本发明所涉及海工用耐低温H型钢产品力学性能良好，易于工业化制备，降低对轧制设备的要求；适合极端气温条件地区使用。

Description

一种基于异型坯轧制成型的热轧H型钢及其制备方法
相关申请的交叉参考
该申请要求2019年12月9日提交的中国专利申请号为2019112501386的专利申请的优先权，该专利申请在此被完全引入作为参考。
技术领域
本发明属于冶金技术领域，具体地，本发明涉及一种基于异型坯轧制成型的热轧H型钢及其制备方法。根据制备工艺和成型方法。
背景技术
随着石油和天然气资源需求增加，海洋石油平台逐渐拓展到复杂气候区域，平台建设质量和要求更加苛刻。因此，建造平台必须使用的热轧H型钢不仅需求量增加，而且对低温环境下的韧性提出更高要求。目前国内外使用的热轧H型钢，对于冲击韧性的要求主要针对沿着轧制方向进行检测的纵向冲击提出要求。由于H型钢形状复杂，组织变化复杂，翼缘沿横向部位组织差别较大，对于横向冲击一般不做具体要求。但是随着工程的发展，平台结构更加复杂，结合使用区域条件的变化，对以横向冲击韧性的指标也逐渐提出更高要求，在部分标准和工程中推广使用具有良好横向冲击韧性的型材。
对于中大规格的H型钢，多采用异型坯轧制成型，另外微合金化在H型钢制备领域的应用，组织保证方面难度更高，众多因素综合一起，最终影响到横向冲击韧性。尤其对于工业化制备而言，稳定性存在一定问题。为保证横向冲击不同专利提供了不同的技术思路。
专利CN103556055B公开了一种用于海洋天然气开采平台结构的热轧H型钢及其生产方法，本发明的一方面提供用于海洋天然气开采平台结构的热轧H型钢，所述热轧H型钢的成分按重量百分比计为：C：0.10～0.17，Si：0.10～0.40，Mn：1.00～1.60，P≤0.025，S≤0.015，Nb：0.02～0.05，Ti≤0.025，其余为铁及不可避免的杂质。本发明涉及到的海洋天然气开采平台结构的热轧H型钢的力学性能、-20℃横向和纵向冲击功、表面质量能够完全满足用于海洋天然气开采平台结构的H型钢的技术要求。本发明中主要采用中碳和Nb，Ti复合微合金化成分设计，由于Nb，Ti复合微合金化机制影响，实际轧制过程中轧制力偏大，对于轧制设备要求较高。
专利申请CN1421286A公开了一种含铌H型钢的轧制方法。该方法利用金属物理冶金学的原理，对常规的工艺条件进行调整和优化，采用再结晶区控轧和未再结晶区控轧，控制单道次变形量，使铁素体在变形带形核得到细小的铁素体晶粒，从而均匀细化金相组织，得到高强度、高韧性、可焊性好的H型钢。所获得的H型钢抗拉强度490～610MPa，-20℃横向冲击功34～98J，满足美国石油协会平台设计规范Ⅱ类钢材的要求。该发明对变形温度和 变形量控制条件苛刻，同样会增加轧机的负荷；实时调整压下量难度巨大，对产品性能影响较大，存在波动性，产品的合格率降低明显。
综上所述，需要针对异型坯轧制成材的H型钢进行冶炼及轧制工艺进行针对性设计，使其不仅满足冶炼需求，降低轧制负荷，同时轧制后组织状态满足一定低温条件下具有较高横向冲击韧性。
发明内容
为了满足不同地域及苛刻复杂环境下海洋石油平台建造的需求，本发明提供一种基于异型坯轧制成型的热轧H型钢及其制备方法。本发明的技术方案如下：
一种基于异型坯轧制成型的热轧H型钢制备方法，其化学成分组成按重量百分比为：C：0.04～0.08；Si：≤0.25；Mn：1.25～1.45；V：0.04～0.10；Ni：0.2～1.0；P≤0.02；S≤0.01；Nb：0.02～0.06，Al：0.02～0.06；N≤0.015；O≤0.005；其余为铁Fe和不可避免杂质。
作为优选，钢水的化学成分优选(wt％)为：C：0.05～0.07；Si：≤0.25；Mn：1.25～1.45；V：0.04～0.06；Ni：0.2～0.7；P≤0.02；S≤0.01；Nb：0.02～0.04，Al：0.02～0.05；N≤0.015；O≤0.005；
生产制备工艺主要包括转炉冶炼，LF精炼，连铸和热轧成型，步骤如下：
1)冶炼及连铸工序：
采用转炉冶炼、LF精炼并浇铸成异型连铸坯，其余为铁及不可避免的杂质；连铸过程中间包液面900mm～950mm，采用全保护浇注工艺；拉速控制在0.7-1.3m/min。
2)轧制工序：
加热：将异型连铸坯在数字化控制加热炉中进行加热出炉后利用高压水进行除鳞；
轧制：粗轧采用水冷进行控制冷却，精轧采用待温轧制和水冷控制轧制，未再结晶区的压下率大于30，优选为30～45％；机前及机后冷却设备开启，对H型钢下腿进行强制冷却，终轧温度控制在750℃～820℃；
冷却：根据规格不同，轧制后型钢分规格经空冷或者水冷后，进入冷床集中冷却，使得碳氮化物充分析出，同时保证轧后晶粒度在8.5级以上。型钢温度降至100℃以下后在矫直机进行矫直，最后将所述型钢切成定尺材、码垛、打捆。
作为优选，所述步骤2)中的加热温度控制在1220℃～1260℃，加热时间为90～180min。
作为优选，所述步骤2)中粗轧的开轧温度控制在1030℃～1130℃，轧制道次为5～7道次。
作为优选，所述步骤2)中精轧的开轧温度控制在900℃～1000℃；精轧轧制道次为3～5道次。
作为优选，所述步骤2)中采用水嘴对H型钢下腿进行强制冷却，上下腿温度差控制在≤10℃范围内；终轧温度控制在780℃～810℃。本发明通过低碳及V和Nb，Al微合金化 工艺设计，结合型钢孔型控制轧制，实现基于异型坯轧制成型具有良好横向冲击韧性耐低温H型钢产品并实现工业化生产制备翼缘厚度18mm～24mm规格H型钢产品。根据本发明实施例，海洋工程用具有良好横向冲击韧性耐低温H型钢制备方法包括转炉冶炼、LF精炼、全保护连铸、粗轧精轧轧制工艺及在线水冷控制工艺。
本发明采用低碳和V，Nb微合金控制轧制工艺工业化制备翼缘厚度18mm～24mm规格H型钢产品，通过Nb控制再结晶轧制配合精轧过程温度控制来细化基体组织，获得细小均匀的铁素体组织，同时依靠V在冷却阶段析出纳米级碳氮化物提高钢的强度，最终保证该规格热轧H型钢具有良好的横向冲击韧性。
本发明未提及的其他工序，均可采用现有技术。
同目前具有横向冲击韧性要求的耐低温H型钢及生产方法比较，本发明技术方案的优点在于：
1.采用细晶强化和沉淀强化机制，具有更加适合制备细晶粒组织的复合微合金化成分设计，从而得到抗拉强度510MPa级别以上海工用热轧H型钢；
2.采用全过程在线控制冷却工艺，结合再结晶和未再结晶区轧制，配合Nb，V，Al，Ni微合金化成分设计，适合制备耐低温热轧H型钢，保证横向冲击韧性良好；
3.与其他专利化学成分设计比较，平均轧制力降低10％～30％，易于工业化制备，降低对轧制设备的要求。
4.本发明所涉及海工用耐低温H型钢产品力学性能良好，抗拉强度大于510MPa，尤其-40℃横向冲击功大于34J，-60℃纵向冲击功大于120J，适合极端气温条件地区使用。
附图说明
图1为本发明翼缘厚度24mm显微组织图。
具体实施方式
以下列举具体实施例对本发明进行说明。需要指出的是，实施例只用于对本发明作进一步说明，不限制本发明的保护范围，其他人根据本发明做出的非本质的修改和调整，仍属于本发明的保护范围。
下述实施例中的连铸坯均按以下工艺流程制备：根据设定的化学成分范围(表1)，以化学成分C，Si，Mn，S，P和Fe为原料，进行转炉冶炼、精炼、连铸、铸坯直接加热或者均热。实施例1-4的制备步骤如下：
1、冶炼：
入炉铁水As，Sn含量均小于80ppm；渣料必须于终点前3分钟加完。终渣碱度控制在2.9～3.9范围内。采用双挡渣出钢工艺，控制转炉下渣量55mm。精炼执行全程底吹氩搅拌 吹氩制度以保证夹杂物充分上浮；精炼软吹氩不小于20分钟。为保证生产顺行，精炼出站前喂入钙线100m。
2、连铸：采用全保护浇注工艺；拉速控制在0.7～1.3m/min。
3、热轧过程轧制及控制冷却：热轧过程轧制及轧后控制冷却以控制温度为主要手段，终轧温度检测翼缘外侧，轧后轧材在冷床进行集中缓冷，使得V的碳氮化物充分析出。图1为本发明翼缘厚度24mm显微组织图。实施例1-4的化学成分及具体工艺见下表。
表1 化学成分(wt％,余量铁)
项目 C Si Mn P S Nb V Ni Al
实施例1 0.05 0.25 1.40 0.02 0.006 0.02 0.08 0.25 0.020
实施例2 0.06 0.22 1.25 0.019 0.007 0.04 0.07 0.23 0.033
实施例3 0.07 0.23 1.45 0.018 0.008 0.04 0.05 0.28 0.028
实施例4 0.08 0.20 1.35 0.017 0.005 0.03 0.09 0.35 0.036
实施例1-4的热轧工艺条件见表2。按照标准为BS EN ISO 377-1997《力学性能试验试样的取样位置和制备》；屈服强度、抗拉强度、延伸率的试验方法参照标准ISO6892-1-2009《金属材料室温拉伸试验方法》；冲击功试验方法参照标准ISO 148-1《金属材料夏比摆锤冲击试验》，结果见表2。
表2 热轧工艺参数及规格
Figure PCTCN2020134563-appb-000001
表中可见，本发明实施例1-4上下翼缘屈服强度均保持420MPa以上，其冲击韧性良好，均满足海洋石油平台海洋工程用构件在极低环境下的使用条件。
表3 力学性能
Figure PCTCN2020134563-appb-000002
Figure PCTCN2020134563-appb-000003
最后所应说明的是，以上实施例仅用以说明本发明的技术方案而非限制。尽管参照实施例对本发明进行了详细说明，本领域的普通技术人员应当理解，对本发明的技术方案进行修改或者等同替换，都不脱离本发明技术方案的精神和范围，其均应涵盖在本发明的权利要求范围当中。

Claims (7)

  1. 一种基于异型坯轧制成型的热轧H型钢，其特征在于，其化学成分组成按重量百分比计，为：C：0.04～0.08；Si：≤0.25；Mn：1.25～1.45；V：0.04～0.10；Ni：0.2～1.0；P≤0.02；S≤0.01；Nb：0.02～0.06，Al：0.02～0.06；N≤0.015；O≤0.005；其余为铁Fe和不可避免杂质；
    所述H型钢翼缘厚度规格18～24mm，上下翼缘屈服强度均≥420MPa；-40℃横向冲击功≥34J，-60℃纵向冲击功≥120J。
  2. 根据权利要求1所述的H型钢，其特征在于，其化学成分组成按重量百分比计，为：C：0.05～0.07；Si：≤0.25；Mn：1.25～1.45；V：0.04～0.06；Ni：0.2～0.7；P≤0.02；S≤0.01；Nb：0.02～0.04，Al：0.02～0.05；N≤0.015；O≤0.005；其余为铁及不可避免的杂质。
  3. 一种基于异型坯轧制成型的热轧H型钢制备方法，包括以下步骤：
    1)冶炼及连铸工序：
    采用转炉冶炼、LF精炼并浇铸成异型连铸坯，连铸过程中间包液面≥900mm，采用全保护浇注工艺；拉速控制在0.7-1.3m/min；
    2)轧制工序：
    加热：将异型连铸坯进行加热，出炉后进行除鳞；
    轧制：粗轧采用水冷进行冷却，精轧采用待温轧制和水冷轧制，未再结晶区的压下率大于30％；机前及机后冷却设备开启，对H型钢下腿进行强制冷却终轧温度控制在750℃～820℃；
    轧后冷却：轧制后型钢经空冷或者水冷，随后进入冷床集中冷却，温度降至100℃以下后在矫直机进行矫直。
  4. 根据权利要求3所述的制备方法，其特征在于，所述步骤2)中的加热温度控制在1220℃～1260℃，加热时间为90～180min。
  5. 根据权利要求3所述的制备方法，其特征在于，所述步骤2)中粗轧的开轧温度控制在1030℃～1130℃，轧制道次为5～7道次。
  6. 根据权利要求3所述的制备方法，其特征在于，所述步骤2)中精轧的开轧温度控制在900℃～1000℃；精轧轧制道次为3～5道次。
  7. 根据权利要求3所述的制备方法，其特征在于，所述步骤2)中采用水嘴对H型钢下腿进行强制冷却，上下腿温度差控制在≤10℃范围内。
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