WO2019218657A1 - 一种屈服强度460MPa级热轧高韧性耐低温H型钢及其制备方法 - Google Patents

一种屈服强度460MPa级热轧高韧性耐低温H型钢及其制备方法 Download PDF

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WO2019218657A1
WO2019218657A1 PCT/CN2018/121100 CN2018121100W WO2019218657A1 WO 2019218657 A1 WO2019218657 A1 WO 2019218657A1 CN 2018121100 W CN2018121100 W CN 2018121100W WO 2019218657 A1 WO2019218657 A1 WO 2019218657A1
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rolling
mpa
steel
temperature
yield strength
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PCT/CN2018/121100
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English (en)
French (fr)
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王中学
赵培林
韩文习
李超
郭伟达
方金林
郭秀辉
武玉利
杨栋
赵传东
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山东钢铁股份有限公司
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Priority to EP18918599.4A priority Critical patent/EP3789508B1/en
Priority to JP2021514462A priority patent/JP7098828B2/ja
Priority to KR1020207032851A priority patent/KR20200143466A/ko
Publication of WO2019218657A1 publication Critical patent/WO2019218657A1/zh

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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
    • 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
    • C22C38/04—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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 belongs to the technical field of metallurgy, in particular, the invention relates to a hot-rolling high-toughness low-temperature resistant H-shaped steel with a yield strength of 460 MPa and a preparation method thereof.
  • the patent application of the application No. CN201310200230.8 discloses a rolling process of a vanadium-containing weathering hot-rolled H-shaped steel having a yield strength of 450 MPa, and the distribution ratio of the vanadium-containing weathering hot-rolled H-shaped steel is (wt%): C: 0.09 to 0.11.
  • the rest are iron and residual trace impurities; the vanadium-containing weathering hot-rolled H-beam adopts two-stage rapid cooling treatment after rolling to achieve the target of yield strength of 450 MPa, and has special requirements for post-rolling cooling equipment. .
  • the patent application of the application No. CN201510044714.7 relates to a low-temperature resistant hot-rolled H-shaped steel and a preparation method thereof, wherein the hot-rolled H-shaped steel has a chemical composition of (wt%): C: 0.07 to 0.10%, Si: 0.2 to 0.4% Mn: 1.30 to 1.60%, P ⁇ 0.020%, S ⁇ 0.015%, V: 0.015 to 0.070%, Ti: 0.010 to 0.030%, and the balance being Fe and unavoidable impurities.
  • Production methods include converter smelting, LF refining, continuous casting, and rolling.
  • the structure of the H-shaped steel prepared by the invention is polygonal ferrite and pearlite structure, and the yield strength is 350-450 MPa.
  • the patented rolling process uses a conventional method, and its chemical composition design makes its post-rolling yield strength close to 450 MPa.
  • the above two high-strength H-shaped steels and preparation techniques adopt micro-alloying and different cooling methods, and have high strength while ensuring a certain low-temperature impact toughness.
  • the requirements for cooling equipment are high, on the other hand, rolling with ordinary equipment, the strength cannot be improved.
  • the object of the present invention is to design a hot-rolling high-toughness low-temperature resistant H-shaped steel with a yield strength of 460 MPa and a preparation method thereof for satisfying the demand for high-strength and high-toughness steel for marine engineering in a complex environment such as extreme cold, and the preparation method thereof It is suitable for the production of support structural parts with high toughness requirements in areas with extremely low temperature conditions (marine engineering).
  • the yield strength of the 460MPa grade high toughness low temperature resistant H-shaped steel of the invention has a chemical composition of C: 0.03% to 0.07%, Si ⁇ 0.3%, Mn: 1.20% to 1.40%, and Nb: 0.015% to 0.030. %, V: 0.10% to 0.15%, Ti: 0.015% to 0.025%, Ni: 0.25% to 0.45%, Cr: 0.30% to 0.50%, A1s: 0.01% to 0.06%, and N: 0.010% to 0.023%, P ⁇ 0.015%, S ⁇ 0.010%, O ⁇ 0.004%, and the balance is Fe and inevitable impurities.
  • the elements of V, Ti and Nb satisfy 0.10% ⁇ V + Ti + Nb ⁇ 0.20%.
  • the H-shaped steel prepared to meet the requirements of the formula can better meet the requirements of precipitation-enhanced microalloying, thereby increasing the strength of the steel.
  • nitrogen plays an important role in the precipitation of microalloyed carbonitrides, especially in steels which are microalloyed with titanium and vanadium.
  • Nitrogen-containing steel not only eliminates the cost increase caused by degassing and refining nitrogen removal during steel making, but also increases nitrogen in the steel to fully exert the role of microalloying elements, saving the amount of microalloying elements and further reducing production costs.
  • the vanadium carbonitride can precipitate and refine the steel structure in the low carbon steel body.
  • Vanadium nitride has lower solid solubility in ferrite than vanadium carbide, increases nitrogen content in vanadium microalloyed steel, and is more likely to precipitate vanadium nitride in ferrite, which can improve precipitation strengthening of vanadium microalloyed steel. And grain refinement strengthening effect.
  • Increasing the nitrogen content in the vanadium-containing microalloyed steel is beneficial to the precipitation of VN. Since the mismatch between VN and ferrite is the smallest, it can become the preferential nucleation position of ferrite, which can promote ferrite transformation and improve phase transformation. The starting temperature and the critical cooling rate at which the full bainite structure is formed.
  • the invention also provides a preparation method of the above-mentioned yield strength 460MPa grade high toughness low temperature resistant H-shaped steel, which comprises the steps of hot metal pretreatment, converter smelting, refining, continuous casting, rolling, cooling and straightening, which are not mentioned in the present invention.
  • the prior art can be used in the process.
  • the soaking temperature of the heating furnace is 1230 ⁇ 1280°C
  • the casting billet is in the furnace time of 120-200min
  • the rolling rolling temperature is 1150 ⁇ 1180°C
  • the water cooling between the finishing stands is all started
  • the finishing rolling temperature is 750 ⁇ 860 ° C.
  • the superheat of the continuous casting tundish steel is ⁇ 25 ° C to ensure the quality of the slab.
  • Steel must ensure a certain acid-soluble aluminum content to ensure that the molten steel achieves a good deoxidation effect, improve the cleanliness of the steel, and reduce the damage of the inclusions in the steel.
  • the steel material After the finish rolling, the steel material enters the finishing mill and enters the heat preservation roller with roller cover to ensure uniform temperature drop, and then enters the cooling bed for slow cooling.
  • the preparation method of the high-toughness and low-temperature resistant H-shaped steel with a yield strength of 460 MPa of the present invention specifically includes hot metal pretreatment, converter smelting, refining, full protection continuous casting, slow cooling of casting billet, and hole rolling process. And offline slow cooling process.
  • the invention is designed by low-carbon microalloying process, with lower carbon content and other lower alloying elements, and nitrogen is a valuable alloying.
  • the elements are kept in the steel as much as possible, through the reasonable optimization of the distribution ratio of the steel seed, the rolling process of the steel rolling and the post-rolling cooling; the fine-grain strengthening, the precipitation strengthening and the phase transformation strengthening mechanism are used to obtain the appropriate amount of bainite.
  • Multiphase structure bainite can not only increase the strength, ductility and toughness of steel, but also reduce the deformation and cracking of steel grades, greatly improve the performance and surface quality of steel grades; the H-beam has high strength and good steel properties.
  • the high finished product rate and low process control difficulty are beneficial to the industrial mass production of large and medium-sized high-strength and tough H-shaped steel products for low-temperature areas or marine engineering.
  • the continuous casting blank is placed in the thermal insulation pit to be slowly cooled to ensure the surface quality and internal defects of the slab.
  • the finished H-shaped steel structure is mainly composed of bainite + ferrite and contains a small amount of pearlite structure
  • the H-shaped steel product of the invention has good mechanical properties, yield strength ⁇ 460 MPa, tensile strength ⁇ 600 MPa, elongation ⁇ 18%; longitudinal impact energy of -40 ° C ⁇ 100 J, suitable for use in extremely low temperature conditions.
  • Fig. 1 is a metallographic structure diagram (x 200) of a high-toughness low-temperature resistant H-shaped steel having a yield strength of 460 MPa prepared in Example 2 of the present invention.
  • the continuous casting slabs in the following examples were prepared according to the following process: according to the set chemical composition range (Table 1), the blast furnace molten iron was used as the raw material, and the C, Si, Mn, S, and P were adjusted by converter smelting and refining. The content of the material is microalloyed, and the composition reaches the target value, and then continuous casting, direct heating of the slab, or soaking.
  • Table 1 the set chemical composition range
  • the steel is subjected to hot metal pretreatment ⁇ converter smelting ⁇ ladle argon blowing ⁇ refining ⁇ continuous casting ⁇ profile steel wire rolling ⁇ cold bed slow cooling.
  • the profile steel wire rolling includes two rolling processes of rough rolling and finish rolling.
  • the prior art can be employed in the processes not mentioned in the present invention.
  • the hot rolling process mainly controls the temperature, and the finish rolling temperature detects the outside of the flange, and the rolled material is naturally cooled in the cold bed after rolling.
  • the chemical compositions and specific processes of Examples 1-4 are shown in Table 1 below.
  • Example 1-4 The hot rolling process conditions of Examples 1-4 are shown in Table 2.
  • BS EN ISO 377-1997 Standard ISO 377-1997 "Sampling position and preparation of test specimens for mechanical properties”; test methods for yield strength, tensile strength and elongation: reference standard ISO6892-1-2009 "Metal materials tensile test method at room temperature”
  • the impact test method is based on the standard ISO 148-1 "Metal material Charpy pendulum impact test", the results are shown in Table 3.
  • the yield strength of Examples 1-4 of the present invention is maintained at the level of 460 MPa, and has good elongation performance, and the impact energy at -40 ° C is high. It can meet the conditions for the preparation of marine engineering components in extremely low environments, and is suitable for the production of supporting structural members with high low temperature toughness requirements such as offshore oil platforms and marine ocean shipping vessels.
  • the tissue of the present application is a granular bainite + ferrite structure.
  • the dispersed bainite in this type of structure increases the strength of the steel, and the fine ferrite contributes greatly to the improvement of toughness and plasticity. Therefore, for the H-shaped steel of the 460 MPa class strength, the toughness, especially the low temperature toughness, is improved while satisfying the strength.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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Abstract

一种屈服强度460MPa级热轧高韧性耐低温H型钢，其化学成分组成按重量百分比为：C：0.03％～0.07％，Si≤0.3％，Mn：1.20％～1.40％，Nb:0.015％～0.030％，V：0.10％～0.15％，Ti：0.015％～0.025％，Ni：0.25％～0.45％，Cr：0.30％～0.50％，Als：0.01％～0.06％，N：0.010％～0.023％，P≤0.015％，S≤0.010％，O≤0.004％，其余为Fe和不可避免杂质；采用含N复合微合金化成分设计，从而在普通热轧H型钢轧机上实现460MPa级别以上强度的同时，获得较高的强韧性；该H型钢产品其力学性能良好，屈服强度≥460MPa，抗拉强度≥600MPa，延伸率≥18％；-40℃纵向冲击功≥100J，适合极低温度条件地区使用。

Description

一种屈服强度460MPa级热轧高韧性耐低温H型钢及其制备方法
相关申请的交叉参考
该申请要求2018年5月16日提交的中国专利申请号为201810467000.0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，本发明涉及一种屈服强度460MPa级热轧高韧性耐低温H型钢及其制备方法。
背景技术
随着能源开采向极寒等复杂区域发展，迫切需要综合性能更高的热轧H型钢替代目前低级别H型钢，在减轻重量的同时，保证具有较高的可靠性。同时为适应极寒等复杂地区服役环境，对钢材的低温冲击韧性，焊接性能，抗层状撕裂性能等提出了更高的要求，更高强度级别的热轧H钢需求逐渐增加。
目前我国的热轧H型钢生产企业已陆续开发出屈服强度345MPa以上不同级别的H型钢，一般采用复合微合金化配合热轧方法生产。不同企业根据装备水平制备出不同级别和不同综合性能的产品。
申请号CN201310200230.8的专利申请公开了一种屈服强度450MPa级含钒耐候热轧H型钢的轧制工艺，该含钒耐候热轧H型钢成分配比为(wt％)：C：0.09～0.11，Si：0.45～0.52，Mn：1.25～1.38，P：0.015～0.022，S：0.008～0.014，Cu：0.27～0.33，Cr：0.35～0.42，Ni：0.25～0.32，V：0.073～0.087，A1 (s)：0.010～0.025，其余为铁和残余的微量杂质；该含钒耐候热轧H型钢在轧后采用两段式快速冷却处理实现屈服强度450MPa的目标，对轧后冷却设备具有特殊要求。
申请号CN201510044714.7的专利申请涉及一种耐低温热轧H型钢及其制备方法，所述的热轧H型钢化学成分为(wt％)：C:0.07～0.10％、Si:0.2～0.4％、Mn:1.30～1.60％、P≤0.020％、S≤0.015％、V:0.015～0.070％、Ti:0.010～0.030％，余量为Fe和不可避免的杂质。生产方法包括转炉冶炼、LF精炼、连铸、轧制等。本发明制备的H型钢的组织为多边形铁素体和珠光体组织，屈服强度为350～450MPa。该专利轧制工艺采用常规方法，化学成分设计使得其轧后屈服强度接近450MPa。
上述两种高强H型钢及制备技术均采用微合金化配合不同冷却的方式，具有较高强度的同时保证一定的低温冲击韧性。一方面对冷却设备要求较高，另一方面采用普通设备轧制，强度不能实现更大的提高。
发明内容
本发明的目的在于，为了满足极寒等复杂环境下海洋工程用高强、高韧钢的需求，设计发明一种屈服强度460MPa级热轧高韧性耐低温H型钢及其制备方法，该H型钢特别适合极低温度条件地区(海洋工程)具有较高强韧性要求的支撑结构件制作使用。
本发明的技术方案如下：
本发明的屈服强度460MPa级高韧性耐低温H型钢，其化学成分组成按重量百分比为：C：0.03％～0.07％，Si≤0.3％，Mn：1.20％～1.40％，Nb:0.015％～0.030％，V：0.10％～0.15％，Ti：0.015％～0.025％，Ni：0.25％～0.45％，Cr：0.30％～0.50％，A1s：0.01％～0.06％，N：0.010％～0.023％，P≤0.015％，S≤0.010％，O≤0.004％，其余为Fe和不可避免杂质。作为优选的，本发明中V、Ti与Nb的元素，满足0.10％≤V+Ti+Nb≤0.20％。满足该公式要求制备出的H型钢，可以更好的满足沉淀强化微合金化要求，从而提高钢的强度。
本发明中氮对微合金化碳氮化物的析出起重要作用，尤其是在用钛和钒微合金化的钢中。含氮钢不仅消除了炼钢过程中因脱气和精炼去氮引起的成本增加，而且钢中增氮更能充分发挥微合金元素的作用，节约微合金化元素的用量，进一步降低生产成本。
钒的碳氮化物可以在低碳钢铁素体中析出并细化钢的组织。氮化钒比碳化钒在铁素体中有更低的固溶度，增加钒微合金钢中的氮含量，在铁素体中更容易析出氮化钒，可以提高钒微合金钢的析出强化和晶粒细化强化效果。
在含钒微合金钢中提高氮含量，有利于VN析出，由于VN与铁素体的错配度最小，能成为铁素体的优先形核位置，可促进铁素体相变、提高相变开始温度和形成全贝氏体组织的临界冷却速率。
本发明还提供了一种上述屈服强度460MPa级高韧性耐低温H型钢的制备方法，依次包括铁水预处理、转炉冶炼、精炼、连铸、轧制、冷却以及矫直步骤，本发明未提及的工序，均可采用现有技术。
其中，在轧制过程中，加热炉均热温度为1230～1280℃，铸坯在炉时间为 120～200min；开轧温度为1150～1180℃，精轧机架间水冷全部开启，终轧温度为750～860℃。
进一步地，根据本发明所述的制备方法，其中优选地，连铸中间包钢水过热度≤25℃，保证铸坯质量。钢中需保证一定的酸溶铝含量保证钢水达到较好的脱氧效果，提高钢的洁净度，减少钢中夹杂物对性能的危害。
精轧后的钢材出精轧机后进入带保温罩辊道保温，保证温降均匀，随后进入冷床进行缓冷。
根据本发明实施例，本发明的屈服强度460MPa级高韧性耐低温H型钢的制备方法具体包括铁水预处理、转炉冶炼、精炼、全保护连铸，铸坯保温坑缓冷，孔型轧制工艺及离线缓冷工艺。
在综合考虑成本、生产工艺及质量的情况下，本发明通过低碳微合金化工艺设计，以较低的碳含量配合其他较低含量的合金元素，将氮作为是一种有价值的合金化元素尽量保留于钢中，通过对钢种成分配比的合理优化，配合型钢轧制及轧后冷却的轧制工艺；利用细晶强化、析出强化和相变强化机制，制得以适量贝氏体+铁素体为主，包含少量的珠光体的高强韧H型钢，其中组织表层为单相下贝氏体或铁素体+单相下贝氏体，内部为铁素体+珠光体的细小复相组织；贝氏体不仅能够增加钢的强度、塑性及韧性，且能减少钢种变形及开裂，极大的提高了钢种性能及表面质量；该H型钢强度高，钢种性能好，成材率高，而且工艺控制难度较低，有利于实现低温地区或海洋工程用大中规格高强韧H型钢产品的工业化批量生产。
本发明技术方案的优点在于：
1、适合普通轧机进行正火轧制的低碳和复合微合金化成分设计思路，降低轧制过程的高温轧制力；同时采用含N复合微合金化成分设计，从而在普通热轧H型钢轧机上实现460MPa级别以上强度的同时，获得较高的强韧性。
2、为避免N含量较高带来的铸坯裂纹缺陷，连铸坯下线后进保温坑进行缓冷，保证铸坯表面质量及内部缺陷。
3、成品H型钢组织以适量贝氏体+铁素体为主，包含少量的珠光体组织；
4、本发明涉及的H型钢产品其力学性能良好，屈服强度≥460MPa，抗拉强度≥600MPa，延伸率≥18％；-40℃纵向冲击功≥100J，适合极低温度条件地区使用。
附图说明
图1是本发明中实施例2制备的屈服强度460MPa级高韧性耐低温H型钢的金相组织图(×200)。
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)，以高炉铁水为原料，通过转炉冶炼、精炼，调整C、Si、Mn、S、P等的含量并进行微合金化，成分达到目标值后进行连铸、铸坯直接加热或者均热。
实施例1-4的制备步骤如下：
该钢经过铁水预处理→转炉冶炼→钢包吹氩→精炼→连铸→型钢线轧制→冷床缓冷。其中，型钢线轧制包括粗轧和精轧两道轧制。本发明未提及的工序，均可采用现有技术。热轧工序以控制温度为主，终轧温度检测翼缘外侧，轧后轧材在冷床自然冷却。实施例1-4的化学成分及具体工艺见下表1。
表1 化学成分(wt％,余量铁)
Figure PCTCN2018121100-appb-000001
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3。
表2 实施例热轧工艺
Figure PCTCN2018121100-appb-000002
表3 实施例力学性能试验结果
Figure PCTCN2018121100-appb-000003
从表中可见，本发明实施例1-4屈服强度保持460MPa级别，具有良好的延伸性能，其-40℃冲击功较高。可以满足制备海洋工程构件在极低环境下的使用条件，适用于制作海洋石油平台、海洋远洋运输船舶等具有较高低温韧性要求的支撑结构件。
从图1可以看出本申请的组织为粒状贝氏体+铁素体组织。该类别组织中弥散分布的贝氏体提高了钢的强度，细小的铁素体对韧性和塑性提高具有很大帮助。因此，对于460MPa级别强度的H型钢，满足强度的同时，韧性尤其是低温韧性得到提升。
当然，本发明还可以有多种实施例，在不背离本发明精神及其实质的情况下，熟悉本领域的技术人员可根据本发明的公开做出各种相应的改变和变形，但这些相应的改变和变形都应属于本发明的权利要求的保护范围。

Claims (6)

  1. 一种屈服强度460MPa级热轧高韧性耐低温H型钢，其特征在于，所述H型钢的化学成分组成按重量百分比为：C：0.03％～0.07％，Si≤0.3％，Mn：1.20％～1.40％，Nb：0.015％～0.030％，V：0.10％～0.15％，Ti：0.015％～0.025％，Ni：0.25％～0.45％，Cr：0.30％～0.50％，A1s：0.010％～0.06％，N：0.010％～0.023％，P≤0.015％，S≤0.010％，O≤0.004％，其余为Fe和不可避免杂质。
  2. 根据权利要求1所述的H型钢，其特征在于，0.10％≤V+Ti+Nb≤0.20％。
  3. 根据权利要求1或2所述的H型钢，其特征在于，所述H型钢的屈服强度≥460MPa，抗拉强度≥600MPa，延伸率≥18％，-40℃纵向冲击功≥100J。
  4. 一种权利要求1-3任一项所述H型钢的制备方法，依次包括铁水预处理、转炉冶炼、精炼、连铸、轧制、冷却以及矫直步骤，
    其中，在轧制过程中，加热炉均热温度为1230～1280℃，铸坯在炉时间为120～200min；开轧温度为1150～1180℃，精轧机架间水冷全部开启，终轧温度为750～860℃。
  5. 根据权利要求4所述的制备方法，其特征在于，连铸中间包钢水过热度≤25℃。
  6. 根据权利要求4所述的制备方法，其特征在于，精轧后的钢材出精轧机后进入带保温罩辊道保温，随后进入冷床进行缓冷。
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