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WO2019029225A1 - 一种提高低温韧性的厚壁大口径高钢级管线钢及其制造方法 - Google Patents

一种提高低温韧性的厚壁大口径高钢级管线钢及其制造方法 Download PDF

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WO2019029225A1
WO2019029225A1 PCT/CN2018/088151 CN2018088151W WO2019029225A1 WO 2019029225 A1 WO2019029225 A1 WO 2019029225A1 CN 2018088151 W CN2018088151 W CN 2018088151W WO 2019029225 A1 WO2019029225 A1 WO 2019029225A1
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temperature
rolling
pass
thickness
low
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PCT/CN2018/088151
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English (en)
French (fr)
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翟冬雨
姜金星
杜海军
员强鹏
殷杰
张媛钰
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南京钢铁股份有限公司
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Priority to RU2019138020A priority Critical patent/RU2728366C1/ru
Publication of WO2019029225A1 publication Critical patent/WO2019029225A1/zh

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
    • 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
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • 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
    • C22C38/002—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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 field of iron and steel metallurgy and relates to a production process for improving the low temperature drop hammer of a large diameter pipeline steel, in particular to a thick wall large diameter high steel grade pipeline steel which improves low temperature toughness and a manufacturing method thereof.
  • Thick-walled large-diameter pipeline steel for oil transportation ( ⁇ 1422 ⁇ 30.8mm thick-walled large-diameter pipeline steel) belongs to high-end products of pipeline steel, requiring large diameters and meeting the requirements for low-temperature service. At present, the existing domestic technology cannot be improved. The barrier of low temperature toughness of this variety. In the prior art, the manufacturing method of the thick-walled large-diameter high-grade steel pipeline steel cannot form the fine bainite and the true ferrite structure, and the band structure of the core cannot be effectively eliminated and the uniformity of strength and toughness is achieved. The fine grain structure meets the requirements of low temperature toughness of the product.
  • the technical problem to be solved by the invention is how to ensure the formation of a fine and uniform bainite and acicular ferrite structure in the core of the rolled piece, to ensure the strength and toughness requirements, and to meet the requirements of the product for the ultra-low temperature drop hammer.
  • a thick-walled large-diameter high-grade steel pipeline steel with improved low-temperature toughness the weight percentage components of which are: C: 0.038-0.058%, Si: 0.17-0.27%, Mn: 1.65-1.75%, P ⁇ 0.01%, S ⁇ 0.003%, Al: 0.015 to 0.05%, Nb: 0.045 to 0.055%, Ti: 0.006 to 0.02%, Cr: 0.11 to 0.16%, Mo: 0.15 to 0.20%, Cu: 0.10 to 0.16%, and Ni: 0.25 to 0.30 %, Ca: 0.0005 to 0.0040%, the balance being Fe and unavoidable impurities.
  • the low-carbon, low-phosphorus and low-sulfur design of the composition is more conducive to the core structure of the slab, which effectively reduces the brittleness of the product.
  • the composition design of Nb, Cr, Mo, Cu and Ni is beneficial to improve the product during the rolling process.
  • the precipitation strength is beneficial to refine the grain of the structure and improve the toughness of the product.
  • the foregoing method for manufacturing a thick-walled large-diameter high-grade steel pipeline steel for improving low-temperature toughness includes the following steps:
  • the weight percentage component of the thick-walled large-diameter high-grade steel pipeline steel of low temperature toughness is the aforementioned component
  • the heating temperature of the slab is 1150 ⁇ 1170°C
  • the heating time is 10.3 ⁇ 13min/cm in thickness of the slab
  • the soaking time is 45 ⁇ 90min; the surface and core temperature of the slab are ensured.
  • Dephosphorization of 2 passes including 1 pass of rough rolling and 1 dephosphorization of 2nd pass of finishing rolling; optimization of dephosphorization pass, in order to ensure rolling temperature and surface quality, design 2 times of phosphorus removal, rough rolling Phosphorus 1 and fine dephosphorization in the second pass of the finishing pass not only ensure the surface quality but also reduce unnecessary temperature loss, ensuring the pass reduction rate;
  • the reduction ratio of the rough rolling pass is more than 25%, and the thickness of the warm blank is 3.5 to 4.0 times the thickness of the steel plate;
  • the second-stage rolling temperature is set at 810-830 ° C, and the final rolling temperature is 800-830 ° C;
  • Laminar flow cooling a total of 12 groups of water, the first 4 groups are cooled according to the maximum flow rate, the flow rate is 300-350 m 3 /h, and the last 8 groups are cooled by a small flow, the flow rate is 200-300 m 3 /h, and the red return temperature is 330-420 ° C;
  • the laminar cooling system improves the grain size of the tissue and reduces the number of Maao islands, which is more conducive to the formation of bainite and acicular ferrite.
  • the invention finally adopts a low-temperature heating system, a low-intake water, and a low-return red rolling process, thereby effectively reducing the grain size of the tissue, obtaining a dense bainite and acicular ferrite structure in the core, and passing the strong cold. Eliminate the unfavorable factors of the band structure, effectively improve the strengthening effect of the precipitation elements, improve the mechanical properties of the product, and meet the requirements of low temperature toughness of the product; thus, the present invention adopts a low carbon design to increase the toughness of the product, and the alloy adopts Nb.
  • Ti, Cr, Mo, Cu design increase the precipitation strength during rolling
  • the heating temperature of the billet adopts low temperature heating system, reduce the dephosphorization pass times, increase the pass reduction rate, odd pass rolling, low water input, low Reddening effectively reduces the grain size of the rolled product and refines the structure.
  • the cooling system effectively eliminates the band structure and ensures the formation of fine and uniform bainite and acicular ferrite structure in the core of the rolled product.
  • the requirements of strength and toughness meet the requirements of the product for ultra-low temperature drop hammer.
  • the invention successfully solves the manufacturing difficulty of the low-temperature drop hammer of the wide and thick pipeline steel, improves the mechanical properties of the steel after rolling, satisfies the requirements of the customer, and greatly improves the economic benefit.
  • FIG. 1 is a view showing the metallographic structure of a first embodiment of the present invention.
  • Figure 2 is a metallographic structure diagram of Embodiment 2 of the present invention.
  • Figure 3 is a metallographic structure diagram of Embodiment 3 of the present invention.
  • the embodiment is a method for manufacturing a thick-walled large-diameter high-grade steel pipeline steel with improved low-temperature toughness, comprising the following steps:
  • the weight percentage components of the low-temperature tough thick-walled large-diameter high-grade steel pipeline steel are: C: 0.039%, Si: 0.19%, Mn: 1.68%, P: 0.006%, S: 0.002%, and Al: 0.025% Nb: 0.051%, Ti: 0.0016%, Cr: 0.15%, Mo: 0.19%, Cu: 0.12%, Ni: 0.27%, Ca: 0.0015%, balance Fe and unavoidable impurities;
  • the heating temperature of the slab is 1155 ° C
  • the heating time is 10.3 min/cm in the thickness of the slab
  • the soaking time is 56 min
  • the reduction ratio of the rough rolling pass is more than 25%, and the thickness of the warm blank is 3.5 to 4.0 times the thickness of the steel plate;
  • the second stage rolling temperature is set at 815 ° C, and the final rolling temperature is 810 ° C;
  • Laminar flow cooling a total of 12 groups of water, the first 4 groups according to the maximum flow rate, the flow rate of 300m 3 / h after 8 groups with a small flow cooling, flow 200m 3 / h, red return temperature 350 ° C.
  • the embodiment is a method for manufacturing a thick-walled large-diameter high-grade steel pipeline steel with improved low-temperature toughness, comprising the following steps:
  • the weight percentage components of the low-temperature tough thick-walled large-diameter high-grade steel pipeline steel are: C: 0.043%, Si: 0.217%, Mn: 1.66%, P: 0.006%, S: 0.001%, and Al: 0.020% Nb: 0.052%, Ti: 0.009%, Cr: 0.13%, Mo: 0.17%, Cu: 0.15%, Ni: 0.26%, Ca: 0.001%, balance Fe and unavoidable impurities;
  • the heating temperature of the slab is 1167 ° C
  • the heating time is 11 min / cm in thickness of the slab
  • the soaking time is 58 min
  • the reduction ratio of the rough rolling pass is more than 25%, and the thickness of the warm blank is 3.5 to 4.0 times the thickness of the steel plate;
  • the second stage rolling temperature is set at 811 ° C, and the final rolling temperature is 810 ° C;
  • Laminar flow cooling a total of 12 groups of water, the first 4 groups according to the maximum flow rate, the flow rate is 320m 3 /h, the last 8 groups use a small flow, the flow rate is 250m 3 /h cooling, the red return temperature is 365 °C.
  • the embodiment is a method for manufacturing a thick-walled large-diameter high-grade steel pipeline steel with improved low-temperature toughness, comprising the following steps:
  • the weight percentage components of the low-temperature tough thick-walled large-diameter high-grade steel pipeline steel are: C: 0.044%, Si: 0.218%, Mn: 1.67%, P: 0.007%, S: 0.002%, and Al: 0.036% Nb: 0.054%, Ti: 0.011%, Cr: 0.12%, Mo: 0.17%, Cu: 0.13%, Ni: 0.28%, Ca: 0.0020%, balance Fe and unavoidable impurities;
  • the heating temperature of the slab is 1158 ° C
  • the heating time is 12 min / cm in thickness of the slab
  • the soaking time is 57 min
  • the reduction ratio of the rough rolling pass is more than 25%, and the thickness of the warm blank is 3.5 to 4.0 times the thickness of the steel plate;
  • the second stage rolling temperature is set at 813 ° C, and the final rolling temperature is 801 ° C;
  • the embodiment is a method for manufacturing a thick-walled large-diameter high-grade steel pipeline steel with improved low-temperature toughness, comprising the following steps:
  • the weight percentage components of the low-temperature tough thick-walled large-diameter high-grade steel pipeline steel are: C: 0.053%, Si: 0.21%, Mn: 1.70%, P: 0.006%, S: 0.001%, and Al: 0.035% , Nb: 0.047%, Ti: 0.02%, Cr: 0.15%, Mo: 0.17%, Cu: 0.13%, Ni: 0.30%, Ca: 0.00240%, balance Fe and unavoidable impurities;
  • the heating temperature of the slab is 1150 ° C
  • the heating time is 13 min / cm in thickness of the slab
  • the soaking time is 55 min
  • the reduction ratio of the rough rolling pass is more than 25%, and the thickness of the warm blank is 3.5 to 4.0 times the thickness of the steel plate;
  • the second stage rolling temperature is set at 822 ° C, and the final rolling temperature is 813 ° C;
  • Laminar flow cooling a total of 12 groups of water, the first 4 groups according to the maximum flow rate, the flow rate of 350m 3 / h after 8 groups using a small flow, flow 300m 3 / h cooling, 200 ⁇ 300m 3 / h red return temperature 410 ° C.
  • the metallographic structure of Figures 1, 2 and 3 was obtained by using the above Examples 1-3. It can be seen from the figure that the core structure is uniform and fine, and there is no granular or island distribution in the tissue, mainly bainite and acicular ferrite.
  • the body structure is dominant, the acicular ferrite has the characteristics of bainite, and is similar in morphology to the carbon-free bainite in low carbon steel.
  • the type of structure is mainly soft phase ferrite, which improves the toughness and improves the impact. Resilience is beneficial.

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Abstract

一种提高低温韧性的厚壁大口径高钢级管线钢及其制造方法，该管线钢的组分为（重量百分比）：C：0.038～0.058％、Si：0.17～0.27％、Mn：1.65～1.75％、P≤0.01％、S≤0.003％、Al：0.015～0.05％、Nb：0.045～0.055％、Ti：0.006～0.02％、Cr：0.11～0.16％、Mo：0.15～0.20％、Cu：0.10～0.16％、Ni：0.25～0.30％、Ca：0.0005～0.0040％、余量为Fe和不可避免的杂质；其制造方法包括采用厚度320mm断面铸坯，通过坯料加热，轧制，层流冷却，保证不同形变储存能及晶界迁移率，有效细化组织晶粒度，得到组织均匀的贝氏体、针状铁素体，确保了组织与性能的稳定，满足了宽厚高钢级管线钢性能要求。

Description

一种提高低温韧性的厚壁大口径高钢级管线钢及其制造方法 技术领域
本发明属于钢铁冶金领域，涉及一种改善大口径管线钢低温落锤的生产工艺，具体的说是一种提高低温韧性的厚壁大口径高钢级管线钢及其制造方法。
背景技术
石油输送用厚壁大口径管线钢(φ1422×30.8mm厚壁大口径管线钢)属于管线钢品种高精端产品，要求管径大，且要满足低温服役要求，目前国内现有技术无法突破改善该品种低温韧性的壁垒。现有技术中，厚壁大口径高钢级管线钢的制造方法无法形成细小贝氏体、真状铁素体组织，无法有效消除芯部的带状组织及实现强度、韧性更高的均匀的细晶组织，满足了产品低温韧性的要求。
发明内容
本发明所要解决的技术问题是，如何保证轧件芯部形成了细小均匀的贝氏体、针状铁素体组织，保证强度、韧性的要求，满足了产品对超低温落锤的要求。
本发明解决以上技术问题的技术方案是：
一种提高低温韧性的厚壁大口径高钢级管线钢，其重百分比成份为：C：0.038～0.058％、Si：0.17～0.27％、Mn：1.65～1.75％、P≤0.01％、S≤0.003％、Al：0.015～0.05％、Nb：0.045～0.055％、Ti：0.006～0.02％、Cr：0.11～0.16％、Mo：0.15～0.20％、Cu：0.10～0.16％、Ni：0.25～0.30％、Ca：0.0005～0.0040％、余量为Fe和不可避免的杂质。成份采用低碳、低磷、低硫设计更有利于铸坯芯部组织，有效降低了产品脆性，采用Nb、Cr、Mo、Cu、Ni的成份设计组合，有利提高产品在轧制过程中的析出强度，有利于细化组织晶粒，提高产品的韧性。
前述的提高低温韧性的厚壁大口径高钢级管线钢的制造方法，包括以下步骤：
㈠低温韧性的厚壁大口径高钢级管线钢的重百分比成份为前述成份；
㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1150～1170℃，加热时间以铸坯厚度为单位10.3～13min/cm，均热时间45～90min；确保了铸坯表面、芯部温度均匀，通过低温加热制度，有效控制了原始晶粒度的尺寸，为强化组织性能提供了保证；
㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；除磷道次的优化，为了保证轧制温度与表面质量，设计2道次除磷，粗轧除磷1道，精轧第2道除磷1道，既保证了表面质量同时减少了不必要的温度损失，保证了道次压下率；
㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
㈤采用低温轧制，二阶段轧制温度设定810～830℃，终轧温度800～830℃；
㈥采用奇道次轧制工艺；可以有效减少冷却时间；
㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度750～770℃；由于芯部温度大于表面温度，低入水温度保证了轧件的芯部温度大于Ar3温度点，芯部组织更加均匀，强度韧性更加优良；
㈧层流冷却共12组水，前4组按最大流量冷却，流量300～350m 3/h，后8组采用小流量冷却，流量200～300m 3/h，返红温度330～420℃；通过层流冷却系统改善组织晶粒度，减少马奥岛组织的数量，更利于生成贝氏体、针状铁素体。
本发明通过反复试验，最终采用低温加热制度、低入水、低返红的轧制工艺，有效降低了组织晶粒度，芯部获得致密的贝氏体、针状铁素体组织，通过强冷消除带状组织的不利因素，有效提高析出元素的强化作用，提高了产品的力学性能，满足了产品低温韧性的要求；由此可见，本发明采用低碳设计，增加产品的韧性，合金采用Nb、Ti、Cr、Mo、Cu设计，增加轧制过程中的析出强度，坯料加热温度采用低温加热制度，减少除磷道次增加了道次压下率、奇道次轧制、低入水、低返红，有效降低了轧制成品的晶粒度，细化组织，冷却制度有效消除了带状组织，保证了轧件芯部形成了细小均匀的贝氏体、针状铁素体组织，保证了强度、韧性的要求，满足了产品对超低温落锤的要求。本发明成功解决了宽厚管线钢低温落锤的制造难点，提高了钢材轧制后的力学性能，满足了客户要求，大幅度提高经济效益。
附图说明
图1是本发明实施例1的金相组织图。
图2是本发明实施例2的金相组织图。
图3是本发明实施例3的金相组织图。
具体实施方式
实施例1
本实施例是一种提高低温韧性的厚壁大口径高钢级管线钢的制造方法，包括以下步骤：
㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.039％、Si：0.19％、Mn：1.68％、P：0.006％、S：0.002％、Al：0.025％、Nb：0.051％、Ti：0.0016％、Cr：0.15％、 Mo：0.19％、Cu：0.12％、Ni：0.27％、Ca：0.0015％、余量为Fe和不可避免的杂质；
㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1155℃，加热时间以铸坯厚度为单位10.3min/cm，均热时间56min；
㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
㈤采用低温轧制，二阶段轧制温度设定815℃，终轧温度810℃；
㈥采用奇道次轧制工艺；
㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度770℃；
㈧层流冷却共12组水，前4组按最大流量，流量300m 3/h后8组采用小流量冷却，流量200m 3/h，返红温度350℃。
实施例2
本实施例是一种提高低温韧性的厚壁大口径高钢级管线钢的制造方法，包括以下步骤：
㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.043％、Si：0.217％、Mn：1.66％、P：0.006％、S：0.001％、Al：0.020％、Nb：0.052％、Ti：0.009％、Cr：0.13％、Mo：0.17％、Cu：0.15％、Ni：0.26％、Ca：0.001％、余量为Fe和不可避免的杂质；
㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1167℃，加热时间以铸坯厚度为单位11min/cm，均热时间58min；
㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
㈤采用低温轧制，二阶段轧制温度设定811℃，终轧温度810℃；
㈥采用奇道次轧制工艺；
㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度760℃；
㈧层流冷却共12组水，前4组按最大流量，流量320m 3/h,后8组采用小流量，流量250m 3/h 冷却，返红温度365℃。
实施例3
本实施例是一种提高低温韧性的厚壁大口径高钢级管线钢的制造方法，包括以下步骤：
㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.044％、Si：0.218％、Mn：1.67％、P：0.007％、S：0.002％、Al：0.036％、Nb：0.054％、Ti：0.011％、Cr：0.12％、Mo：0.17％、Cu：0.13％、Ni：0.28％、Ca：0.0020％、余量为Fe和不可避免的杂质；
㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1158℃，加热时间以铸坯厚度为单位12min/cm，均热时间57min；
㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
㈤采用低温轧制，二阶段轧制温度设定813℃，终轧温度801℃；
㈥采用奇道次轧制工艺；
㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度761℃；
㈧层流冷却共12组水，前4组按最大流量，流量340m 3/h后8组采用小流量，流量280m 3/h冷却，返红温度365℃。
实施例4
本实施例是一种提高低温韧性的厚壁大口径高钢级管线钢的制造方法，包括以下步骤：
㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.053％、Si：0.21％、Mn：1.70％、P：0.006％、S：0.001％、Al：0.035％、Nb：0.047％、Ti：0.02％、Cr：0.15％、Mo：0.17％、Cu：0.13％、Ni：0.30％、Ca：0.00240％、余量为Fe和不可避免的杂质；
㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1150℃，加热时间以铸坯厚度为单位13min/cm，均热时间55min；
㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
㈤采用低温轧制，二阶段轧制温度设定822℃，终轧温度813℃；
㈥采用奇道次轧制工艺；
㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度760℃；
㈧层流冷却共12组水，前4组按最大流量，流量350m 3/h后8组采用小流量，流量300m 3/h冷却，200～300m 3/h返红温度410℃。
采用以上实施例1-3得到图1、2和3的金相组织，由图可知，芯部组织均匀细小，组织内没有颗粒状或岛状物分布，主要以贝氏体、针状铁素体组织为主，针状铁素体具有贝氏体的特征，在形态上类似低碳钢中的无碳贝氏体，组织的类型以软相铁素体为主，对改善韧性、提高冲击韧性有利。
表2 本发明各实施例的力学性能
Figure PCTCN2018088151-appb-000001
由表2可以看出，实施例1、2、3和4的力学性能均达到API 5L标准中X80的要求及中石油中俄东线客户要求，经济效益显著，超低温落锤剪切面积大于85％，本发明的生产方法简单易行，使材料的综合性能提高。
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 (6)

  1. 一种提高低温韧性的厚壁大口径高钢级管线钢，其特征在于：其重百分比成份为：C：0.038～0.058％、Si：0.17～0.27％、Mn：1.65～1.75％、P≤0.01％、S≤0.003％、Al：0.015～0.05％、Nb：0.045～0.055％、Ti：0.006～0.02％、Cr：0.11～0.16％、Mo：0.15～0.20％、Cu：0.10～0.16％、Ni：0.25～0.30％、Ca：0.0005～0.0040％、余量为Fe和不可避免的杂质。
  2. 如权利要求1所述的提高低温韧性的厚壁大口径高钢级管线钢的制造方法，其特征在于：包括以下步骤：
    ㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.038～0.058％、Si：0.17～0.27％、Mn：1.65～1.75％、P≤0.01％、S≤0.003％、Al：0.015～0.05％、Nb：0.045～0.055％、Ti：0.006～0.02％、Cr：0.11～0.16％、Mo：0.15～0.20％、Cu：0.10～0.16％、Ni：0.25～0.30％、Ca：0.0005～0.0040％、余量为Fe和不可避免的杂质；
    ㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1150～1170℃，加热时间以铸坯厚度为单位10.3～13min/cm，均热时间45min～90min；
    ㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
    ㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
    ㈤采用低温轧制，二阶段轧制温度设定810～830℃，终轧温度800～830℃；
    ㈥采用奇道次轧制工艺；
    ㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度750～770℃；
    ㈧层流冷却共12组水，前4组按最大流量冷却，流量300～350m 3/h，后8组采用小流量冷却，流量200～300m 3/h，返红温度330～420℃。
  3. 如权利要求2所述的提高低温韧性的厚壁大口径高钢级管线钢的制造方法，其特征在于：包括以下步骤：
    ㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.048％、Si：0.19％、Mn：1.68％、P：0.008％、S：0.002％、Al：0.025％、Nb：0.05％、Ti：0.006％、Cr：0.13％、Mo：0.19％、Cu：0.13％、Ni：0.28％、Ca：0.0015％、余量为Fe和不可避免的杂质；
    ㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1155℃，加热时间以铸坯厚度为单位10.3min/cm，均热时间55min；
    ㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
    ㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
    ㈤采用低温轧制，二阶段轧制温度设定815℃，终轧温度810℃；
    ㈥采用奇道次轧制工艺；
    ㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度770℃；
    ㈧层流冷却共12组水，前4组按最大流量，流量300m 3/h后8组采用小流量冷却，流量200m 3/h，返红温度350℃。
  4. 如权利要求2所述的提高低温韧性的厚壁大口径高钢级管线钢的制造方法，其特征在于：包括以下步骤：
    ㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.043％、Si：0.217％、Mn：1.66％、P：0.006％、S：0.001％、Al：0.020％、Nb：0.052％、Ti：0.009％、Cr：0.11％、Mo：0.16％、Cu：0.15％、Ni：0.26％、Ca：0.001％、余量为Fe和不可避免的杂质；
    ㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1167℃，加热时间以铸坯厚度为单位11min/cm，均热时间51min；
    ㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
    ㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
    ㈤采用低温轧制，二阶段轧制温度设定811℃，终轧温度810℃；
    ㈥采用奇道次轧制工艺；
    ㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度760℃；
    ㈧层流冷却共12组水，前4组按最大流量，流量320m 3/h,后8组采用小流量，流量250m 3/h冷却，返红温度365℃。
  5. 如权利要求2所述的提高低温韧性的厚壁大口径高钢级管线钢的制造方法，其特征在于：包括以下步骤：
    ㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.044％、Si：0.218％、Mn：1.67％、P：0.007％、S：0.002％、Al：0.036％、Nb：0.054％、Ti：0.011％、Cr：0.12％、Mo：0.17％、Cu：0.16％、Ni：0.28％、Ca：0.0020％、余量为Fe和不可避免的杂质；
    ㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1158℃，加热时间以铸坯厚度为单位12min/cm，均热时间48min；
    ㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
    ㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
    ㈤采用低温轧制，二阶段轧制温度设定813℃，终轧温度801℃；
    ㈥采用奇道次轧制工艺；
    ㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度761℃；
    ㈧层流冷却共12组水，前4组按最大流量，流量340m 3/h后8组采用小流量，流量280m 3/h冷却，返红温度365℃。
  6. 如权利要求2所述的提高低温韧性的厚壁大口径高钢级管线钢的制造方法，其特征在于：包括以下步骤：
    ㈠所述低温韧性的厚壁大口径高钢级管线钢的重百分比成份为：C：0.051％、Si：0.21％、Mn：1.70％、P：0.006％、S：0.001％、Al：0.035％、Nb：0.046％、Ti：0.012％、Cr：0.13％、Mo：0.19％、Cu：0.15％、Ni：0.29％、Ca：0.00240％、余量为Fe和不可避免的杂质；
    ㈡采用厚度为320mm断面的铸坯，铸坯加热温度为1150℃，加热时间以铸坯厚度为单位13min/cm，均热时间49min；
    ㈢2道次除磷，包括粗轧除磷1道，精轧第2道除磷1道；
    ㈣提高粗轧末道次压下率，粗轧末道次压下率大于25％，待温坯厚度为钢板厚度的3.5～4.0倍；
    ㈤采用低温轧制，二阶段轧制温度设定822℃，终轧温度813℃；
    ㈥采用奇道次轧制工艺；
    ㈦设定Ar 3温度点为725.73度，采用低入水温度，入水温度760℃；
    ㈧层流冷却共12组水，前4组按最大流量，流量350m 3/h后8组采用小流量，流量300m 3/h冷却，200～300m 3/h返红温度410℃。
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