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WO2019001464A1 - Technologie de production de plaque d'acier de pipeline de gande épaisseur à grain ultra-fin - Google Patents

Technologie de production de plaque d'acier de pipeline de gande épaisseur à grain ultra-fin Download PDF

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Publication number
WO2019001464A1
WO2019001464A1 PCT/CN2018/093096 CN2018093096W WO2019001464A1 WO 2019001464 A1 WO2019001464 A1 WO 2019001464A1 CN 2018093096 W CN2018093096 W CN 2018093096W WO 2019001464 A1 WO2019001464 A1 WO 2019001464A1
Authority
WO
WIPO (PCT)
Prior art keywords
ultra
steel plate
fine grain
pipeline steel
thickness
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/CN2018/093096
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English (en)
Chinese (zh)
Inventor
黄一新
祝瑞荣
姚永宽
楚觉非
翟冬雨
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nanjing Iron and Steel Co Ltd
Original Assignee
Nanjing Iron and Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nanjing Iron and Steel Co Ltd filed Critical Nanjing Iron and Steel Co Ltd
Priority to RU2019135632A priority Critical patent/RU2734901C1/ru
Publication of WO2019001464A1 publication Critical patent/WO2019001464A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • 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
    • C21D8/0221—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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 steel metallurgy and relates to a production process of a pipeline steel plate, in particular to a production process for improving the grain size of a steel plate with a width of 3500-5000 mm and a thickness of 25-40 mm by a rolling control technology. .
  • the technical problem to be solved by the present invention is how to eliminate the unfavorable factors of the band structure for the pipeline steel plate with a width of 3500-5000 mm and a thickness of 25-40 mm, how to obtain a dense bainite and needle shape at the quarter of the steel plate and the core.
  • the ferrite structure which results in a tissue that is evenly organized and fine-grained, improves product performance.
  • a production process of an ultra-fine grain wide and thick pipeline steel plate comprising the following steps:
  • the weight percentage components of ultra-fine grain wide and thick pipeline steel plates are: C: 0.040-0.070%, Si: 0.15-0.30%, Mn: 1.30-1.80%, P ⁇ 0.015%, S ⁇ 0.005%, Nb: 0.030-0.07 %, Ti: 0.006 to 0.020%, Ca: 0.0005 to 0.0040%, Al: 0.015 to 0.050%, Ni: 0.10 to 0.30%, Cr: 0.10 to 0.30%, Mo: 0.08 to 0.18%, Cu: 0.1 to 0.2% The balance is Fe and inevitable impurities;
  • the heating temperature of the slab is set to 1120 ⁇ 1140°C, the heating time is 10.3 ⁇ 13min/cm, and the soaking time is 45min; the surface temperature of the slab and the core are uniform, and the original grain size is effectively controlled by the low-temperature heating system. Dimensions provide a guarantee for enhanced tissue performance;
  • the thickness of the blank to be warmed is set to 3.5 to 4.0 times of the finished product, and the reduction ratio of the rough rolling pass is 26%; the thickness of the blank to be warmed is increased, and the reduction between the finishing passes is improved, and further reduced by rolling means.
  • the effective rolling load to cooling interval is reduced from 35 to 40s to 18 to 23s, effectively reducing the finishing temperature, and the roller speed is increased from 0.6 to 0.9 m/s to 1.3 to 1.5 m/s. Effectively reduce the cooling time, appropriately increase the roll speed, reduce the tissue transition time, and effectively refine the grain size of the tissue;
  • the reddening temperature is 165 ⁇ 190°C; the applicant has found through research that the grain size is improved by the laminar cooling system. Because the difference between the surface temperature of the thick plate and the core temperature is large, when the reddening temperature is greater than 300 degrees, the steel plate After reaching the cooling bed, the temperature will rise by more than 100 degrees. During the cooling process of the cooling bed, the temperature rise will lead to the weakening of the dislocation of the tissue and the aggravation of the banded structure, which will affect the mechanical properties. By setting the red plate return temperature of 165-190 °C, it is ensured.
  • the core structure forms fine acicular ferrite, and the structure is uniform, and there is no phenomenon that the temperature recovers in the cold bed, weakening the dislocation of the tissue, deteriorating the band structure, and refining the crystal
  • the particle size is improved when the uniform fine crystals are obtained while the band structure is obtained.
  • the invention proceeds from the viewpoint of the grain size of the tissue to solve the stability of the performance of the extremely thick and wide variety, and is suitable for the pipeline steel plate with the width of 3500-5000 mm and the thickness of 25-40 mm, and the design of the low carbon, low phosphorus and low sulfur is more Conducive to the core structure of the slab, effectively reducing the brittleness of the product; using high Nb design to achieve solid solution strengthening, effectively refining the microstructure of the grains in the form of carbides, oxides, can effectively increase tempering stability; Mo can improve Hardenability and tempering stability of thick gauge products; Ni can improve the strength and toughness of steel, effectively reduce the brittle temperature of steel, and reasonable composition design can improve the hardenability of thick slabs, which is conducive to uniform and refined microstructure.
  • Organized grains mainly adopt low temperature heating system, 3.5 to 4.0 times the thickness of the blank to be warmed, suitable rolling schedule, reach the reddening temperature of less than 200 degrees by suitable roll speed and ultra-fast cooling technology, and eliminate by strong cold
  • the unfavorable factor of the band structure is that the dense penticular and acicular ferrite structure is obtained at 1/4 of the steel plate and the core, thereby obtaining a uniform microstructure and fine crystal strengthening structure, thereby improving product performance.
  • the invention adopts a low carbon design to increase the toughness of the product, and the alloy adopts Nb, Ti, Cr, Mo, Cu design to increase the precipitation strength during the rolling process, and the heating temperature of the billet adopts a low temperature heating system, and the odd pass rolling System, low water, less than 200 degrees red, the laminar cooling system effectively eliminates the band structure and meets the requirements of the fine grain structure of the core.
  • the invention successfully solves the manufacturing difficulty of the uneven structure of the wide and thick pipeline steel, effectively refines the grain size of the structure, improves the mechanical properties of the product, and greatly improves the economic benefit.
  • FIG. 1 is a metallographic structure diagram of a side portion of an embodiment of the present invention.
  • Figure 2 is a metallographic structure diagram at 1/4 of the embodiment of the present invention.
  • FIG. 3 is a metallographic structure diagram of a core portion of an embodiment of the present invention.
  • This embodiment is a production process of an ultra-fine grain wide and thick pipeline steel plate, comprising the following steps:
  • the weight percentage components of ultra-fine grain wide and thick pipeline steel sheets are: C: 0.04%, Si: 0.15%, Mn: 1.3%, P: 0.008%, S: 0.001%, Nb: 0.03%, Ti: 0.006%, Ca : 0.0005%, Al: 0.015%, Ni: 0.10%, Cr: 0.10%, Mo: 0.08%, Cu: 0.136%, the balance being Fe and unavoidable impurities;
  • the heating temperature of the slab is set to 1120 ° C, the heating time is 10.3 min / cm, and the soaking time is 45 min;
  • the thickness of the warm billet is set to 3.5 times of the finished product, and the reduction ratio of the rough rolling pass is 26%;
  • the effective rolling load to cooling interval is reduced from 35-40s to 18s, effectively reducing the finishing temperature, and the roller speed is increased from 0.6-0.9m/s to 1.3m/s, effectively reducing the cooling time. , appropriately increase the roller speed, reduce the tissue transition time, and effectively refine the grain size of the tissue;
  • the reddening temperature is 180 °C.
  • This embodiment is a production process of an ultra-fine grain wide and thick pipeline steel plate, comprising the following steps:
  • the weight percentage components of ultra-fine grain wide-thickness pipeline steel plates are: C: 0.048%, Si: 0.248%, Mn: 1.53%, P: 0.009%, S: 0.002%, Nb: 0.032%, Ti: 0.013%, Ca : 0.0013%, Al: 0.032%, Ni: 0.20%, Cr: 0.14%, Mo: 0.136%, Cu: 0.137%, the balance being Fe and unavoidable impurities;
  • the heating temperature of the slab is set to 1130 ° C, the heating time is 12 min / cm, and the soaking time is 45 min;
  • the effective rolling load to cooling time interval is reduced from 35-40s to 20s, effectively reducing the finishing temperature, and the roller speed is increased from 0.6-0.9m/s to 1.4m/s, effectively reducing the cooling time. , appropriately increase the roller speed, reduce the tissue transition time, and effectively refine the grain size of the tissue;
  • the red return temperature is 169 °C.
  • This embodiment is a production process of an ultra-fine grain wide and thick pipeline steel plate, comprising the following steps:
  • the weight percentage components of ultra-fine grain wide and thick pipeline steel plates are: C: 0.045%, Si: 0.253%, Mn: 1.54%, P: 0.007%, S: 0.002%, Nb: 0.036%, Ti: 0.015%, Ca : 0.0025%, Al: 0.05%, Ni: 0.30%, Cr: 0.15%, Mo: 0.138%, Cu: 0.138%, the balance being Fe and unavoidable impurities;
  • the heating temperature of the slab is set to 1130 ° C, the heating time is 12.3 min / cm, and the soaking time is 45 min;
  • the effective rolling load to cooling interval is reduced from 35-40s to 21s, effectively reducing the finishing temperature, and the roller speed is increased from 0.6-0.9m/s to 1.3m/s, effectively reducing the cooling time. , appropriately increase the roller speed, reduce the tissue transition time, and effectively refine the grain size of the tissue;
  • the red return temperature is 186 °C.
  • This embodiment is a production process of an ultra-fine grain wide and thick pipeline steel plate, comprising the following steps:
  • the weight percentage components of ultra-fine grain wide and thick pipeline steel plates are: C: 0.070%, Si: 0.30%, Mn: 1.8%, P: 0.005%, S: 0.001%, Nb: 0.07%, Ti: 0.02%, Ca : 0.0040%, Al: 0.036%, Ni: 0.15%, Cr: 0.30%, Mo: 0.18%, Cu: 0.131%, the balance being Fe and unavoidable impurities;
  • the heating temperature of the slab is set to 1140 ° C, the heating time is 13 min / cm, and the soaking time is 45 min;
  • the thickness of the warm billet is set to 4.0 times of the finished product, and the pass reduction rate of the rough rolling pass is 26%;
  • the effective rolling load to cooling interval is reduced from 35 to 40s to 23s, effectively reducing the finishing temperature, and the roller speed is increased from 0.6-0.9m/s to 1.5m/s, effectively reducing the cooling time. , appropriately increase the roller speed, reduce the tissue transition time, and effectively refine the grain size of the tissue;
  • the reddening temperature is 175 °C.
  • Figs. 1, 2 and 3 The metallographic structure of Figs. 1, 2 and 3 was obtained by the above examples. It can be seen from the figure that 1/4, the core structure is uniform and fine, and the microstructure is mainly composed of bainite and acicular ferrite, and the grain size of the tissue is observed. Rating 12th level.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne une plaque d'acier de pipeline de gande épaisseur à grain ultra-fin et une technologie de production de celle-ci. La plaque d'acier comprend les constituants suivants en pourcentage en poids: C: 0,040 à 0,070%; Si: 0,15 à 0,30%; Mn: 1,30 à 1,80%; P ≤ 0,015%; S ≤ 0,005%; Nb: 0,030 à 0,07%; Ti: 0,006 à 0,020%; Ca: 0,0005 à 0,0040%; Al: 0,015 à 0,050%; Ni: 0,10 à 0,30%; Cr: 0,10 à 0,30%; Mo: 0,08 à 0,18%; Cu: 0,1 à 0,20%; et le reste étant constitué de Fe et d'impuretés inévitables. La bainite à structure uniforme et la ferrite aciculaire sont obtenues par amélioration raisonnable d'une technologie de chauffage d'ébauche, optimisation d'un processus de laminage et perfectionnement de la technologie de refroidissement laminaire, ce qui assure la stabilisation de la structure et des performances, et répond aux exigences de performance d'un acier fin de grande épaisseur pour pipeline.
PCT/CN2018/093096 2017-06-27 2018-06-27 Technologie de production de plaque d'acier de pipeline de gande épaisseur à grain ultra-fin Ceased WO2019001464A1 (fr)

Priority Applications (1)

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RU2019135632A RU2734901C1 (ru) 2017-06-27 2018-06-27 Способ производства ультрамелкозернистой толстолистовой трубопроводной стали

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CN201710499699.4 2017-06-27
CN201710499699.4A CN107385326B (zh) 2017-06-27 2017-06-27 一种超细晶粒宽厚管线钢板的生产工艺

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CN115323265A (zh) * 2022-07-15 2022-11-11 南京钢铁股份有限公司 一种超细晶钢板及其制备方法

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CN107385326B (zh) * 2017-06-27 2019-06-04 南京钢铁股份有限公司 一种超细晶粒宽厚管线钢板的生产工艺
CN108070789B (zh) * 2018-01-17 2020-04-03 山东钢铁集团日照有限公司 屈服强度不小于480MPa级超细晶特厚钢及制备方法

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WO2011148755A1 (fr) * 2010-05-27 2011-12-01 新日本製鐵株式会社 Procédé de fabrication d'une tôle d'acier haute résistance pour une structure soudée
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CN115323265B (zh) * 2022-07-15 2024-03-19 南京钢铁股份有限公司 一种超细晶钢板及其制备方法

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