WO2021058003A1 - 一种管线钢及其制造方法 - Google Patents

一种管线钢及其制造方法 Download PDF

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WO2021058003A1
WO2021058003A1 PCT/CN2020/118447 CN2020118447W WO2021058003A1 WO 2021058003 A1 WO2021058003 A1 WO 2021058003A1 CN 2020118447 W CN2020118447 W CN 2020118447W WO 2021058003 A1 WO2021058003 A1 WO 2021058003A1
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temperature
pipeline steel
steel
rolling
cooling
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French (fr)
Chinese (zh)
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章传国
王波
孙磊磊
郑磊
吴扣根
沈燕
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宝山钢铁股份有限公司
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Priority to JP2022519416A priority Critical patent/JP2022550119A/ja
Priority to KR1020227012885A priority patent/KR20220065020A/ko
Priority to DE112020004648.6T priority patent/DE112020004648T5/de
Publication of WO2021058003A1 publication Critical patent/WO2021058003A1/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
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/32—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for gear wheels, worm wheels, or the like
    • 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
    • C22C38/002—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
    • C22C38/06—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to pipeline steel, in particular to a pipeline steel and a manufacturing method thereof.
  • Japan's JFE company uses online heat treatment equipment and applies the HOP process to improve the uniformity of the structure in the thickness direction of the steel plate, which is conducive to improving the toughness of thick-gauge pipeline steel and obtaining uniform mechanical properties, while also improving the ovality of the steel pipe.
  • the steel used for submarine pipelines at home and abroad mainly focuses on high-strength and high-toughness research, but there are few studies on high plasticity.
  • the requirements of high uniform elongation are proposed for the strain-designed land pipelines.
  • the design mainly adopts dual-phase structure control, and the vault-type stress-strain curve is obtained through the combination of soft and hard phases. Better work hardening rate, thereby improving the uniform deformation ability of steel.
  • the representative process directions include the ferrite + lower bainite dual phase structure obtained by the relaxation + controlled cooling process adopted by Chinese companies, and the MA component + bainite dual phase structure obtained by the online heat treatment HOP process adopted by JFE in Japan Both of these two types of microstructures can obtain high uniform elongation, but due to the existence of the dual-phase interface, the low-temperature impact toughness of steel is significantly reduced, which is not conducive to the safety of steel crack arrest.
  • European Patent No. EP2105513B1 discloses a method for manufacturing thick gauge and high toughness pipeline steel with a yield strength of 450MPa.
  • a low-C, low-Mn, and low-Nb microalloying design method By adopting a low-C, low-Mn, and low-Nb microalloying design method, combining low-temperature heating technology and controlled rolling and controlled cooling technology, A microstructure dominated by refined polygonal ferrite is obtained, the volume ratio of ferrite is 40-90%, and the ferrite grain size is less than or equal to 10 ⁇ m.
  • the pipeline steel prepared by the invention has excellent toughness.
  • Chinese patent CN101611163A discloses a kind of anti-aging dual-phase pipeline steel with yield strength ⁇ 400MPa, tensile strength ⁇ 500MPa, and yield ratio ⁇ 0.90. It adopts C-Mn basic composition and alloyed composition design. Two-stage cooling rate control obtains that the first phase is ferrite, and the second phase is one or more of pearlite, upper bainite, lower bainite, granular bainite or martensite, which can make the steel The uniform elongation rate reaches 8% and above.
  • the US patent US20120247606A1 discloses the composition and process plan of a X80 grade 6-16mm thin gauge pipeline steel. It adopts a low C high Nb and Mo alloying design without adding other alloying elements. The process adopts 675 ⁇ 715°C low temperature finishing rolling. And the air cooling process of 1 ⁇ 2°C/s, the pipeline steel with the strength level of 80Ksi can be obtained, and it has good weldability.
  • Australian patent AU2006305841A1 discloses a manufacturing method of dual-phase steel with a tensile strength of 900 MPa and a longitudinal yield ratio ⁇ 0.85. It adopts a low C, high Mn and Nb, Mo alloying composition design, and obtains 10-60 through process control. % Of refined ferrite with a grain size of ⁇ 5 ⁇ m, and the remaining structure is one or more mixed structures such as refined martensite, lower bainite, degraded upper bainite, and granular bainite.
  • Chinese patent CN109023068A discloses a manufacturing method of NbC nanoprecipitation strengthened X80 high-plasticity pipeline steel plate. It adopts a microalloyed composition design of medium C, low Mn and high Nb, through controlled rolling, controlled cooling process, and Subsequent solution treatment at 1180 to 1220°C and isothermal treatment at 670 to 710°C to control the precipitation of NbC to 0.05 to 0.20% to obtain X80 pipeline steel with a yield strength of 470Mpa, high plasticity and high toughness.
  • Chinese patent CN101343715B discloses a method for manufacturing large-strain pipeline steel pipes with a yield strength of 650MPa.
  • the composition adopts a medium-C, low-Mn, and high-alloy B-containing design method.
  • ferrite is obtained + Acicular ferrite + MA and other complex structure, can produce steel pipes with a yield strength of 650-680MPa and a uniform elongation of 12-15%.
  • the purpose of the present invention is to design a high-plasticity thick gauge pipeline steel and its manufacturing method, the yield strength R t0.5 is 450-635MPa, the tensile strength R m is 520-780MPa, especially the full-size Charpy at -20°C
  • the impact energy AKv is higher than 275J
  • the -20°C full wall thickness DWTT shear fracture area percentage SA is greater than 85%
  • its longitudinal uniform elongation Uel ⁇ 8% and it is manufacturable. It can be used for submarine pipelines, crossing pipelines and polar regions.
  • Pipeline construction is mainly used for long-distance transportation of natural gas.
  • a high-plasticity thick-gauge pipeline steel whose composition weight percentages are: C: 0.03 ⁇ 0.10%, Si: 0.1 ⁇ 0.5%, Mn: 1.51 ⁇ 1.85%, P ⁇ 0.015%, S ⁇ 0.002%, Cr: 0.05 ⁇ 0.3%, Mo: 0.05 to 0.20%, Cu: 0.06 to 0.3%, Ni: 0.17 to 0.50%, Nb: 0.05 to 0.10%, Ti: 0.005 to 0.02%, Ca: 0.001 to 0.005%, Al: 0.02 to 0.045 %, N ⁇ 0.006%, B ⁇ 0.0002%, O ⁇ 0.005%, the balance is Fe and unavoidable impurities; and, at the same time, meet:
  • the microstructure of the pipeline steel of the present invention is refined polygonal ferrite + acicular ferrite, and the proportion of the refined polygonal ferrite is 15-39%.
  • the yield strength R t0.5 of the pipeline steel of the present invention is 450-635 MPa, the tensile strength R m is 520-780 MPa, especially the full-scale Charpy impact energy AKv at -20°C is higher than 275J and the full wall thickness at -20°C DWTT shear fracture area percentage SA is greater than 85%, longitudinal uniform elongation Uel ⁇ 8%.
  • Carbon C The most basic strengthening element. Carbon dissolves in steel to form interstitial solid solution, which plays a role of solid solution strengthening, and forms carbides with strong carbide forming elements to precipitate, which plays a role of precipitation strengthening. But too high C is detrimental to the toughness and welding performance of steel, and at the same time reduces the plasticity of the steel; too low C reduces the strength of the steel. Therefore, C is controlled at 0.03 to 0.10%.
  • Silicon Si a solid solution strengthening element and also a deoxidizing element in steel, but too high content will deteriorate the welding performance of the steel, reduce the plasticity, and is not conducive to the removal of hot-rolled iron scale during the rolling process, so the content is controlled at 0.1-0.5 %.
  • Manganese Mn Improve the strength of steel through solid solution strengthening. It is the most important and economical strengthening element in steel to compensate for the strength loss caused by the decrease in C content. Mn is also an element that expands the ⁇ phase region, which can reduce the ⁇ transformation temperature of steel, help obtain fine phase transformation products, and improve the toughness of steel; but Mn is an element that is easy to segregate. When the content of Mn is high, During the casting process, Mn is easy to segregate in the center of the plate thickness, and the hard phase martensite structure is formed after the rolling is completed, which reduces the plasticity and low temperature toughness of the material. Therefore, the Mn content in the present invention is limited to 1.51 to 1.85%.
  • the carbon manganese product parameter J C ⁇ Mn C*Mn*10 4 needs to meet the requirements of 0.06 ⁇ J C ⁇ Mn ⁇ 0.14, J C When ⁇ Mn is less than 0.6, due to insufficient C and Mn content, the solid solution strengthening effect is not significant and the strength is low; when J C ⁇ Mn is greater than 0.14, the range of ⁇ austenite is reduced, which is not conducive to the diffusion and distribution of C and Mn elements. , Increase the tendency of segregation.
  • Chromium Cr an important element to improve the hardenability of steel, to ensure the uniformity of the structure and performance of the thickness of the thick steel plate, and can effectively improve the corrosion resistance of the steel; but too high chromium is added to the steel to increase the strength and Hardness, reduce elongation and reduction of area; when added at the same time with higher Mn, it is easy to generate compound to produce cracks, and severely deteriorate welding performance.
  • the Cr content should be limited to 0.05-0.3%.
  • Molybdenum Mo an element that expands the ⁇ phase region, can reduce the ⁇ transformation temperature of steel, can obtain a finer transformation structure, and improve the toughness of the steel; at the same time, a small amount of Mo can improve the hardenability of the steel and improve the thickness direction The uniformity of the organization.
  • Mo content is controlled by 0.05 to 0.20%.
  • Copper Cu It can increase the strength of steel through solid solution strengthening, and improve the resistance to atmospheric corrosion; too high Cu is prone to copper brittleness, which has a negative impact on hot workability.
  • the Cu content is controlled to be 0.06-0.3%.
  • Nickel Ni can increase the strength of steel through solid solution strengthening.
  • the addition of Ni can improve the hot brittleness caused by Cu in steel; it can expand the austenite zone and increase the stability of austenite, which is beneficial to plasticity and toughness.
  • the control range of Ni content is all 0.17 to 0.50%.
  • Niobium Nb It is one of the important elements of low-carbon microalloyed steel.
  • the Nb dissolved in the hot rolling process induces precipitation to form Nb(N, C) particles, which pin the grain boundaries to inhibit the growth of deformed austenite and inhibit renewal.
  • the solid solution Nb is dispersed and precipitated in the matrix as the second phase particles NbC after coiling, which plays a role of precipitation strengthening.
  • the dispersion and precipitation effect of too low Nb content is not obvious, and it does not play the role of refining grains and strengthening the matrix; too high Nb content inhibits the occurrence of recrystallization of the steel plate core, which is not conducive to Grain Refinement.
  • the solid solution of Nb is related to the content of C. If the content of C is too high, the amount of solid solution of Nb is small, and the effect of precipitation strengthening and grain refinement cannot be achieved; if the content of C is too low, the grain boundary will be weakened, while the content of Nb is too low for precipitation strengthening Not obvious.
  • the Nb content should be limited to 0.05 to 0.10%.
  • Titanium Ti is a strong carbonitride forming element. Undissolved carbonitrides of Ti can prevent the growth of austenite grains when steel is heated. TiN precipitated during rough rolling in the high-temperature austenite zone can be Effectively inhibit the growth of austenite grains. In addition, during the welding process, the TiN particles in the steel can significantly prevent the grain growth in the heat-affected zone, thereby improving the welding performance of the steel plate and at the same time have a significant effect on improving the impact toughness of the welding heat-affected zone. In the present invention, the Ti content is controlled at 0.005 to 0.02%.
  • Nitrogen N In microalloyed steel, an appropriate nitrogen content can inhibit the coarsening of slab grains during reheating by forming high melting point TiN particles and improve the strength and toughness of the steel. However, when the N content is too high, the high concentration of free N atoms pin dislocations after aging, which significantly increases the yield strength, and significantly decreases the plasticity and toughness. Therefore, in the present invention, N ⁇ 0.006% is controlled.
  • Oxygen O For low-alloy pure steel smelting, deoxidation treatment is required at the end of the smelting process to reduce bubbles and oxide inclusions generated during the casting process, improve the internal quality of the steel, and improve the low-temperature impact toughness and dynamic tear resistance of the finished steel plate performance.
  • the oxygen content is higher than 50 ppm, internal defects such as inclusions and pores increase significantly, which reduces the plasticity and toughness of the steel. Therefore, in the present invention, O ⁇ 0.005% is controlled.
  • Sulfur and phosphorus are the unavoidable impurity elements in steel, hope the lower the better.
  • Ultra-low sulfur (less than 20ppm) and Ca treatment are used to control the form of sulfide inclusions, while controlling the P content below 150ppm, which can ensure that the invention steel has good low-temperature impact toughness.
  • Ca treatment can control the form of sulfide, improve the anisotropy of the steel sheet, and improve the low temperature toughness. To ensure the best effect, the control range of Ca is 0.0010 to 0.0050%.
  • Aluminum (A1) It is an element added to steel for deoxidation. Adding a proper amount of Al is beneficial to refine grains and improve the toughness of steel.
  • the control range of Al content in the present invention is 0.02-0.045%.
  • B Boron
  • a lower C content and higher Nb microstructure are adopted. Alloying composition design; combined with low-temperature rough rolling and finishing rolling processes to give full play to the deformation-induced phase transformation mechanism to promote ferrite phase transformation; through appropriate cooling rate and cooling stop temperature control, refined polygonal ferrite +
  • the acicular ferrite microstructure has the comprehensive mechanical properties of high strength, high toughness and high plasticity, and has good deformability.
  • the method for manufacturing high-plasticity thick-gauge pipeline steel according to the present invention includes the following steps:
  • Intermediate billet thickness 3t ⁇ 5t, t is the thickness of pipeline steel, unit mm;
  • Finish rolling start-rolling temperature 750 ⁇ 810°C
  • finishing rolling temperature 740 ⁇ 800°C
  • Water cooling temperature T start 620 ⁇ 720°C
  • water cooling stop temperature T stop 150 ⁇ 530°C
  • the heating temperature for reheating the slab in step 2) is 1110-1150°C.
  • step 3 the rough rolling opening temperature is 960-990°C, the single-pass reduction rate of the final rough rolling pass is ⁇ 14%; the intermediate billet thickness is 4 ⁇ 4.5t; the finishing rolling opening temperature is 770-800°C, The finishing temperature of rolling is 750 ⁇ 780°C.
  • step 4 the cooling is controlled, the water-cooling opening and cooling temperature T start is 660-700°C, and the water-cooling stop temperature T stop is 200-350°C.
  • the 28-40mm thick high-plasticity pipeline steel is finally obtained.
  • Cooling after rolling is a key process that determines the phase transformation structure.
  • the target refined polygonal ferrite + acicular ferrite phase transformation structure can be controlled by controlling the water-cooling opening temperature T start , the water-cooling stop temperature T stop and the water-cooling cooling speed V c Obtained, each cooling parameter must conform to the above relationship.
  • the water-cooled opening and cooling temperature T start is higher than 720°C, the precipitation power of the soft-phase polygonal ferrite is small, which will lead to high strength of the steel, and if the soft-phase polygonal ferrite is lower than 620°C, the soft-phase polygonal ferrite is coarse and the proportion is too high, which will lead to the strength.
  • the water cooling stop temperature T stop mainly determines the hardness of the hard phase acicular ferrite. When it is higher than 530°C, the dislocation density is low, the hardness is low, and the strength is low. When it is below 150°C, it is easy to form horses.
  • the microstructure causes the dislocation density to be too high, the hardness is high, and the plasticity decreases;
  • the water-cooling cooling rate V c is mainly used to match the water-cooling opening and stopping temperature to control the phase change structure type and the key parameter of the phase ratio, and the water cooling stopping temperature T stop is positively correlated and negatively correlated with the water-cooled opening and cooling temperature T start.
  • the present invention is mainly aimed at high-plasticity pipeline steel products with a yield strength of 450MPa.
  • the composition is designed with low C, high Mn and Nb microalloying, combined with low temperature controlled rolling in the recrystallization rolling stage.
  • the process suppresses the grain size of the original austenite, and through a relatively low water cooling rate control, a refined polygonal ferrite + acicular ferrite phase transformation grain size is obtained, and the proportion of polygonal ferrite is controlled at 40% Below, it has better plasticity and toughness.
  • the present invention adopts a relatively high Nb and low B design to give full play to the grain refinement and suppress the low-temperature transformation structure. Combining the low-temperature rolling process and the low cooling rate process, a refined polygonal shape is finally obtained.
  • the ferrite + acicular ferrite structure not only has a lower yield ratio, higher uniform deformation ability, but also has better low temperature toughness.
  • the present invention is mainly aimed at pipeline steel products of 28mm and above with a yield strength R t0.5 of 450-635MPa and a tensile strength R m of 520-780MPa.
  • the composition is low in C,
  • the present invention is mainly aimed at high plastic pipeline steel products with a yield strength of 450MPa and a longitudinal uniform elongation Uel ⁇ 8%.
  • the composition has a low C and low Nb design, combined with recrystallization rolling.
  • the low-temperature controlled rolling process in the production stage suppresses the grain size of the original austenite, and through the relatively low water cooling rate control, a refined polygonal ferrite + acicular ferrite phase transformation grain size is obtained. Good deformability.
  • the present invention mainly adopts the Nb microalloying design with low C and high Mn, through lower recrystallization rolling temperature and low temperature non-recrystallization rolling, combined with reasonable cooling rate control, to obtain fine The microstructure of modified polygonal ferrite + acicular ferrite to ensure the high strength, high plasticity and toughness of the steel, without solid solution and isothermal heat treatment, and low cost.
  • the difference from Chinese patent CN101343715B is that the present invention mainly adopts the Nb microalloying design with low C and high Mn, through lower recrystallization rolling temperature and low temperature non-recrystallization rolling, combined with reasonable cooling rate control, to obtain fine The microstructure of modified polygonal ferrite + acicular ferrite to ensure the high strength, high plasticity and toughness of the steel.
  • the amount of alloy addition is small, and online heat treatment is not required, and the cost is low.
  • the present invention adopts a low-temperature heating process to inhibit the growth of reheated austenite grains and control the grain size from the source.
  • the heating temperature is too high, the high-temperature precipitation phase of the microalloying element Ti will undergo solid solution, which weakens the grain boundary pinning effect, the grain boundary migrates and merges, and the grains are significantly coarsened, which is not conducive to low-temperature toughness;
  • the present invention adopts a low-temperature rolling process at the recrystallization stage to inhibit the growth of recrystallized grains.
  • the recrystallization temperature is higher, the Gibbs free energy of the grain boundary is higher, and the driving force for the migration of the recrystallized grains is greater, which promotes the merger of the grains to reduce the Gibbs free energy of the grain boundary, thereby making the recrystallized crystal Grain coarsening.
  • the present invention adopts an appropriate amount of Nb alloy design promotion, combined with recrystallization low temperature rolling, and refines the recrystallization grain size.
  • Higher Nb will increase the recrystallization temperature, which is not conducive to the occurrence of recrystallization; while lower Nb will reduce the recrystallization temperature, increase the deformation resistance of recrystallization low-temperature rolling, and place high requirements on equipment capabilities;
  • the invention adopts a refined polygonal ferrite + acicular ferrite microstructure design, and improves the plastic deformation ability of the pipeline steel through the soft-phase polygonal ferrite structure design, so that the longitudinal uniform elongation of the pipeline steel Uel ⁇ 8%; and use high-density and large-angle grain boundaries to improve crack propagation resistance, thereby effectively improving the dynamic tear resistance of steel.
  • Fig. 1 is the microstructure of the steel of the embodiment of the present invention (the plate thickness is 1/2 position).
  • Fig. 2 is the microstructure of the steel of the embodiment of the present invention (the position of plate thickness 1/4).
  • the chemical composition of the design examples is shown in Table 1, and the manufacturing process of the examples is shown in Table 2.
  • the mechanical properties obtained in each example are shown in Table 3.
  • the tensile performance test of the invention adopts the Zwick Z330 tensile testing machine, the test standard is ASTM A370, the impact toughness test adopts the Zwick PSW750 impact tester, the test standard is ASTM A370, the full wall thickness of -20°C DWTT shear fracture area percentage SA adopts The 40,000-joule impact tester ZBC2404 was tested, and the test standard was API RP 5L3.
  • the components and processes designed according to the present invention can meet the target performance requirements, have good comprehensive mechanical properties, and have a low carbon equivalent, which is beneficial to improve the performance of steel pipe forming welding and field girth welding.
  • the composition of the invention is simple, the process window is wide, and the manufacturability is strong.
  • the high plastic thick gauge pipeline steel of the present invention is mainly used for subsea pipelines, pipelines passing through seismic belts and other special demand and harsh environment areas.
  • the plastic deformation capacity of the pipeline is improved through organizational control, and the pipeline's bearing weight is improved. Resist sports ability to ensure the safety and security of service.
  • high-plastic thick-gauge pipeline steel With the exploitation of oil and gas resources from inland to ocean, polar frozen soil, frequent geological movement and other areas, high-plastic thick-gauge pipeline steel will have good application prospects.

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  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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