WO2014114111A1 - 一种500MPa级低屈强比直缝焊钢管及其制造方法 - Google Patents

一种500MPa级低屈强比直缝焊钢管及其制造方法 Download PDF

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WO2014114111A1
WO2014114111A1 PCT/CN2013/084872 CN2013084872W WO2014114111A1 WO 2014114111 A1 WO2014114111 A1 WO 2014114111A1 CN 2013084872 W CN2013084872 W CN 2013084872W WO 2014114111 A1 WO2014114111 A1 WO 2014114111A1
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Prior art keywords
strip
yield ratio
slab
cooled
steel tube
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PCT/CN2013/084872
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English (en)
French (fr)
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田青超
史宏德
王怀忠
王起江
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宝山钢铁股份有限公司
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Priority to US14/761,365 priority Critical patent/US9663840B2/en
Priority to DE112013006498.7T priority patent/DE112013006498T5/de
Priority to JP2015544327A priority patent/JP6258959B2/ja
Publication of WO2014114111A1 publication Critical patent/WO2014114111A1/zh

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • B21C37/08—Making tubes with welded or soldered seams
    • B21C37/0807—Tube treating or manipulating combined with, or specially adapted for use in connection with tube making machines, e.g. drawing-off devices, cutting-off
    • B21C37/0811—Tube treating or manipulating combined with, or specially adapted for use in connection with tube making machines, e.g. drawing-off devices, cutting-off removing or treating the weld bead
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
    • B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or welding
    • B23K31/027—Making tubes with soldering or welding
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/085—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
    • F16L9/00—Rigid pipes
    • F16L9/02—Rigid pipes of metal
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
    • F16L9/00—Rigid pipes
    • F16L9/17—Rigid pipes obtained by bending a sheet longitudinally and connecting the edges
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints

Definitions

  • the invention relates to a method for manufacturing a steel pipe for construction, in particular to a straight seam welded steel pipe with a yield strength of 500 MPa and a low yield ratio excellent in welding performance and a manufacturing method thereof.
  • China's construction steel structure has long used low carbon steel and low alloy steel with yield strength of 235 ⁇ 345MPa.
  • the yield strength grade of medium-low alloy steel GB50017-2003 has been extended to 460MPa.
  • the use of high-strength grade steel pipes for construction aims to reduce the section size of steel structures and save investment.
  • thin-section steel structures are prone to local and overall yield instability problems, which limits the thinning of steel structure sections and high strength grades.
  • the advantages of steel for construction cannot be exploited. Therefore, it is imperative to develop high-strength grade steel for construction to solve the problem of yield instability of thin-section steel structures.
  • the high-strength steel pipe concrete structure in which the steel pipe and the concrete work together is formed by filling the concrete in the thin-section high-strength steel pipe, which can significantly improve the rigidity and solve the structural yield instability problem. Because the high-strength steel pipe concrete structure can take advantage of high-strength steel and high-strength concrete, saving investment and speeding up construction progress, it is a technological growth point for developing high-strength grade construction steel market.
  • welded pipes Compared with seamless pipes, welded pipes have the characteristics of high production efficiency, good dimensional accuracy, wide specification range and low cost. Therefore, they are the first choice of manufacturers and oilfield users, and have been favored by the market.
  • the production process of ERW casing is: steel casting, continuous casting, hot rolling, coiling, sheet rolling, head-to-tail shearing, butt welding, strip forming, in-line welding, weld heat treatment or whole tube heat treatment, one tube processing, one factory inspection, etc. .
  • the coil head-to-tail shear butt welding process is a key process for achieving continuous production of multiple rolls and reflecting the production efficiency of ERW welded pipes.
  • the carbon equivalent of the material required for butt welding of the coil head must be low, the steel sheet may be broken, which seriously affects the production efficiency.
  • high-strength steel pipe centrifugal concrete members are often used as construction piles to withstand extreme impact loads. Therefore, steel pipes with good toughness and low yield ratio are required, and welds are required to have excellent mechanical properties.
  • the carbon equivalent Ceq requirement of such a material cannot be greater than 0.4.
  • the patent JP56035749A proposes a method of the ERW sleeve, which does not contain the above elements of strengthening elements such as Ti, Nb, V, Cr, etc., although high strength requirements can be achieved, and Si is as high as 1%, during welding. Welds are prone to gray spots, which seriously affect the quality of the weld, and the carbon equivalent of up to 0.8 cannot achieve shear butt welding.
  • Japanese patents JP09029460A, JP54097523A, JP56069354A, and JP59047364A all add Cu, and may also meet the requirements for producing high-strength bushings, but since Cu is substantially insoluble in ferrite at room temperature, it is in the form of ⁇ -Cu or face-centered cubic ⁇ -Cu. Precipitation makes the strengthening effect of steel very sensitive to the cooling rate. In the process of controlled rolling and controlled cooling of hot rolled sheet production, the performance of hot rolled sheet is difficult to control stably;
  • ⁇ Patent JP57131346A provides a welded pipe resistant to groove corrosion.
  • more than one type of Cu, Ni, Al, Cr or even harmful elements As, Sb, Sn are added on the basis of controlling the low S content.
  • Bi or the like, or further adding one or more of Ti, Nb, Zr, V, etc. does not at all meet the requirements of the 500 MPa high strength and toughness of the present invention.
  • Japanese patents JP58093855A and JP59096244A all contain expensive Ni elements, and the alloys are expensive.
  • Japanese companies JP57131346A and JP58093855A have higher Si contents, and it is difficult to obtain excellent weld bead properties.
  • the steel types involved in the Chinese patents CN200710038400.1 and CN200310104863 can achieve the performance requirements of high strength and low yield ratio, but because of the high C content, the carbon equivalent is greater than 0.4, which can only meet the requirements of shear butt welding. Production can be carried out continuously, but it is difficult to obtain excellent weld performance and cannot withstand the extreme impact loads that the pile pipe is subjected to.
  • the steel grade provided by the Chinese patent CN200310104863 can also reach 500 MPa, but because the composition is too simple, the desired mechanical properties can only be achieved at a coiling temperature of 430-470 °C. At such low coiling temperatures, the performance of hot rolled sheets is more difficult to achieve stable control. Summary of invention
  • the object of the present invention is to provide a 500MPa grade low yield ratio straight seam welded steel pipe and a manufacturing method thereof, which meet the characteristics of the load applied to the pile foundation for construction, and have the characteristics of excellent welding performance, high strength and toughness, low yield ratio, etc.
  • the yield strength is greater than 500 MPa, and the yield ratio is less than 0.85.
  • the invention adopts low carbon content in material design, maintains proper Mn content, adds appropriate amount of microalloying elements such as Ti and Nb, and improves strength through the action of controlled rolling and controlled cooling, and finally obtains high strength and toughness and low yield. Stronger than steel pipe.
  • the steel of the 500MPa grade low yield ratio straight seam welded steel pipe of the present invention has a component weight of the following:
  • the design component carbon equivalent Ceq is not more than 0.4%, which not only meets the requirements of shear butt welding, but also achieves excellent weld performance.
  • the sufficiency of the carbon content is 0. 11-0. 16%, the C content is 0. 11-0. .
  • the Si is dissolved in the ferrite to increase the yield strength of the steel, the content should not be too high, should be controlled at 0. 15-0. 35%.
  • the Mn content is 0. 8-1.
  • the Mn content is 0. 8-1.
  • the Mn content is 0. 8-1. .5%.
  • V The vanadium carbonitride precipitates in the ferrite and has the effect of stabilizing the ferrite to delay the bainite transformation. It can improve the strength of the material during the control of cooling and improve the mechanical properties of the weld. The percentage is 0. 06-0. 15%.
  • A1 The conventional deoxidation and nitrogen-fixing element, the formation of A1N, the austenite grains can be refined, and the toughness is increased.
  • Ti Strong carbonitride forming element, TiN and TiC can refine austenite grains during soaking and reheating, improve the mechanical properties of the weld; if the content is too high, it is easy to form coarse TiN. Not for the purpose of adding. 05% ⁇ By weight percentage, should be used 0-0. 05%.
  • Nb Strong carbonitride forming element, which can delay the recrystallization of austenite during hot rolling to achieve grain refinement. During reheating, it can hinder austenite grain growth and increase the toughness of the material. 05% ⁇ The content should be 0-0. 05%.
  • the molten steel is smelted by a converter or an electric furnace, and cast into a slab; the slab is heated by 1200-130 CTC and rolled into a strip, and the final rolling temperature of the strip is between 840 and 940 °C; Board
  • the layer is cooled by laminar flow, and the laminar cooling adopts the latter stage cooling mode.
  • the number of cooling water valves that are not opened in the front section accounts for 15%-40% of the total number of cooling water valves, and is cooled to 50CT560 °C in 30 s. After the sheet is rolled, the stack is slowly cooled; after welding, it is heat treated by the weld and the heating temperature is 950 ⁇ 50 °C.
  • the chemical composition of the invention is microalloyed carbon-manganese steel, and the alloying element is fully dissolved in austenite at a rolling temperature range of 130 (T840 °C), and the latter cooling method is advantageous for the length of austenite grains.
  • T840 °C rolling temperature range of 130
  • Large, rapid cooling of the water curtain inhibits the precipitation of carbides and the transformation of austenite to ferrite pearlite, which causes the supercooled austenite to undergo phase transformation and precipitation carbonization at 50 (T560 °C coiling temperature concentration).
  • the microstructure of the fine carbides of ferrite + dispersion distribution is obtained, which ensures that the material has high strength and low yield ratio.
  • the alloy composition of the invention has low carbon equivalent and low alloy content, and does not contain expensive alloy elements such as Mo and Ni.
  • the heat treatment of the steel pipe is not high, and has significant economic and social benefits.
  • Comparative example 2 900 25 550 580 710 0.82 40
  • the yield strength of the material is greater than 500 MPa, the yield ratio is less than 0.85, and the full-scale impact energy at 0 °C is greater than 100 J, and the mechanical properties are stable.
  • Comparative Example 1 After shear butt welding, coil forming, ERW pipe production, ERW high-strength steel pipe is produced through the process steps of weld heat treatment, and the strength of Examples 1-5 can meet the requirement of yield strength greater than 500 MPa.
  • the composition of Comparative Example 1 is simple, does not contain the V element, and is far below the requirement of a yield strength of more than 500 MPa at the coiling temperature of the present invention; the C content of Comparative Example 2 is high, and the impact toughness of the material is remarkably lowered, failing to satisfy the construction.
  • the stringent requirements of steel for pile foundation are impact loads. It can be seen that the ERW steel pipe satisfying the high performance requirement of the yield strength greater than 500 MPa can be stably produced by using the chemical composition and process system designed by the present invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • General Engineering & Computer Science (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatments In General, Especially Conveying And Cooling (AREA)

Abstract

一种500MPa级低屈强比直缝焊钢管及其制造方法，其成分重量百分比如下：C 0.11~0.16%、Si 0.15~0.35%、Mn 0.8~1.5%、V 0.06~0.15%、Al 0.002~0.04%、Ti 0 ~0.05%、Nb 0~0.05%、其余为 Fe和不可避免杂质；且，碳当量 Ceq不大于0.4。根据上述成分设计，钢水经转炉或电炉冶炼，并浇铸制成板坯；板坯经1200~1300℃加热后轧成板带，板带的终轧温度在840～940℃之间；轧后板带经层流冷却，层流冷却采取后段冷却方式，冷却到500~560℃温度区间卷取成板卷；焊接成型后，经焊缝热处理，加热温度为950±50℃。本发明钢管具有焊接性能优良、高强韧性、低屈强比等特点，其屈服强度大于500MPa，屈强比小于0.85。

Description

一种 500MPa级低屈强比直缝焊钢管及其制造方法 发明领域
本发明涉及建筑用钢管制造方法， 特别是一种焊接性能优良的屈服强度 500MPa级低屈强比直缝焊钢管及其制造方法。 背景技术
我国的建筑用钢结构长期使用屈服强度 235〜345MPa 的低碳钢和低合金 钢。 目前《钢结构设计规范》 GB50017-2003中低合金钢的屈服强度等级已经拓 展至 460MPa。 采用高强度等级建筑用钢管， 目的是减薄钢结构断面尺寸并节 省投资， 但是薄断面钢结构容易出现局部和整体屈服失稳问题， 从而限制了钢 结构断面尺寸的减薄， 使高强度等级建筑用钢材的优势不能得到发挥， 因此发 展高强度等级建筑用钢的当务之急是解决薄断面钢结构屈服失稳问题。 在薄断 面高强度等级钢管内填充混凝土形成钢管和混凝土共同工作的高强度钢管混 凝土结构， 可以显著提高其刚度， 解决结构屈服失稳问题。 由于高强度钢管混 凝土结构可以发挥高强度钢材和高强度混凝土的优势， 节省投资、 加快施工进 度， 是开拓高强度等级的建筑用钢市场有发展潜力的技术生长点。
相对于无缝管而言， 焊管具有生产效率高、 尺寸精度好、 规格范围宽、 成 本低等显著特点， 因此是生产厂家与油田用户的首选品种， 一直受到市场的青 睐。 ERW套管的生产工艺是： 炼钢一连铸一热轧成板卷一板卷头尾剪切对焊一 板带成型一在线焊接一焊缝热处理或整管热处理一管加工一出厂检验等。 板卷 头尾剪切对焊工序是实现多卷连续生产、体现 ERW焊管生产效率的关键工序。 但是由于板卷头尾对焊要求材料的碳当量须低， 否则容易造成钢板断带， 严重 影响生产效率。 不仅如此， 高强度钢管离心混凝土构件用做建筑用桩基往往承 受极大的冲击载荷， 因此在要求钢管具有良好的强韧性、 低屈强比的同时， 还 要要求焊缝具有优良的力学性能， 这样材料的碳当量 Ceq要求不能大于 0.4。
曰本专利 JP56035749A提出了 ERW套管的一种方法， 该套管成分中不含 Ti、 Nb、 V、 Cr等强化元素上述元素， 虽然可以实现高强度的要求， 而 Si高达 1%, 焊接时焊缝容易形成灰斑， 严重影响焊缝质量， 并且碳当量高达 0.8无法 实现剪切对焊。 日本专利 JP09029460A、 JP54097523A, JP56069354A 、 JP59047364A均 添加了 Cu, 也可能实现生产高强度套管的要求， 但是由于 Cu在室温基本不溶 于铁素体而以 ε -Cu 或面心立方 α -Cu 的形式析出， 使得钢的强化效果对于冷 却速度的敏感性很大， 在热轧板生产的控轧控冷过程中， 热轧板的性能难以稳 定控制；
曰本专利 JP57131346A提供一种抗沟槽腐蚀的焊管， 为了减少 MnS的生 成， 在控制低的 S含量的基础上， 添加一种以上 Cu、 Ni、 Al、 Cr甚至有害元 素 As、 Sb、 Sn、 Bi等， 或进一步添加一种以上 Ti、 Nb、 Zr、 V等， 根本不能 实现本发明 500MPa 高强韧性的要求。 日本专利 JP58093855A, JP59096244A 都含有昂贵的 Ni 元素， 合金成本较高， 另外日本专利 JP57131346A、 JP58093855A 的 Si 含量较高， 难以获得优良的焊缝性能。 而中国专利 CN200710038400.1、 CN200310104863 所涉及的钢种虽然也能实现高强度、 低 屈强比的性能要求， 但是由于 C含量高， 碳当量大于 0.4, 仅能满足剪切对焊 的要求， 使得生产能够连续进行， 但难以获得优良的焊缝性能， 无法抵抗桩管 所承受的极大的冲击载荷。 中国专利 CN200310104863 提供的钢种也能达到 500MPa, 但是由于成分过于简单， 只能在 430-470°C的卷取温度下达到所需的 力学性能。 在这么低的卷取温度下， 热轧板的性能更难以实现稳定控制。 发明概述
本发明的目的在于提供一种 500MPa级低屈强比直缝焊钢管及其制造方法， 满足建筑用桩基所承受载荷的特点， 具有焊接性能优良、 高强韧性、 低屈强比 等特点， 其屈服强度大于 500MPa, 屈强比小于 0. 85。
为达到上述目的， 本发明的技术方案是：
本发明在材料设计上采用低碳含量， 保持适当的 Mn含量， 添加适量 、 Ti、 Nb等微合金元素， 通过其在控轧控冷过程中的作用来提高强度， 最终获得高强 韧性、 低屈强比的钢管。
具体的， 本发明的一种 500MPa级低屈强比直缝焊钢管用钢， 其成分重量百 分比如下：
C 0. 1广 0. 16% Si 0. 15 0. 35%
Mn 0· 8〜1· 5%
V 0. 06〜0. 15%
Al 0. 002〜0· 04%
Ti 0 〜0· 05%
Nb 0〜0· 05%
其余为 Fe和不可避免杂质； 且， 碳当量 Ceq不大于 0. 4%。
在本发明成分设计中：
设计成分碳当量 Ceq不大于 0. 4%, 不仅可以满足剪切对焊的要求， 而且还 可以获得优良的焊缝性能。
C: 随 C含量的增高， 焊接性能降低， 按重量百分比， C含量不宜大于 0. 16%, 但是 C含量太低将有损材料的强度， 宜采用含碳量 0. 11-0. 16%。
Si : 固溶于铁素体以提高钢的屈服强度， 其含量不宜过高， 应控制在 0. 15-0. 35%。
Mn: 主要溶于铁素体起强化作用， 用来提高铁素体的强度， 但含量太高时 偏析严重， 局部会产生马氏体， 按重量百分比， 宜采用 Mn含量为 0. 8-1. 5%。
V： 钒的碳氮化物在铁素体中析出， 具有稳定铁素体推迟贝氏体相变的作 用， 可以在控制冷却的过程中提高材料的强度， 同时提高焊缝的力学性能， 按 重量百分比， 宜采用含量 0. 06-0. 15%。
A1: 传统脱氧固氮元素， 形成 A1N, 可以细化奥氏体晶粒， 有利于提高材 料的韧性， 按重量百分比， 宜采用含量 0. 002-0. 04%。
Ti : 强碳氮化物形成元素， 形成 TiN、 TiC在均热和再加热过程中均可以细 化奥氏体晶粒， 提高焊缝的力学性能； 若含量太高， 易形成粗大的 TiN, 达不 到添加的目的。 按重量百分比， 宜采用含量 0-0. 05%。
Nb: 强碳氮化物形成元素， 热轧时可以推迟奥氏体再结晶而达到细化晶粒 在再加热过程中， 可以阻碍奥氏体晶粒长大， 提高材料强韧性， 按重量百分比， 宜采用含量 0-0. 05%。
根据上述合金设计方案， 钢水经转炉或电炉冶炼， 并浇铸制成板坯； 板坯 经 1200-130CTC加热后轧成板带， 板带的终轧温度在 840 ~ 940 °C之间； 轧后板 带经水帘层流冷却， 层流冷却采取后段冷却方式， 前段不开的冷却水阀门数量 占总冷却水阀门数量的 15%- 40% , 30 s内冷却到 50CT560 °C温度区间卷取成板卷 后堆垛緩冷； 焊接成型后， 经焊缝热处理， 加热温度为 950 ± 50 °C。
本发明的化学成分是微合金化的碳锰钢， 合金元素在 130(T840 °C的轧制温 度范围的充分固溶于奥氏体内， 后段冷却方式有利于奥氏体晶粒的长大， 水帘 快速冷却抑制了碳化物的析出以及奥氏体向铁素体珠光体相变的发生， 使得过 冷奥氏体在 50(T560 °C的卷取温度集中发生相变和析出碳化物， 从而获得了铁 素体 +弥散分布的细小的碳化物的微观组织， 保证了材料在获得高强度的同时， 还具有低屈强比的特征。
本发明的有益效果：
本发明合金成分碳当量低， 而且合金含量低， 不含 Mo、 Ni等吊贵的合金元 素， 仅经焊缝热处理， 钢管生产成本不高， 具有重大的经济和社会效益。 发明的详细说明
下面结合实施例对本发明做进一步说明。
本发明实施例成分参见表 1 , 其中 Fe为余量。 本发明实施例制造方法及性 能参见表 2。
表 1 单位： wt.%
Figure imgf000005_0001
表 2 前段不 开的冷 终轧 水帘冷 卷取 0°C全尺 水阀 t 0.5 tm 屈强
却时间 寸冲击 门数量
MPa MPa 比
。c s 。c 功 /J 占总冷 水阀 门数量 实施例 1 940 28 550 510 655 0.78 1 15 15% 实施例 2 900 15 560 545 660 0.83 120 24% 实施例 3 880 23 510 535 680 0.79 105 29% 实施例 4 850 12 540 540 645 0.84 1 10 37% 实施例 5 840 15 500 550 670 0.82 130 40% 对比例 1 870 22 500 430 500 0.86 120
对比例 2 900 25 550 580 710 0.82 40
如表 2所示， 采用本发明的化学成分设计以及生产工艺制度， 材料的屈服 强度大于 500MPa, 屈强比小于 0.85 , 0 °C全尺寸冲击功大于 100J, 力学性能稳 定。
经剪切对焊、板卷成型、 ERW制管后，经焊缝热处理等工艺步骤生产 ERW 高强度钢管， 实施例 1 -5的强度均可满足屈服强度大于 500MPa的要求。 比较 例 1的成分简单， 不含 V元素， 在本发明的卷取温度下远达不到屈服强度大于 500MPa的要求； 比较例 2的 C含量较高， 材料的冲击韧性显著下降， 不能满 足建筑桩基用钢对冲击载荷的苛刻要求。 可见， 采用本发明所设计的化学成分 和工艺制度，可以稳定生产出满足屈服强度大于 500 MPa的高性能要求的 ERW 钢管。

Claims

权 利 要 求 书
1. 一种 500MPa级低屈强比直缝焊钢管， 其成分重量百分比如下： C 0·11〜0·16%
Si 0·15〜0·35%
Μη 0·8〜1·5%
V 0.06-0.15%
Α1 0.002-0.04%
Ti 0〜0·05%
Nb 0-0.05%
其余为 Fe和不可避免杂质； 且， 碳当量 Ceq < 0.4;
并通过下述方法获得： 钢水经转炉或电炉冶炼， 并浇铸制成板坯； 板坯经 1200〜1300°C加热后轧成板带， 板带的终轧温度在 840~940°C之间； 轧后板带 经水帘层流冷却， 层流冷却采取后段冷却方式， 前段不开的冷却水阀门数量占 总冷却水阀门数量的 15%— 40%, 30秒内冷却到 500〜560°C温度区间卷取成板 卷； 焊接成型后， 经焊缝热处理， 加热温度为 950 ±50°C; 钢管屈服强度大于 500MPa, 屈强比小于 0.85。
2. 一种 500MPa级低屈强比直缝焊钢管的制造方法，钢水经转炉或电炉冶 炼， 并浇铸制成板坯， 其成分重量百分比如下： C0.11〜0.16%、 Si 0.15-0.35%, Μη0·8〜1·5%、 V 0.06-0.15%, Α10·002〜0·04%、 Ti0〜0.05%、 Nb 0-0.05%, 其 余为 Fe和不可避免杂质； 且， 碳当量 Ceq不大于 0.4; 板坯经 1200〜1300°C加 热后轧成板带，板带的终轧温度在 840 ~ 940°C之间；轧后板带经水帘层流冷却， 层流冷却采取后段冷却方式， 前段不开的冷却水阀门数量占总冷却水阀门数量 的 15%— 40%, 30秒内冷却到 500〜560°C温度区间卷取成板卷； 焊接成型后， 经焊缝热处理， 加热温度为 950 ±50°C; 获得钢管的屈服强度大于 500MPa, 屈 强比小于 0.85。
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CN113770174A (zh) * 2021-08-13 2021-12-10 邯郸钢铁集团有限责任公司 一种高强韧性工程机械用钢板形控制方法
CN113770174B (zh) * 2021-08-13 2023-09-05 邯郸钢铁集团有限责任公司 一种高强韧性工程机械用钢板形控制方法

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