WO2014048337A1 - 一种高频直缝焊管及其制造方法 - Google Patents

一种高频直缝焊管及其制造方法 Download PDF

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Publication number
WO2014048337A1
WO2014048337A1 PCT/CN2013/084267 CN2013084267W WO2014048337A1 WO 2014048337 A1 WO2014048337 A1 WO 2014048337A1 CN 2013084267 W CN2013084267 W CN 2013084267W WO 2014048337 A1 WO2014048337 A1 WO 2014048337A1
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Prior art keywords
welded pipe
frequency straight
straight seam
weld
manufacturing
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English (en)
French (fr)
Inventor
王怡然
沈建兰
崔俊
谷中莹
吴文辉
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to AU2013324845A priority Critical patent/AU2013324845B2/en
Priority to CA2885696A priority patent/CA2885696C/en
Publication of WO2014048337A1 publication Critical patent/WO2014048337A1/zh
Priority to SA515360196A priority patent/SA515360196B1/ar
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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
    • C22C38/18—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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • 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
    • C22C38/02—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
    • C22C38/18—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to a steel pipe and a method of manufacturing the same, and more particularly to a high frequency welded pipe and a method of manufacturing the same. Background technique
  • high-frequency straight seam welded pipe is widely used due to its low manufacturing cost, high dimensional accuracy and easy control of the length of the fixed length. It is mainly used for oil and gas on land and seabed. The transportation of pulp has a broad application prospect.
  • the object of the present invention is to provide a high-frequency straight seam welded pipe which has good anti-HIC performance and can achieve L360MCS steel grade performance, has high yield strength, tensile strength and impact. Toughness and weldability.
  • the present invention provides a high frequency straight seam welded pipe having a chemical element mass percentage of:
  • the balance is Fe and other unavoidable impurities.
  • C is the main solid solution strengthening element of pipeline steel.
  • HIC hydrogen induced cracking
  • Ca treatment has an important influence on the resistance to hydrogen induced cracking (HIC) of the strip.
  • HIC hydrogen induced cracking
  • the content control of Ca has a correlation with the S content. Therefore, the technical solution of the present invention controls the content of Ca to 0.001 0.003 wt%.
  • Cu Of the many alloying elements, only copper is advantageous against hydrogen induced cracking (HIC) properties. Adding a certain amount of copper to the pipeline steel, the hydrogen induced crack sensitivity is significantly reduced, mainly copper promotes blunt The formation of the film reduces the intrusion of hydrogen and hinders the formation of hydrogen induced cracks. In the technical solution of the present invention, the resistance to hydrogen induced cracking (HIC) is improved by adding a certain amount of copper. Therefore, the Cu content is controlled to be 0.125 to 0.135 wt%.
  • Mn The effect of Mn on the hydrogen induced cracking resistance of pipeline steel is mainly reflected in the influence of Mn on the phase transformation process of strip steel.
  • the Mn content exceeds 1.0 wt%, the sensitivity of hydrogen induced cracking (HIC) increases. Therefore, in the technical solution of the present invention, the Mn content is set to 0.75 to 0.95 wt%.
  • the present invention also provides a method for manufacturing the above-mentioned high-frequency straight seam welded pipe, comprising the following steps: in the waste pipe forming step, controlling the amount of extrusion to be 2 to 3% of the outer diameter of the welded pipe;
  • the welding speed is controlled to be 18 ⁇ 20m/min ;
  • the weld After the post-weld heat treatment, the weld is subjected to normalizing heat treatment at a temperature of 930 to 970 ° C. After normalizing, the weld is air-cooled to below 380 ° C, and then water-cooled to lower the temperature of the weld to below 80 ° C.
  • the opening angle is controlled to be 3 to 4.2°.
  • the amount of extrusion before and after welding is controlled to be 2 to 3% of the outer diameter of the welded pipe, and the amount of extrusion refers to the difference between the circumference of the waste pipe before extrusion and the circumference after extrusion.
  • the molten pool at the weld is exposed to the air, and the oxidation reaction is prone to occur.
  • the oxidation reaction product is closely related to the chemical composition of the strip. Therefore, it is necessary to use a large amount of extrusion to extrude the produced high melting point product onto the surface of the strip weld and remove it by deburring.
  • the amount of extrusion below 2% is prone to defects such as cold welding, which makes it impossible to remove the inclusions in the strip from the surface of the weld, thereby affecting the strip to set the welding speed to 18 to 20 m/min.
  • the reason is that the welding speed is usually inversely proportional to the welding power, and the faster welding speed easily offsets the high welding power and the large amount of extrusion, which is easy to discharge the inclusions, resulting in a decrease in the discharge inclusion effect. Therefore, for the present technical solution, the inventors controlled the welding speed to 18 to 20 m/min.
  • the manufacturing method of the high-frequency straight seam welded pipe according to the present invention is based on the high-frequency straight seam induction welding (HFW) manufacturing method, and the high-frequency welding forming and welding parameters are set by appropriately adjusting the extrusion amount and the molding process. Control the subsequent heat treatment technical parameters to produce high-frequency straight seam welded pipes that meet HIC resistance, tensile properties, impact toughness and microstructure requirements.
  • HAW high-frequency straight seam induction welding
  • the high-frequency straight seam welded pipe of the invention has good anti-HIC performance, and achieves L360MCS steel grade performance, has high yield strength, tensile strength, impact toughness. Sex and welding performance, suitable as a conveying pipe for harsh working environments with high H or S content or acid corrosion. detailed description
  • the high frequency straight seam welded pipe of the present invention is manufactured according to the following steps:
  • the head and the tail of the coil are cut off to form a flush cut 3° in the transverse direction of the coil, and the tail of the previous coil and the head of the next coil are rolled by carbon dioxide gas shielded welding.
  • Welded together; high-frequency straight seam welded pipe is produced by steel strip, and the edge width of the strip and the perpendicularity of the edge of the board are precisely controlled by the edge milling method; the strip forming method is used to form the strip into a waste pipe, and the pressing amount is controlled as a welded pipe.
  • control opening angle is 3 ⁇ 4.2°; when welding, the welding speed is controlled to 18 ⁇ 20m/min; after welding, the weld is subjected to normalizing heat treatment, and the normalizing heat treatment temperature is 930 ⁇ 970° C. After normalizing, the weld is air cooled to below 380 °C, then water cooled to reduce the temperature of the weld to below 80 °C.
  • the high-frequency straight seam welded pipe obtained by the above process has a wall thickness of 6.4 mm to 9.5 mm and a pipe diameter of 219.7 mm to 406.4 mm.
  • Table 1 shows the chemical distribution ratios of the high-frequency straight seam welded pipes in Examples 1-6.
  • Table 2 shows the detailed process parameters for manufacturing high frequency straight seam welded pipes in Examples 1-6. Table 2
  • Table 3 shows the performance parameters of each of the high frequency straight seam welded pipes in Examples 1-6.
  • the high-frequency straight seam welded pipe of the present invention has good mechanical properties and has anti-HIC performance, as follows: welded pipe body yield strength 399Mpa, tensile strength 505 ⁇ &, elongation 24%, welded pipe The tensile strength of the weld is 475Mpa, which indicates that the high-frequency straight seam welded pipe meets the high strength requirements and has high tensile strength.
  • the impact toughness of the welded pipe body is the minimum value of the Charpy impact work.

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

Abstract

本发明公开了一种高频直缝焊管，其化学元素质量百分含量为：C： 0.042～0.056%；Si：0.18～0.22%；Mn：0.75～0.95%；P：0.0064～0.015%； S：0.0006～0.002%；Ti：0.012～0.018%；V：0.001～0.002%；Al：0.026～ 0.038%；Ni：0.080～0.13%；Nb：0.020～0.029%；Cu：0.125～0.135%；Cr： 0.018～0.03%；Mo：0.004～0.008%；B：0～0.0005%；Ca：0.001～0.003%；余量为 Fe和其他不可避免的杂质。同时，本发明还公开了一种高频直缝焊管的制造方法。

Description

一种高频直缝焊管及其制造方法
技术领域
本发明涉及一种钢管及其制造方法， 尤其涉及一种高频焊管及其制造方 法。 背景技术
在石油天然气生产和输送领域中， 高频直缝焊管（HFW) 以其制造成本 低、 尺寸精度高、 定尺长度容易控制等优势获得广泛应用， 主要用于陆上、 海底的石油、 天然气、 矿浆的输送， 应用前景广阔。
随着全球对于石油及天然气需求的不断增长， 石油井和天然气井的开采 条件日趋恶化、 复杂。 由于一些 11、 S含量高， 具有严重腐蚀环境的油气田 的相继开发， 因此迫切需要钢管制造业开发与生产适应在这类酸性工作条件 下的石油、 天然气输送用管。 目前， 我国有上百套高频直缝焊管 （HFW)机 组，但大多数厂家只能依靠大型钢厂提供板卷原料，主要生产常规钢级钢管。 对于市场需求急迫的抗 HIC (hydrogen induced crack, 氢致裂纹） 性能优异 的较高钢级的管线管， 国内尚无相应的生产厂家。 对于抗 HIC 性能的 L360MCS钢级高频直缝焊管及其制造工艺， 目前国内尚存在空白。 发明内容
本发明的目的在于提供一种高频直缝焊管及其制造方法， 该高频直缝焊 管具备良好的抗 HIC性能， 并可达到 L360MCS钢级性能， 具有较高屈服强 度， 抗拉强度， 冲击韧性和焊接性能。
为达到上述发明目的， 本发明提供了一种高频直缝焊管， 其化学元素质 量百分含量为：
C: 0·042〜0·056%;
Si: 0· 18〜0·22%;
Μη: 0·75〜0·95%;
Ρ: 0·0064〜0·015%; S: 0·0006 0·002%;
Ti: 0·012 0·018%;
V 0.001 0·002%;
Al: 0·026 0·038%;
Ni: 0·080 0·13%;
Nb: 0·020 0·029%;
Cu: 0.125 0.135%;
Cr: 0·018 0·03%;
Mo: 0.004—0.008%
B: 0 05%;
Ca: 0.001 0·003%;
余量为 Fe和其他不可避免的杂质。
本发明所述的高频直缝焊管中主要化学元素的成分设计原理如下： C: C 是管线钢的主要固溶强化元素。 经研究人员通过大量实验表明， 随着带钢中 C含量增加， 带钢的氢致裂纹 （HIC) 的敏感性随之增加， 所以 适当控制 C的含量在可接受的不影响带钢强度的下限范围是必要的。本成分 适当降低了 C的含量， 从通常的 0.07wt%左右降低为 0.056wt%以下。 因而， 本发明的技术方案中将 C控制为 0.042 0.056wt%
S: 在低硫钢中， 裂纹长度率降低且在破裂断口上呈现 MnS， 这说明在 带钢中降低 N S可以有效地控制裂纹生成。 但是如果将 S的含量降低到很 低也不能避免带钢裂纹的发生， 所以一味追求降低 S含量的也是不必要的。 发明人通过大量实验发现， 将 S的质量百分含量控制在 0.0006 0.002%既可 以满足耐蚀要求又可以防止带钢裂纹产生。
Ca: Ca处理对带钢抗氢致裂纹（HIC)性能有重要影响。本技术方案中， 在成分中添加适当的 Ca， 在最终凝固位置析出的 CaS， 经轧制后使之变化成 球状夹杂物， 提高了带钢的抗氢致裂纹 （HIC) 性能。 但 Ca的含量控制与 S 含量具有相关关系。 故本发明的技术方案将 Ca 的含量控制在 0.001 0.003wt%
Cu: 在众多的合金元素中， 仅有铜对抗氢致裂纹（HIC)性能是有利的。 在管线钢中加入一定量的铜， 氢致裂纹敏感性明显减小， 主要是铜促进了钝 化膜的形成， 减少了氢元素的侵入， 阻碍了氢致裂纹的形成。 本发明的技术 方案中通过加入一定量的铜， 提高了抗氢致裂纹 （HIC ) 的性能。 因此， 将 Cu含量控制在 0.125〜0.135wt%。
Mn: Mn对管线钢氢致裂纹敏感性的作用主要表现在 Mn对带钢相变过程 的影响。 当 Mn含量超过 1.0wt%时， 氢致裂纹 （HIC) 的敏感性增加。 所以， 在本发明的技术方案中将 Mn含量设定为 0.75〜0.95wt%。
相应地，本发明还提供了上述高频直缝焊管的制造方法，包括以下歩骤： 在荒管成型歩骤， 控制挤压量， 使其为焊管外径的 2〜3%；
在焊接歩骤， 控制焊接速度为 18〜20m/min;
在焊后热处理歩骤， 对焊缝进行正火热处理， 温度为 930〜970°C， 正火 后使焊缝空冷至 380°C以下， 然后水冷使焊缝的温度降至 80°C以下。
进一歩地， 在本发明的高频直缝焊管的制造方法的荒管成型歩骤中， 控 制开口角为 3〜4.2° 。
在本发明的技术方案中， 焊接前后的挤压量控制为焊管外径的 2〜3%， 该挤压量是指挤压前的荒管周长和挤压后的周长之差。 在熔化状态时， 焊缝 处的熔池裸露在空气中， 容易发生氧化反应， 氧化反应产物与带钢化学成分 密切相关。 因此， 需要采用较大的挤压量， 将生产的高熔点产物挤压到带钢 焊缝表面并通过去毛刺手段去除。 然而， 低于 2%的挤压量容易产生冷焊等 缺陷， 导致无法将带钢中的夹杂物排出焊缝表面进行去除， 从而影响带钢质 将焊接速度设定为 18〜20m/min， 原因在于通常焊接速度与焊接功率呈 反比， 较快的焊接速度容易抵消较高的焊接功率和较大的挤压量带来的夹杂 物易排出性， 导致排出夹杂效果下降。 所以对于本技术方案， 发明人将该焊 接速度控制在 18〜20m/min。
本发明所述的高频直缝焊管的制造方法在采用高频直缝感应焊 （HFW) 制造方法的基础上， 通过合理调整挤压量及成型过程， 设定高频焊接成型及 焊接参数并控制后续的热处理技术参数， 从而生产出满足抗 HIC性能、 拉伸 性能、 冲击韧性和微观组织要求的高频直缝焊管。
与现有技术相比， 本发明所述的高频直缝焊管， 具有良好抗 HIC性能， 并且达到了 L360MCS钢级性能， 具有较高的屈服强度， 抗拉强度， 冲击韧 性和焊接性能， 适合作为输送用管道应用于 H、 S含量较高或带有酸性腐蚀 的恶劣工作环境。 具体实施方式
实施例 1-6
按照下述歩骤制造本发明所述的高频直缝焊管：
将开卷后钢卷的头部和尾部切除， 形成平齐的与钢卷横向方向呈 3 ° 的 切口， 采用二氧化碳气体保护焊将前一卷钢卷的卷尾和后一卷钢卷的卷头焊 接在一起； 用钢带生产高频直缝焊管， 板边采用铣边方法精确控制带钢宽度 和板边垂直度； 采用排辊成型方法将带钢成型为荒管， 控制挤压量为焊管外 径的 2〜3%；控制开口角为 3〜4.2° ；焊接时，控制焊接速度为 18〜20m/min; 焊后对焊缝进行正火热处理， 正火热处理的温度为 930〜970°C， 正火后使焊 缝空冷至 380°C以下， 然后水冷使焊缝的温度降至 80°C以下。 经上述工艺歩 骤获得的高频直缝焊管的壁厚为 6.4mm〜9.5mm， 管径为 219.7mm〜 406.4mm。
表 1显示了实施例 1-6中各高频直缝焊管的化学成分配比。
表 1 (余量为 Fe和其他不可避免的杂质， wt%)
Figure imgf000005_0001
表 2显示了实施例 1-6中制造高频直缝焊管的详细工艺参数。 表 2
Figure imgf000006_0001
表 3显示了实施例 1-6中各高频直缝焊管的各项性能参数。
表 3
Figure imgf000006_0002
由表 3可知， 本发明所述的高频直缝焊管具有良好的力学性能并且具备 抗 HIC性能， 具体如下： 焊管管体屈服强度 399Mpa， 抗拉强度 505^^&， 延伸率 24%， 焊管焊缝的抗拉强度 475Mpa， 表明所述高频直缝焊管整体 均满足较高的强度要求且具有较高的拉伸能力； 焊管管体的冲击韧性夏比 (charpy)冲击功单值最小值 119J， 均值 127J， 焊管焊缝的冲击韧性夏比 (charpy)冲击功单值最小值 139J， 均值 145J， 表明所述高频直缝焊管具有 较好的韧性性能及焊接性能； 作为评价带钢材料抗氢致裂纹 （HIC ) 性能优 劣指标的 3 个参数： 裂纹敏感率 (CSR：)、 裂纹长度率 (CLR)及裂纹厚度率 (CTR), 在表 3中所显示均为 0%， 表明所述高频直缝焊管具备良好的抗氢致 裂纹 （HIC) 性能。 要注意的是， 以上所举的仅为本发明的具体实施方式， 显然本发明不 限于以上实施方式， 随之有着许多的类似变化。 本领域的技术人员如果从 本发明公开的内容直接导出或联想到的所有变形， 均应属于本发明的保护 范围。

Claims

权利要求书
1. 一种高频直缝焊管， 其特征在于， 其化学元素质量百分含量为：
C: 0·042 0·056%;
Si: 0·18 0·22%;
Μη: 0·75 0·95%;
Ρ: 0·0064 0·015%;
S: 0·0006 0·002%;
Ti: 0·012 0·018%;
V 0.001 0·002%;
Α1: 0·026 0·038%;
Ni: 0·080 0·13%;
Nb: 0·020 0·029%;
Cu: 0.125 0.135%;
Cr: 0·018 0·03%;
Μο: 0.004—0.008%
Β: 0 05%;
Ca: 0.001 0·003%;
余量为 Fe和其他不可避免的杂质。
2. 如权利要求 1所述的高频直缝焊管的制造方法， 其特征在于：
在荒管成型歩骤， 控制挤压量， 使其为焊管外径的 2 3%
在焊接歩骤， 控制焊接速度为 18 20m/min;
在焊后热处理歩骤， 对焊缝进行正火热处理， 温度为 930 970°C 正火后使焊缝空冷至 380°C以下， 然后水冷使焊缝的温度降至 80°C以下。
3. 如权利要求 2所述的高频直缝焊管的制造方法，其特征在于，在荒管成型 歩骤， 控制开口角为 3 4.2°
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