WO2014029328A1 - 一种超高韧性高强度钻杆及其制造方法 - Google Patents

一种超高韧性高强度钻杆及其制造方法 Download PDF

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Publication number
WO2014029328A1
WO2014029328A1 PCT/CN2013/081922 CN2013081922W WO2014029328A1 WO 2014029328 A1 WO2014029328 A1 WO 2014029328A1 CN 2013081922 W CN2013081922 W CN 2013081922W WO 2014029328 A1 WO2014029328 A1 WO 2014029328A1
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drill pipe
pipe
drill rod
water spray
high strength
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English (en)
French (fr)
Inventor
赵鹏
于杰
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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 US14/422,864 priority Critical patent/US10227828B2/en
Priority to CA2881904A priority patent/CA2881904C/en
Publication of WO2014029328A1 publication Critical patent/WO2014029328A1/zh
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Classifications

    • E—FIXED CONSTRUCTIONS
    • E21—EARTH OR ROCK DRILLING; MINING
    • E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
    • E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • 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 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
    • C21D9/08—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
    • 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
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum

Definitions

  • the present invention relates to a metal article and a method of manufacturing the same, and more particularly to a drill pipe and a method of manufacturing the same. Background technique
  • Drill pipes for oil and gas drilling are manufactured in accordance with the standards of the American Petroleum Institute (API).
  • API SPEC 5DP the drill pipe has only four steel grades: E, X, G, and S, which correspond to four strengths of 75ksi, 95ksi, 105ksi, and 135ksi.
  • E, X, G, and S which correspond to four strengths of 75ksi, 95ksi, 105ksi, and 135ksi.
  • the American Petroleum Institute's "Drill Pipe Specification” specifies the longitudinal full-scale impact toughness of the drill pipe at room temperature of 54J.
  • the publication number is CN1690241A, and the publication date is November 2, 2005.
  • the Chinese patent document entitled "High-strength oil drill pipe and its manufacturing method” discloses a high-strength drill pipe whose chemical composition percentage percentage is: C: 0.20-0.30%; Si: 0.1-0.5%; Mn: 0.7-1.5%; Cr: 0.7-1.5%; Mo: 0.1-0.4%; V: 0.01-0.15%; the balance being Fe and inevitable impurities.
  • This patent produces an S-grade drill pipe that meets the American Petroleum Institute's API Specification (API SPEC 5DP), and its impact toughness meets the requirements for room temperature longitudinal full-scale impact toughness 54J. Summary of the invention
  • the object of the present invention is to provide a high-strength drill pipe and a manufacturing method thereof, the high-strength drill pipe being full
  • the S-class ultra-high toughness requirements of the American Petroleum Institute's "Drill Pipe Specifications” (API SPEC 5DP) -20 ° C longitudinal full-scale impact toughness 100] which can be used in deep wells, ultra-deep wells, horizontal wells, large displacement wells Work under wells with harsh working conditions.
  • the present invention provides an ultra high toughness and high strength drill pipe having a chemical element mass percentage of: C: 0.24 - 0.30%, Si: 0.1 to 0.5%, Mn: 0.7 - 1.5 %,
  • the chemical composition design principle of the ultra high toughness high strength drill pipe according to the present invention is as follows:
  • C is a carbide forming element, which can increase the strength of steel.
  • the control range of the C content of the present invention is 0.24% to 0.30%, preferably 0.25% to 0.29%, more preferably 0.26% to 0.28%.
  • Si is an element that must be added to improve casting properties. However, if the content is too high, the brittleness of the steel is increased. Therefore, in the present invention, the Si content is controlled to be 0.1 to 0.5%, preferably 0.24 to 0.38%, more preferably
  • Mn is an austenite forming element.
  • Mn is an austenite forming element.
  • the transformation of austenite to ferrite and bainite during high-temperature cooling is delayed, thereby obtaining more quenched martensite and improving quenching of steel.
  • Permeability If the Mn content is less than 0.7%, the effect of improving the hardenability is not obvious; if the Mn content is more than 1.5%, the austenite is too stable, and the amount of retained austenite after quenching is increased. Therefore, the content of Mn of the present invention is 0.7 to 1.5%, preferably 0.7 to 1.17%, more preferably 0.92 to 1.17%.
  • Cr is a carbide forming element, which can improve the strength and hardenability of steel. When the content is too low, the effect is not obvious; when the content is too high, the hardness of the steel is greatly increased. Therefore, the Cr content in the present invention ranges from 0.7 to 1.5%, preferably from 0.95 to 1.22%.
  • the carbide particles formed by Mo are fine, do not cause stress concentration of the microstructure, and are advantageous for improving impact toughness.
  • the strip steel mainly improves the strength and tempering stability of the steel by carbide precipitation strengthening and solid solution strengthening, while the higher Mo content forms a part of excess Mo in the matrix while forming the carbide of Mo.
  • the tempering stability of steel is improved.
  • the improvement of tempering stability is beneficial to increase the tempering temperature, thereby reducing the residual stress after heat treatment and improving the impact toughness.
  • Mo is a precious metal, the content is too high, which greatly increases the production cost.
  • the Mo content is set to 0.5 to 0.75%, preferably 0.6 to 0.75%, more preferably 0.61 to 0.72%, and most preferably 0.66 to 0.70%.
  • V can form carbides, which can refine grains and improve the strength and toughness of steel. However, when the content reaches a certain amount, the effect is not obvious, and since vanadium is a precious metal, its price is high, which leads to an increase in production cost. Therefore, in the present invention, the V content is controlled to 0.01 to 0.10%, preferably 0.05 to 0.09%, more preferably 0.05 to 0.08%.
  • Nb refines grains, forms carbides, and increases the strength and toughness of steel. However, when the amount reaches a certain amount, the effect which can be exhibited is not remarkable, and since the price is high, the content is controlled in the present invention to be 0.01 to 0.05%, preferably 0.02 to 0.04%.
  • Phosphorus is an impurity element, and the lower the better, in the present invention, when the phosphorus element exceeds 0.015%, microsegregation is increased, which affects the impact toughness of the steel. Therefore, the phosphorus content should be controlled to 0.015% in the present invention.
  • S Sulfur is also an impurity element, the lower the better.
  • the sulfur content exceeds 0.005%, the sulfide content is increased to affect the impact toughness of the steel, so the sulfur content should be controlled to 0.005% in the present invention.
  • the inventor adds a higher content of Mo, and adds Nb and V elements. These metal elements improve the strength of the drill pipe while refining the crystal grains, and the drill pipe can be made later.
  • a high tempering temperature reaches an intensity level of 135 ksi.
  • the present invention also provides a method of manufacturing the above-described high-strength drill pipe, comprising: manufacturing a drill pipe having a mass percentage composition of the above elements, and then performing a quenching and tempering operation.
  • the quenching process after the whole of the drill pipe is heated to 900 ⁇ 950 °C, the axial flow water spray cooling on the inner surface of the drill pipe and the laminar water spray cooling on the outer surface of the drill pipe are simultaneously controlled, and the water spray of the thickened pipe end of the drill pipe is controlled at the same time.
  • the amount of water sprayed from the pipe body is different so that the pipe body of different wall thickness and the thickened pipe end have substantially the same cooling rate; in the tempering process, the tempering temperature is controlled to be 650 to 675 °C.
  • the entire drill pipe in the quenching step, is heated to 910 to 940 ° C, preferably to 920 to 940 ° C, more preferably to 910 to 930 ° C.
  • the tempering temperature in the tempering step, is controlled to be 650 to 670 ° C, or 660 to 670 ° C.
  • the axial flow water spray cooling on the inner surface of the drill pipe and the laminar water spray cooling on the outer surface of the drill pipe are simultaneously controlled, and the water spray amount of the thickened pipe end of the drill pipe and the pipe body are controlled at the same time.
  • the amount of water sprayed is different so that the tubes of different wall thicknesses and the thickened tube ends have substantially the same cooling rate.
  • “basic” It means that the difference between the cooling speeds of the pipe body of different wall thickness and the thickened pipe end is less than or equal to 10%, preferably less than or equal to 5%.
  • the inventor firstly thickens the pipe end of the drill pipe to form a pipe body of the thickened drill pipe; after being heated to 900 ⁇ 950 ° C as a whole, it is placed on a rotary quenching gantry, While the steel pipe rotates, the axial flow water spray cooling on the inner surface of the drill pipe and the laminar water spray cooling on the outer surface of the drill pipe are performed, and the different water spray amounts of the pipe end and the pipe body are controlled by the drill pipe to make pipes of different wall thicknesses.
  • the body and the thickened pipe end have substantially the same cooling speed to ensure that the drill pipe body and the thickened pipe end have the same quenching structure; finally, the tempering treatment at 650 ⁇ 675 °C makes the pipe body and the thickened pipe end reach 135 ksi Mechanical properties.
  • the ultra high toughness high strength drill pipe and the manufacturing method thereof have the following beneficial effects:
  • the -20 °C longitudinal full-scale impact toughness is 100 J and the impact toughness is much higher than the S-grade drill pipe level in the American Petroleum Institute's API Specification (API SPEC 5DP). Drilling requirements for difficult wells such as deep wells, ultra-deep wells, horizontal wells, and large displacement wells. detailed description
  • Table 1 lists the chemical element ratios of Examples 1-6 of the present invention and the currently used CrMnMo steel (Comparative Example).
  • the ultra high toughness high strength drill pipe of the present invention is produced by the following steps (see Table 2 for detailed process parameters and mechanical properties of Examples 1-6):
  • the drill pipe end is thickened to make a thickened drill pipe body; the whole drill pipe is heated to 900 ° C ⁇ 950 ° C; the drill pipe is placed on a rotating quenching rig as a whole, and the steel pipe is rotated At the same time, the axial flow spray cooling on the inner surface of the drill pipe and the laminar water spray cooling on the outer surface are simultaneously controlled, and the water spray amount of the thickened pipe end of the drill pipe is controlled differently from the water spray volume of the pipe body to make the pipe body with different wall thicknesses and The thickened pipe ends have the same cooling speed, ensuring that the pipe body and the thickened end have the same quenching structure; finally, after tempering at 650 ⁇ 675 °C, the drill pipe body and the drill pipe thickened pipe end reach the required 135ksi mechanical properties.
  • the tempering temperature of the ultra high toughness high strength drill pipe described in the technical solution is much higher than the tempering temperature of the ordinary 135 ksi drill pipe of the comparative example, thereby making the invention
  • the -20°C longitudinal full-scale impact toughness of the ultra-high toughness and high-strength drill pipe is 100J, which is much higher than the impact toughness level of the ordinary 135ksi drill pipe, and can be carried out for a long time under the severe conditions of frequent alternating stress and frictional collision. Work.

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Abstract

一种超高韧性高强度钻杆，其质量百分比含量为：C：0.24-0.30%，Si：0.1-0.5%，Mn：0.7-1.5%，Cr：0.7-1.5%，Mo：0.5-0.75%，V：0.01-0.10%，Nb：0.01-0.05%，P≤0.015%，S≤0.005%，其余为Fe和不可避免的杂质。该钻杆的制备方法为：将上述组分的钻杆整体加热至900-950℃后，进行钻杆内表面轴流喷水冷却和外表面层流喷水冷却，同时控制钻杆加厚管端与管体的喷水量不同，之后在650-675℃进行回火，从而得到强度为135ksi，-20℃纵向全尺寸冲击韧性≥100J的超高韧性高强度钻杆。

Description

一种超高韧性高强度钻杆及其制造方法
技术领域
本发明涉及一种金属制品及其制造方法， 尤其涉及一种钻杆及其制造方 法。 背景技术
用于石油天然气钻探的钻杆是按照美国石油协会 （API , American Petroleum Institute)标准生产制造的。根据美国石油协会的《钻杆规范》（API SPEC 5DP)，钻杆仅有 E、 X、 G、 S四种钢级，分别对应 75ksi、 95ksi、 105ksi、 135ksi四种强度。为保证钻杆的冲击性能，美国石油协会的《钻杆规范》 (API SPEC 5DP) 规定了钻杆室温纵向全尺寸冲击韧性 54J。
随着石油工业的发展， 钻杆的工作条件日趋恶劣， API标准钻杆已不能 满足日益苛刻的钻井作业要求。 近年来， 随着深井、 超深井的不断开发， 对 钻杆的性能提出了更高要求。 这不仅要求钻杆材料有较高的强度水平， 而且 要有充足的韧性储备。 只有这样才能抵御过载操作中的强拉、 强扭、 冲击振 动以及各种交变载荷作用， 并能适应各种特殊工作条件对钻杆的使用要求。 因此， 美国石油协会的 《钻杆规范》 （API SPEC 5DP) 中 S级钻杆规定的室 温纵向全尺寸冲击韧性 54〗 的标准已无法满足日益苛刻的钻井作业要求。 为此， 美国石油协会的标准提出了 PSL3级钻杆的性能要求： S级钻杆 -20°C 纵向全尺寸冲击韧性 100J， 即超高韧性高强度钻杆的性能要求。
公开号为 CN1690241A, 公开日为 2005年 11月 2日， 名称为 "高强度 石油钻杆及其制造方法" 的中国专利文献公开了一种高强度钻杆， 其化学成 分质量百分比配比为： C: 0.20-0.30%； Si: 0.1-0.5%； Mn: 0.7-1.5%； Cr: 0.7-1.5%； Mo: 0.1-0.4%； V： 0.01-0.15%； 其余为 Fe和不可避免杂质。 采 用该专利可生产出符合美国石油协会的 《钻杆规范》 （API SPEC 5DP) 的 S 级钻杆， 其冲击韧性满足室温纵向全尺寸冲击韧性 54J的要求。 发明内容
本发明的目的在于提供一种高强度钻杆及其制造方法， 该高强度钻杆满 足美国石油协会的 《钻杆规范》 （API SPEC 5DP) 中 -20°C纵向全尺寸冲击韧 性 100】的 S级超高韧性的要求， 从而可以在深井、 超深井、 水平井、 大位 移井等具有苛刻工作条件的钻井下进行工作。
为了实现本发明的目的， 本发明提供了一种超高韧性高强度钻杆， 其各 化学元素质量百分含量为： C: 0.24—0.30%, Si: 0.1〜0.5%， Mn: 0.7—1.5%,
Cr: 0·7〜1·5%， Mo: 0.5—0.75%, V： 0·01〜0· 10%， Nb: 0·01〜0·05%， P 0.015%， S^O.005%, 其余为 Fe和不可避免的杂质。
在本发明中， 除非另外说明， 所有的百分数都是质量百分数。
本发明所述的超高韧性高强度钻杆的化学成分设计原理如下：
C: C为碳化物形成元素， 可以提高钢的强度。 当 C含量太低时， 效果 不明显； c含量太高时， 会大大降低钢的韧性， 并有可能产生淬火裂纹。 因 此， 本发明 C含量的控制范围为 0.24%〜0.30%， 优选 0.25%〜0.29%， 更优 选 0·26%〜0·28 %。
Si: Si是提高浇铸性能必须加入的元素。但是含量过高会增加钢的脆性， 故在本发明将中将 Si含量控制在 0.1〜0.5%， 优选 0.24〜0.38 %， 更优选
0·27〜0·36%。
Mn: Mn为奥氏体形成元素， 通过稳定奥氏体组织， 推迟高温冷却过程 中奥氏体向铁素体和贝氏体的转变， 从而得到更多的淬火马氏体， 提高钢的 淬透性。 若 Mn含量小于 0.7%时， 提高淬透性的作用不明显； 若 Mn含量大 于 1.5%时， 则奥氏体过于稳定， 会增加淬火后的残余奥氏体量。 因此， 本发 明的 Mn的含量为 0.7〜1.5%， 优选 0.7〜1.17 %， 更优选 0.92〜 1.17 %。
Cr: Cr为碳化物形成元素，可以提高钢的强度和淬透性。其含量太低时， 效果不明显； 含量太高时， 则会大大提高钢的硬度。所以， 本发明中 Cr含量 范围为 0.7〜1.5%， 优选 0.95〜1.22 %。
Mo: Mo形成的碳化物颗粒细小， 不会造成微观组织结构的应力集中， 有利于提高冲击韧性。 带钢主要是通过碳化物析出强化及固溶强化形式来提 高钢的强度和回火稳定性， 而较高的 Mo含量在形成 Mo的碳化物同时， 还 会有一部分多余的 Mo固溶在基体中， 以固溶强化的形式提高钢的回火稳定 性。回火稳定性的提高有利于提高回火温度，从而降低热处理后的残余应力， 提高冲击韧性。 但是由于 Mo是贵金属， 含量过高， 则大大提高生产成本。 在本发明的技术方案中将 Mo 含量设定为 0.5〜0.75%，优选 0.6〜0.75 %，更 优选 0.61〜0.72 %， 最优选 0.66〜0.70 %。
V： V 能形成碳化物， 能够细化晶粒， 提高钢的强度和韧性。 但含量达 到一定量后， 其效果增加不明显， 又因为钒是贵金属， 其价格很高， 会导致 生产成本的增加。所以，本发明中将 V含量控制在 0.01〜0.10%，优选 0.05〜 0.09 % , 更优选 0.05〜0.08 %。
Nb: Nb 能够细化晶粒， 形成碳化物， 提高钢的强度和韧性。 但含量达 到一定量时， 能够显现的效果便不明显， 同时因为价格很高， 所以本发明中 将其含量控制在 0.01〜0.05%， 优选 0.02〜0.04%。
P: 磷为杂质元素， 越低越好， 在本发明中， 当磷元素超过 0.015%会增 加微观偏析，影响钢的冲击韧性，因此本发明中应将磷含量控制为 0.015%。
S: 硫也为杂质元素， 越低越好。 在本发明中， 当硫含量超过 0.005%会 增加硫化物含量， 影响钢的冲击韧性， 所以本发明中应将硫含量控制为 0.005%。
在本发明技术方案中， 发明人添加了含量较高的 Mo， 而且添加了 Nb、 V元素， 这些金属元素在细化晶粒的同时还提高了钻杆的强度， 可以使钻杆 在后续较高的回火温度下达到 135ksi的强度水平。
相应地， 本发明还提供上述高强度钻杆的制造方法， 其包括： 制造具有 上述各元素质量百分比组成的钻杆， 然后对其进行淬火和回火操作。 在淬火 歩骤中， 将钻杆整体加热到 900〜950°C后， 进行钻杆内表面轴流喷水冷却和 钻杆外表面层流喷水冷却， 同时控制钻杆加厚管端的喷水量与管体的喷水量 不同以使不同壁厚的管体和加厚管端具有基本相同的冷却速度； 在回火歩骤 中， 控制回火温度为 650〜675°C。
在本发明的一个优选的实施方式中， 在所述淬火歩骤中， 将钻杆整体加 热到 910〜940°C， 优选加热到 920〜940°C， 更优选加热到 910〜930°C。
在本发明的另一个优选的实施方式中， 在所述回火歩骤中， 控制回火温 度为 650〜670°C， 或者 660〜670°C。
在本发明中， 在所述淬火歩骤中， 通过进行钻杆内表面轴流喷水冷却和 钻杆外表面层流喷水冷却， 同时控制钻杆加厚管端的喷水量与管体的喷水量 不同以使不同壁厚的管体和加厚管端具有基本相同的冷却速度。所谓"基本" 指的是不同壁厚的管体和加厚管端的冷却速度之差小于或等于 10%，优选小 于或等于 5 %。
在本技术方案中， 发明人首先对钻杆管端进行加厚处理， 制成加厚钻杆 的管体； 经整体加热到 900~950°C后， 放置于一个旋转淬火台架上， 在钢管 旋转的同时， 进行钻杆内表面轴流喷水冷却和钻杆外表面层流喷水冷却， 并 通过控制钻杆加厚管端和管体的不同喷水量， 使不同壁厚的管体和加厚管端 有基本相同的冷却速度， 以保证钻杆管体和加厚管端具有相同的淬火组织； 最后经 650~675°C回火处理使管体与加厚管端达到 135ksi的力学性能。
较之现有技术， 本发明所述的超高韧性高强度钻杆及其制造方法具有下 列有益效果：
在钻杆达到 135ksi 的强度情况下， 其 -20°C纵向全尺寸冲击韧性 100J 且冲击韧性远高于美国石油协会的 《钻杆规范》 （API SPEC 5DP) 中的 S级 钻杆水平， 满足了深井、 超深井、 水平井、 大位移井等高难度井的钻探要求。 具体实施方式
下面将结合具体实施例和对比例对于本发明所述的技术方案作出进一歩 的说明。
实施例 1-6
表 1列出了本发明的实施例 1-6与目前常用的 CrMnMo钢 （对比例） 的 化学元素配比。
Figure imgf000005_0001
Figure imgf000005_0002
采用下述歩骤制造本发明所述的超高韧性高强度钻杆 （实施例 1-6的详 细工艺参数和力学性能参阅表 2):
首先进行钻杆管端加厚处理， 制成加厚的钻杆管体； 将钻杆整体加热到 900°C~950°C ; 将钻杆整体放置在一个旋转淬火台架上， 在钢管旋转的同时， 进行钻杆内表面轴流喷水冷却与外表面层流喷水冷却， 同时控制钻杆加厚管 端的喷水量与管体的喷水量不同以使不同壁厚的管体和加厚管端具有相同的 冷却速度， 保证管体和加厚端具有相同的淬火组织； 最后经 650~675°C回火 处理后， 钻杆管体与钻杆加厚管端达到所需要的 135ksi力学性能。
表 2
Figure imgf000006_0001
由表 2可知， 在达到同样 135ksi强度的条件下， 本技术方案所述的超高 韧性高强度钻杆的回火温度远高于对比例的普通 135ksi钻杆的回火温度， 从 而使本发明的超高韧性高强度钻杆的 -20°C纵向全尺寸冲击韧性 100J，远远 高于普通 135ksi钻杆的冲击韧性水平， 可以在经常处于交变应力及摩擦碰撞 的恶劣情况下进行长时间地工作。 要注意的是， 以上列举的仅为本发明的具体实施例， 显然本发明不限于 上述实施例， 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. 一种超高韧性高强度钻杆， 其特征在于， 其各化学元素质量百分 含量为：
C: 0.24—0.30% , Si: 0·卜 0·5%， Μη: 0·7〜1 ·5%， Cr: 0.7—1.5%, Mo: 0·5〜0·75%， V: 0.01〜0.10%，Nb: 0·01〜0·05%， Ρ≤0·015%， S<0.005%, 其余为 Fe和不可避免的杂质。
2. 如权利要求 1 所述的超高韧性高强度钻杆， 其特征在于， 其各化 学元素质量百分含量为：
C: 0.25—0.29% , Si: 0.24—0.38% , Μη: 0·92〜1 · 17%， Cr: 0·95〜 1.22%, Mo: 0.6—0.75% , V： 0·05〜0·09%， Nb: 0·02〜0·04%， P<0.015%, S≤0.005%， 其余为 Fe和不可避免的杂质。
3. 如权利要求 1 所述的超高韧性高强度钻杆， 其特征在于， 其各化 学元素质量百分含量为：
C: 0.26—0.28% , Si: 0.27—0.36% , M 0·70〜1 · 17%， Cr: 0·95〜 1.22%, Mo: 0·61〜0·72%， V： 0·05〜0·08%， Nb: 0·02〜0·04%， Ρ<0.015%, S≤0.005%， 其余为 Fe和不可避免的杂质。
4. 如权利要求 1所述的超高韧性高强度钻杆， 其特征在于， Mo的质 量百分含量为 0.66〜0.70%。
5. 如权利要求 1-4中任一项所述的超高韧性高强度钻杆的制造方法， 其特征在于：
加工形成具有所需化学元素质量百分含量组成的钻杆；
在淬火歩骤中， 将钻杆整体加热到 900〜950°C后， 进行钻杆内表面 轴流喷水冷却和钻杆外表面层流喷水冷却， 同时控制钻杆加厚管端的喷水 量与管体的喷水量不同， 以使不同壁厚的管体和加厚管端具有基本相同的 冷却速度；
在回火歩骤中， 控制回火温度为 650〜675 °C。
6. 如权利要求 5所述的方法， 其特征在于， 在淬火歩骤中， 将钻杆 整体加热到 910〜940°C， 或者 920〜940°C， 或者 910〜930°C。
7. 如权利要求 5所述的方法， 其特征在于， 在回火歩骤中， 控制回 火温度为 650〜670°C， 或者 660〜670°C。
8. 如权利要求 5所述的方法， 其特征在于， 在淬火歩骤中， 通过同 时控制钻杆加厚管端的喷水量与管体的喷水量不同，以使不同壁厚的管体 和加厚管端的冷却速度之差小于或等于 10%， 或者小于或等于 5 %。
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