WO2018099381A1 - 一种高强高韧射孔枪管及其制造方法 - Google Patents

一种高强高韧射孔枪管及其制造方法 Download PDF

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WO2018099381A1
WO2018099381A1 PCT/CN2017/113460 CN2017113460W WO2018099381A1 WO 2018099381 A1 WO2018099381 A1 WO 2018099381A1 CN 2017113460 W CN2017113460 W CN 2017113460W WO 2018099381 A1 WO2018099381 A1 WO 2018099381A1
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strength
perforating
mpa
barrel
toughness
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French (fr)
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WO2018099381A8 (zh
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董晓明
张忠铧
赵存耀
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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 DE112017006053.2T priority Critical patent/DE112017006053T5/de
Priority to US16/463,634 priority patent/US11459643B2/en
Publication of WO2018099381A1 publication Critical patent/WO2018099381A1/zh
Publication of WO2018099381A8 publication Critical patent/WO2018099381A8/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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/002—Stainless steels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/006—Continuous casting of metals, i.e. casting in indefinite lengths of tubes
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/10—Supplying or treating molten metal
    • B22D11/11—Treating the molten metal
    • B22D11/114—Treating the molten metal by using agitating or vibrating means
    • B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
    • 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
    • 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
    • C22C38/04—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
    • C22C38/22—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
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron

Definitions

  • the invention relates to a perforating barrel and a manufacturing method thereof, in particular to a perforating barrel used in the field of petroleum exploitation and a manufacturing method thereof.
  • Perforation is an extremely important technology in petroleum exploration and development system engineering and one of the important means to improve oil and gas well recovery.
  • the perforating gun tube is used as a spring frame to position the perforating direction, and the perforating fire-fighting device is protected from the fluid immersion in the well, withstands the pressure and reduces the damage to the downhole casing during the perforating operation, and during the explosion process.
  • Protect the oil casing Due to the harsh working conditions, the barrel is not only affected by medium corrosion, well temperature and pressure, but also mainly from the high pressure and huge shock wave generated by the perforating projectile. Therefore, the quality, strength and toughness of the perforating barrel are especially The lateral impact toughness requirements are very strict.
  • the requirements for the perforating barrel are not only strong in pressure resistance, but also need to perforate the barrel to resist the high pressure environment generated by the deep well and the perforating projectile, and the anti-expansion deformation ability is strong, effectively preventing the stuck phenomenon.
  • the perforating barrel requires high toughness matching at the same time, because the high-strength perforating barrel has insufficient toughness, especially when the lateral impact toughness is low, the perforation burr is high and the gun body is cracked, resulting in Accidents such as Kajing.
  • the perforating barrel tube has higher requirements on the uniformity of the circumferential strength of the barrel due to the perforation quality.
  • the publication number is CN103352169A, and the publication date is October 16, 2013.
  • the Chinese patent document entitled "separate steel tube material for perforating gun tube body and heat treatment method thereof" discloses a perforating gun tube body.
  • the steel pipe material, the strength of the seamless steel pipe for the perforating gun pipe body prepared by the technical solution disclosed in the patent document reaches 150 steel grade, but the process is complicated, and the quenching and tempering heat treatment is adopted, and the cost is high.
  • the publication number is CN103614631A, and the publication date is March 5, 2014.
  • the Chinese patent document entitled "Rare earth-containing perforating gun body material and its preparation method” discloses a rare earth perforating gun body material, which adopts Rare earth elements are added to improve the morphology of inclusions and improve the toughness index.
  • the perforating gun tube disclosed in this patent document has a yield strength of 863 to 882 MPa and a tensile strength of 951 to 965 MPa.
  • Japanese Patent Publication No. JP11131189A published on May 18, 1999, entitled: "Steel Tube and Method of Manufacture" discloses a steel pipe which is heated in the range of 400-750 ° C and then at 20%. Or 60% change Rolling is performed in a range of the above amount, and a steel pipe product having a yield strength of 950 MPa or more and having good toughness is produced.
  • the process disclosed in this patent document is difficult to roll in large scale due to the low heating temperature, and it is difficult to mass-produce industrially. At the same time, martensite structure is easily generated due to a low rolling temperature.
  • One of the objects of the present invention is to provide a high-strength and high-toughness perforating barrel which has high strength, good toughness, and uniform circumferential strength of the perforating barrel.
  • the present invention provides a high strength and high tenacity perforating barrel having a chemical element mass percentage of:
  • C is a precipitate forming element, which can increase the strength of steel.
  • the mass percentage of C is less than 0.15%, the hardenability is lowered, thereby reducing the toughness, so that the present invention
  • the strength of the high-strength and high-tough perforating barrel is difficult to achieve high strength requirements; when the mass percentage of C is higher than 0.22%, C forms a large amount of coarse precipitates with Cr and Mo, and significantly increases the segregation of steel, resulting in
  • the toughness of the high-strength and high-toughness perforating barrel is significantly reduced, and it is difficult to achieve the requirements of high strength and high toughness. Therefore, in the high-strength and high-strength perforating barrel of the present invention, the mass percentage of C is controlled to be 0.15-0.22%.
  • Si:Si is solid-dissolved in ferrite to increase the yield strength of steel.
  • the mass percentage of Si is higher than 0.4%, the processing and toughness are deteriorated; when the mass percentage of Si is less than 0.1%, the steel is easy. Oxidation. Therefore, in the high-strength and high-resistance perforating barrel of the present invention, the mass percentage of Si is controlled to be 0.1% to 0.4%.
  • Mn is an austenite forming element, which can improve the hardenability of steel.
  • Mn is an austenite forming element, which can improve the hardenability of steel.
  • the mass percentage of Mn is less than 0.5%, the hardenability of steel is significantly lowered, and Markov is lowered.
  • the proportion of the body thus reduces the toughness; when the mass percentage of Mn is more than 1%, the segregation of the structure in the steel is significantly increased, which affects the uniformity and impact performance of the hot rolled structure. Therefore, the mass percentage of Mn in the high-strength and high-toughness perforating barrel of the present invention is limited to 0.5-1.0%.
  • Cr In the high-strength and high-toughness perforating barrel of the present invention, Cr strongly enhances the hardenability element, forms a strong precipitate, and precipitates precipitates during tempering to increase the strength of the steel.
  • the mass percentage of Cr when the mass percentage of Cr is higher than 0.7%, it is easy to precipitate coarse M 23 C 6 precipitates at the grain boundary, and reduce the toughness of the high-strength and high-toughness perforating barrel; when the mass percentage of Cr is less than 0.3%, The hardenability of the steel of the high strength and high tenacity perforating barrel is insufficient. Therefore, the mass percentage of Cr in the high-strength and high-toughness perforating barrel of the present invention is 0.3-0.7%.
  • the strength and tempering stability of the steel are improved by controlling the precipitates and the solid solution strengthening form, and the high-strength and high-resistance perforating barrel of the present invention has a low carbon content. Therefore, when the mass percentage of added Mo is higher than 0.7%, segregation structure is likely to occur; when the mass percentage of Mo is less than 0.3%, the strength cannot reach the requirement of high strength. Therefore, the mass percentage of Mo in the high-strength and high-resistance perforating barrel of the present invention is 0.3-0.7%.
  • Nb is a fine crystal and precipitation strengthening element, which can make up for the decrease of strength caused by carbon reduction.
  • Nb has good anti-tempering stability, which is beneficial to improve the difference of the high-strength and high-resistance perforating barrel.
  • the intensity uniformity of the position When the mass percentage of Nb is less than 0.01%, the effect is not obvious; when the mass percentage of Nb is higher than 0.04%, coarse Nb (CN) is easily formed, thereby reducing the high-strength and high-toughness perforating barrel. toughness. Therefore, the mass percentage of Nb of the high strength and high tenacity perforating barrel of the present invention is from 0.01% to 0.04%.
  • V is a typical precipitation strengthening element that compensates for the decrease in strength due to carbon reduction.
  • V has good anti-tempering stability, which is beneficial to improve the strength uniformity of different positions of the high-strength and high-perforation perforating barrel.
  • the mass percentage of V is less than 0.1%, the strengthening effect is difficult to achieve the high strength requirement of the high-strength and high-perforation perforating barrel of the present invention; when the mass percentage of V is higher than 0.2%, it is easy to form a coarse V(CN), thereby reducing the toughness of the high strength and high toughness perforating barrel. Therefore, the mass percentage of V of the high strength and high tenacity perforating barrel of the present invention is limited to 0.1% to 0.2%.
  • Ti is a strong carbonitride forming element, which refines the austenite grains remarkably, and can compensate for the decrease in strength due to carbon reduction. When the mass percentage of Ti is higher than 0.05%, coarse TiN is easily formed, which is lowered. The toughness of the high strength and high tenacity perforating barrel of the present invention.
  • B can also significantly improve the hardenability.
  • B is used to solve the problem of poor hardenability due to a low content of C. Since the mass percentage of B is less than 0.0015%, the effect of improving the hardenability is not significant; when the mass percentage of B is higher than 0.005%, the BN brittle phase is easily formed, and the toughness of the high-strength and high-perforation perforating barrel is lowered. Therefore, the mass percentage of B in the high-strength and high-toughness perforating barrel of the present invention is controlled to be 0.0015% to 0.005%.
  • Al is a good deoxidizing nitrogen-fixing element and can refine grains. Therefore, the mass percentage of controlling Al in the technical solution of the present invention is 0.01 to 0.05%.
  • Ca can purify molten steel, promote spheroidization of MnS, and improve the impact toughness of the high-strength and high-perforation perforating barrel of the present invention, but when the mass percentage of Ca is higher than 0.004% It is easy to form coarse non-metallic inclusions.
  • N is a harmful impurity element in steel. If the content is too high, the toughness of steel will be high. Therefore, the mass percentage of controlling N is N ⁇ 0.008%.
  • the unavoidable impurities mainly include P and S, which is disadvantageous to the improvement of the toughness of the high-strength and high-toughness perforating barrel of the present invention. Therefore, the mass percentage is controlled at: P ⁇ 0.015, S ⁇ 0.003.
  • the high-strength and high-toughness perforating barrel of the present invention also satisfies 0 ⁇ (Ti-3.4*N) ⁇ 0.025%.
  • Ti and N are further defined in the present invention, and Ti and N also need to satisfy the above formula.
  • the inventors of the present invention found that by limiting the ratio of the mass percentage between Ca and S elements, the effect of Ca on eliminating MnS inclusions can be further improved.
  • the high strength and high tenacity perforating barrel of the invention also satisfies Ca/S ⁇ 1.5.
  • the microstructure is tempered sorbite.
  • the grain level is above 9 or higher, and the level of MnS inclusions in the high-strength and high-perforation perforating barrel is below 0.5.
  • the yield strength is 896-1103 MPa
  • the tensile strength is ⁇ 965 MPa
  • the lateral Charpy impact energy of 0 degree is ⁇ 130 J
  • the high-strength and high-impedance perforating gun The extreme difference of the yield strength of the tube is within 60 MPa, and the extreme difference of the tensile strength of the high-strength and high-resistance perforating barrel is also within 60 MPa.
  • the yield strength is 965-1173 MPa
  • the tensile strength is ⁇ 1034 MPa
  • the lateral Charpy impact energy of 0 degree is ⁇ 130 J
  • the high-strength and high-impedance perforating gun The extreme difference of the yield strength of the tube is within 60 MPa, and the extreme difference of the tensile strength of the high-strength and high-resistance perforating barrel is also within 60 MPa.
  • the yield strength is 1069-1276 MPa
  • the tensile strength is ⁇ 1138 MPa
  • the lateral Charpy impact energy of 0 degree is ⁇ 120 J
  • the high-strength and high-impedance perforating gun The extreme difference of the yield strength of the tube is within 60 MPa, and the extreme difference of the tensile strength of the high-strength and high-resistance perforating barrel is also within 60 MPa.
  • the “extreme difference” of the yield strength or the tensile strength refers to taking a plurality of detection points along the circumferential direction of the perforating barrel, and measuring the axial yield strength and the axial tensile of the detection points.
  • the difference between the maximum and minimum values of the respective axial yield strengths at these points, and the difference between the maximum and minimum values of the tensile strength is the "very poor", so the "very poor” reflects within 60 MPa.
  • the hole barrel has good strength uniformity and can improve the perforation quality.
  • Another object of the present invention is to provide a method for manufacturing the high strength and high tenacity perforating barrel described above, which comprises the steps of:
  • the transverse impact toughness of the steel used in the perforating barrel is required to be high, and the stability of the mechanical properties of the tube needs to be maintained. Since the factors affecting the lateral impact toughness are more influential than the longitudinal impact toughness, the MnS inclusions formed in the steel of the high-strength and high-perforation perforating barrel can significantly reduce the transverse impact toughness of the steel, and the branches formed during the casting process. Crystal segregation will form a banded composition segregation structure after rolling, which will also affect the transverse impact toughness of the steel, and the above two factors have no significant effect on the longitudinal impact toughness.
  • the process parameters of the casting process in the step (2) are controlled to reduce dendrite segregation of the tube blank. Moreover, the control of MnS inclusions is achieved by rational optimization of the chemical element distribution ratio.
  • the MnS in order to further reduce the MnS inclusions, in the step (1), can be realized by using an electric furnace for smelting, and then using external refining, vacuum degassing, and argon stirring to reduce the contents of O and H. Control of inclusions. Further, in the step (1), those skilled in the art can also perform inclusion denaturation by Ca treatment to further reduce the content of MnS inclusions.
  • the tube blank is soaked at 1200 to 1240 ° C; then perforated, the perforation temperature is 1180 to 1240 ° C; and the controlled rolling temperature is 950. ⁇ 1000 ° C; reheating furnace temperature is 950-1000 ° C; tension reducing diameter is 900 ⁇ 950 ° C.
  • quenching temperature is 880-920 ° C, heat preservation 30-60 min; then tempering: tempering temperature is 550-650 ° C , holding time 50-80min.
  • the heat sizing temperature is 500 to 550 °C.
  • the yield strength is 896-1103MPa
  • the tensile strength is ⁇ 965MPa
  • the lateral Charpy impact energy of 0 degree is ⁇ 130J
  • the high-strength and high-perforation perforating barrel The extreme difference in yield strength is within 60 MPa, and the extreme difference in tensile strength of the high-strength and high-strength perforating barrel is also within 60 MPa.
  • the yield strength is 965-1173 MPa
  • the tensile strength is ⁇ 1034 MPa
  • the lateral Charpy impact energy of 0 degree is ⁇ 130 J
  • the high-strength and high-impedance perforating barrel The range of the yield strength is within 60 MPa, and the tensile strength of the high-strength and high-perforation perforating barrel is also within 60 MPa.
  • the yield strength is 1069-1276MPa
  • 0 degree transverse Charpy impact energy is not less than ⁇ 120J
  • the high-strength and high-toughness perforating barrel has a yield strength within 60MPa
  • the tensile strength of the high-strength and high-resistance perforating barrel The range is also within 60 MPa.
  • the manufacturing method of the present invention has a simple process and is easy to be mass-produced, and the high-strength and high-strength perforating barrel obtained by the manufacturing method of the present invention has the advantages of high strength and good toughness.
  • Example 1 is a photomicrograph of a high strength and high tenacity perforating barrel of Example 5.
  • Figure 3 is a photograph of the microstructure of a conventional perforating barrel of Comparative Example 5.
  • the tube blank is soaked at 1200 ⁇ 1240 ° C; then perforated, the perforation temperature is 1180 ⁇ 1240 ° C; the controlled rolling temperature is 950 ⁇ 1000 ° C; the reheating furnace temperature is 950-1000 ° C; The reducing temperature is 900-950 ° C;
  • the hot sizing temperature is 500-550 °C.
  • Table 1 lists the mass ratios of the chemical elements of the high-strength and high-toughness perforating barrels of Examples 1-5 and the conventional perforating barrel tubes of Comparative Examples 1-5.
  • Table 2 lists the specific process parameters of the manufacturing methods of the respective examples and comparative examples. Table 2.
  • Table 3 lists the results of the measurements of the high strength and high tenacity perforating barrels of Examples 1-5 and the conventional perforating barrels of Comparative Examples 1-5.
  • Comparative Example 4 the mass percentage of Ca was too high, resulting in the formation of a coarse non- Metal inclusions, thus increasing the brittleness of Comparative Example 4 and reducing the lateral impact energy.
  • Ti-3.4*N ⁇ 0 of Comparative Example 4 is easy to form BN after heat treatment, which is disadvantageous to the improvement of the strength and toughness of Comparative Example 4;
  • the Mo content was high and the Ca/S ratio was less than 1.5, resulting in the formation of coarse MnS inclusions and carbides of Mo in Comparative Example 5, which lowered the lateral impact toughness.
  • Example 1 is a photomicrograph of a high strength and high tenacity perforating barrel of Example 5. As shown in Fig. 1, the microstructure of Example 5 is tempered sorbite and does not have a banded component segregation structure, and the level of MnS inclusions is 0.5 or less.
  • FIG. 2 is a photograph of a microstructure of a conventional perforating barrel of Comparative Example 2. As shown in Fig. 2, in Comparative Example 2, the mass fraction of the C and Cr elements was high, and the segregation structure of the band component was severe.
  • Figure 3 is a photograph of the microstructure of a conventional perforating barrel of Comparative Example 5. As shown in FIG. 3, coarse MnS inclusions were formed in Comparative Example 5.

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Abstract

一种高强高韧射孔枪管，其化学元素质量百分配比为：C：0.15％-0.22％、Si：0.1％-0.4％、Mn：0.5％-1％、Cr：0.3％-0.7％、Mo：0.3％-0.7％、Nb：0.01％-0.04％、V：0.1％-0.2％、Ti：0.02％-0.05％、B：0.0015％-0.005％、Al：0.01％-0.05％、Ca：0.001％-0.004％、N≤0.008％，余量为Fe和其他不可避免的杂质。相应地，本发明还公开了一种上述的高强高韧射孔枪管的制造方法。本发明所述的高强高韧射孔枪管的强度高，韧性好，周向强度均匀，适用于石油勘探与开采领域的应用。

Description

一种高强高韧射孔枪管及其制造方法 技术领域
本发明涉及一种射孔枪管及其制造方法，尤其涉及一种用于石油开采领域的射孔枪管及其制造方法。
背景技术
射孔是石油勘探与开发系统工程中极其重要的一项技术，是提高油气井采收率的重要手段之一。射孔作业中射孔枪管作为弹架对射孔方向进行定位，保护射孔火工器件不受井内流体浸泡、承受压力和减轻射孔作业时对井下套管的损害，并在爆炸过程中保护油层套管。由于其工作条件恶劣，枪管除了受介质腐蚀、井温及压力的影响外，主要威胁来自射孔弹发射时产生的高压及巨大冲击波，因此对射孔枪管的质量、强度和韧性尤其是横向冲击韧性要求非常严格。
对于射孔枪管的要求不仅只是抗压能力强，而且还需要射孔枪管可抵御深井和射孔弹发射时产生的高压环境，而且抗膨胀变形能力强，有效防止卡井现象发生。此外，除了对射孔枪管的强度有所要求以外，也期望能够降低枪体壁厚，提高射孔质量。因此，射孔枪管在要求高强度的同时也需具有高的韧性匹配，因为高强度射孔枪管韧性不足，尤其是横向冲击韧性低时会导致射孔孔眼毛刺高甚至枪体开裂，造成卡井等事故。另外射孔枪管出于射孔质量的考虑，还对枪管的周向强度均匀性要求较高。
公开号为CN103352169A，公开日为2013年10月16日，名称为“射孔枪管管体用无缝钢管材料及其热处理方法”的中国专利文献公开了一种射孔枪管管体用无缝钢管材料，通过该专利文献所公开的技术方案所制备得到的射孔枪管管体用无缝钢管的强度达到150钢级，但是其工艺复杂，采用两次调质热处理，成本较高。
公开号为CN103614631A，公开日为2014年3月5日，名称为“含稀土射孔枪管体材料及其制备方法”的中国专利文献公开了一种含稀土射孔枪管体材料，其采用加入稀土元素以改善夹杂物形态，提高韧性指标。但是此专利文献所公开的射孔枪管屈服强度在863～882MPa，抗拉强度在951～965MPa。
公开号为JP11131189A，公开日为1999年5月18日，名称为：“钢管及其制造方法”的日本专利文献公开了一种钢管，其采用在400-750℃范围内加热，然后在20％或60％变 形量以上的范围内进行轧制，生产出屈服强度950Mpa以上、具有良好韧性的钢管产品。然而该专利文献所公开的工艺由于加热温度较低，轧制难度较大，难以大批量工业化生产，同时由于轧制温度较低，易产生马氏体组织。
发明内容
本发明的目的之一在于提供一种高强高韧射孔枪管，其强度高，韧性佳，且射孔枪管周向强度均匀。
基于上述发明目的，本发明提供了一种高强高韧射孔枪管，其化学元素质量百分比为：
C：0.15％-0.22％、Si：0.1％-0.4％、Mn：0.5％-1％、Cr：0.3％-0.7％、Mo：0.3％-0.7％、Nb：0.01％-0.04％、V：0.1％-0.2％、Ti：0.02％-0.05％、B：0.0015％-0.005％、Al：0.01％-0.05％、Ca：0.001％-0.004％、N≤0.008％，余量为Fe和其他不可避免的杂质。
本发明所述的高强高韧射孔枪管的各化学元素的设计原理为：
C：在本发明所述的技术方案中，C为析出物形成元素，可以提高钢的强度，当C的质量百分比低于0.15％时，会使淬透性降低，从而降低韧性，使得本发明所述的高强高韧射孔枪管的强度难以达到高强度要求；当C的质量百分比高于0.22％时，C与Cr、Mo形成大量粗化的析出物，并显著加重钢的偏析，造成所述的高强高韧射孔枪管的韧性显著降低，难以达到高强度高韧性的要求。因此，在本发明所述的高强高韧射孔枪管中，C的质量百分比控制在0.15-0.22％。
Si：Si固溶于铁素体以提高钢的屈服强度，然而，当Si的质量百分比高于0.4％时，会使加工和韧性恶化；当Si的质量百分比低于0.1％，会使钢容易氧化。因此，在本发明所输的高强高韧射孔枪管中，Si的质量百分比控制在0.1％-0.4％。
Mn：Mn为奥氏体形成元素，可以提高钢的淬透性，在本发明所述的技术方案中，当Mn的质量百分比小于0.5％时，会显著降低钢的淬透性，降低马氏体比例从而降低韧性；当Mn的质量百分比大于1％时，则显著增加钢中的组织偏析，影响热轧组织的均匀性和冲击性能。因此，在本发明所述的高强高韧射孔枪管中对Mn的质量百分比限定在0.5-1.0％。
Cr：在本发明所述的高强高韧射孔枪管中，Cr是强烈提高淬透性元素，强析出物形成元素，回火时析出析出物提高钢的强度。但当Cr的质量百分比高于0.7％时，容易在晶界析出粗大M23C6析出物，降低所述的高强高韧射孔枪管的韧性；当Cr的质量百分比低于0.3％时，则所述的高强高韧射孔枪管的钢的淬透性不足。因此，在本发明所述的高强高韧射孔枪管Cr的质量百分比在0.3-0.7％。
Mo：在本发明所述的技术方案中，通过控制析出物及固溶强化形式来提高钢的强度及回火稳定性，由于本发明所述的高强高韧射孔枪管的碳含量较低，因此添加Mo的质量百分比高于0.7％时，容易产生偏析组织；当Mo的质量百分比低于0.3％时，则强度无法达高强度的要求。因此，在本发明所述的高强高韧射孔枪管的Mo质量百分比在0.3-0.7％。
Nb：Nb是细晶和析出强化元素，可弥补因碳降低而引起的强度的下降，此外，Nb具有良好的抗回火稳定性，有利于提高所述的高强高韧射孔枪管的不同位置的强度均匀性。当Nb的质量百分比小于0.01％时，其作用效果不明显；当Nb的质量百分比高于0.04％时，则容易形成粗大的Nb(CN)，从而降低所述的高强高韧射孔枪管的韧性。因此，在本发明所述的高强高韧射孔枪管的Nb的质量百分比在0.01％-0.04％。
V：V是典型的析出强化元素，可弥补因碳降低而引起的强度的下降。此外，V具有良好的抗回火稳定性，有利于提高所述的高强高韧射孔枪管的不同位置的强度均匀性。当V的质量百分比小于0.1％时，则强化效果难以使本发明所述的高强高韧射孔枪管的强度达到高强度要求；当V的质量百分比高于0.2％时，则容易形成粗大的V(CN)，从而降低所述的高强高韧射孔枪管的韧性。因此，在本发明所述的高强高韧射孔枪管的V的质量百分比限定在0.1％-0.2％。
Ti：Ti是强碳氮化物形成元素，显著细化奥氏体晶粒，可弥补因碳降低而引起的强度的下降，当Ti的质量百分比高于0.05％时，易形成粗大的TiN，降低本发明所述的高强高韧射孔枪管的韧性。
B：B也可以显著提高淬透性，在本发明所述的技术方案中，B用于解决因C的含量较低所带来的淬透性差的问题。由于B的质量百分比低于0.0015％时，提高淬透性作用不显著；当B的质量百分比高于0.005％时，易形成BN脆性相，降低所述的高强高韧射孔枪管的韧性。因此，在本发明所述的高强高韧射孔枪管中B的质量百分比控制在0.0015％-0.005％。
Al：Al是良好的脱氧固氮元素，可细化晶粒，因此，本发明所述的技术方案中控制Al的质量百分比为0.01～0.05％。
Ca：在本发明所述的技术方案中，Ca可以净化钢液，促使MnS球化，提高本发明所述的高强高韧射孔枪管的冲击韧性，但Ca的质量百分比高于0.004％时，易形成粗大的非金属夹杂物。
N：N是钢中的有害杂质元素，含量过高会钢的韧性，因此控制N的质量百分比为N≤0.008％
在本发明所述的技术方案中，不可避免的杂质主要包括P和S，不利于本发明所述的高强高韧射孔枪管的韧性提高，因此，其质量百分比控制在：P≤0.015，S≤0.003。
进一步地，在本发明所述的高强高韧射孔枪管中，其还满足0<(Ti-3.4*N)<0.025％。为了保证Ti和N的充分结合，以避免B和N形成BN脆性相而降低钢材的韧性，因此，本发明中对Ti和N进行了进一步限定，Ti和N还需要满足上述公式。
进一步地，在本发明所述的高强高韧射孔枪管中，其还满足Ca/S≥1.5。
为了进一提高本发明所述的高强高韧射孔枪管的韧性，本案发明人发现通过对Ca和S元素间质量百分比比值的限定，可以进一步提高Ca消除MnS夹杂物的作用效果，因此，本发明所述的高强高韧射孔枪管中还满足Ca/S≥1.5。
进一步地，在本发明所述的高强高韧射孔枪管中，其微观组织为回火索氏体。
进一步地，在本发明所述的高强高韧射孔枪管中，其晶粒级别在9级以上，所述高强高韧射孔枪管中的MnS夹杂物的级别在0.5级以下。
进一步地，在本发明所述的高强高韧射孔枪管中，其屈服强度为896-1103MPa，抗拉强度≥965MPa，0度横向夏比冲击功≥130J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
进一步地，在本发明所述的高强高韧射孔枪管中，其屈服强度为965-1173MPa，抗拉强度≥1034MPa，0度横向夏比冲击功≥130J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
进一步地，在本发明所述的高强高韧射孔枪管中，其屈服强度为1069-1276MPa，抗拉强度≥1138MPa，0度横向夏比冲击功≥120J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
需要说明的是，上述屈服强度或抗拉强度的“极差”是指，沿着射孔枪管的周向方向取若干个检测点，测量这些检测点的轴向屈服强度和轴向抗拉强度，这些点的各个轴向屈服强度的最大值和最小值的差值，以及抗拉强度的最大值和最小值的差值就是“极差”，因此“极差”在60MPa以内反映了射孔枪管具有良好的强度均匀性，可以提高射孔质量。
另外，本发明的另一目的在于提供一种上文所述的高强高韧射孔枪管的制造方法，其包括步骤：
(1)冶炼；
(2)铸造：浇铸成圆坯，浇铸过程中采用电磁搅拌工艺，电磁搅拌采用的电流为600-650A，频率为8-20Hz，以降低管坯枝晶偏析，同时控制浇铸过程中的钢水过热度低于 30℃；
(3)轧制；
(4)热处理；
(5)热定径。
在本发明所述的技术方案中，为了保证射孔枪管具有良好的射孔性能，因而要求射孔枪管采用的钢的横向冲击韧性较高，并且需要保持管体力学性能的稳定性。由于影响横向冲击韧性的因素比纵向冲击韧性影响因素更多，并且高强高韧射孔枪管的钢中所形成的MnS夹杂物会显著降低钢的横向冲击韧性，同时在浇铸过程中形成的枝晶偏析会在轧管后形成带状成分偏析组织，也会影响钢的横向冲击韧性，而上述两种因素对纵向冲击韧性无显著影响。
因此，为了提高本发明所述的高强高韧射孔枪管的强度和韧性，对步骤(2)中浇铸过程的工艺参数进行了控制从而降低了管坯枝晶偏析。并且，通过对化学元素成分配比的合理优化从而实现了对MnS夹杂物的控制。
需要说明的是，为了进一步降低MnS夹杂物，在步骤(1)中，可以采用电炉冶炼后，然后采用炉外精炼、真空脱气和氩气搅拌后，以降低O、H含量从而实现了MnS夹杂物的控制。此外，在步骤(1)中，本领域内技术人员还可以通过Ca处理进行夹杂物变性从而进一步降低了MnS夹杂物的含量。
进一步地，在本发明所述的制造方法中，在所述步骤(3)中，管坯在1200～1240℃下均热；然后穿孔，穿孔温度为1180～1240℃；控制轧制温度为950～1000℃；再加热炉温度为950-1000℃；张力减径温度为900～950℃。
进一步地，在本发明所述的制造方法中，在所述步骤(4)中，先淬火：淬火温度为880-920℃，保温30-60min；然后回火：回火温度为550-650℃，保温时间50-80min。
进一步地，在本发明所述的制造方法，在所述步骤(5)中，热定径温度为500-550℃。
本发明所述的高强高韧射孔枪管强度达到130ksi钢级时，屈服强度896-1103MPa，抗拉强度≥965MPa，0度横向夏比冲击功≥130J，所述高强高韧射孔枪管屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
本发明所述的高强高韧射孔枪管强度达到140ksi钢级时，屈服强度965-1173MPa，抗拉强度≥1034MPa，0度横向夏比冲击功≥130J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
本发明所述的高强高韧射孔枪管强度达到155ksi钢级时，屈屈服强度1069-1276MPa， 抗拉强度≥1138MPa，0度横向夏比冲击功不小于≥120J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
此外，本发明所述的制造方法工艺简单，易于大规模生产实施，采用本发明所述的制造方法所获得的高强高韧射孔枪管具有强度高、韧性好的优点。
附图说明
图1为实施例5的高强高韧射孔枪管的微观组织照片。
图2为对比例2的常规射孔枪管的微观组织照片。
图3为对比例5的常规射孔枪管的微观组织照片。
具体实施方式
下面将结合说明书附图和具体的实施例对本发明所述的高强高韧射孔枪管及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-5和对比例1-5
实施例1-5的高强高韧射孔枪管和对比例1-5的常规射孔枪管采用下述步骤制得：
(1)冶炼：采用电炉进行初炼，控制各化学元素的质量百分比如表1所示，初炼后进行炉外精炼，真空脱气和氩气搅拌后，采用Ca处理进行夹杂物变性，从而降低夹杂物含量；
(2)铸造：浇铸成圆坯，浇铸过程中采用电磁搅拌工艺，电磁搅拌采用的电流为600-650A，频率为8-20Hz，以降低管坯枝晶偏析，同时控制浇铸过程中的钢水过热度低于30℃；
(3)轧制：，管坯在1200～1240℃下均热；然后穿孔，穿孔温度为1180～1240℃；控制轧制温度为950～1000℃；再加热炉温度为950-1000℃；张力减径温度为900～950℃；
(4)热处理：先淬火：淬火温度为880-920℃，保温30-60min；然后回火：回火温度为550-650℃，保温时间50-80min；
(5)热定径：热定径温度为500-550℃。
表1列出了实施例1-5的高强高韧射孔枪管和对比例1-5的常规射孔枪管钢中各化学元素的质量百分配比。
表1.(wt％，余量为Fe和除了P和S之外的其他不可避免杂质元素)
Figure PCTCN2017113460-appb-000001
Figure PCTCN2017113460-appb-000002
表2列出了各实施例和对比例的制造方法的具体工艺参数。表2.
Figure PCTCN2017113460-appb-000003
Figure PCTCN2017113460-appb-000004
对上述实施例1-5的高强高韧射孔枪管和对比例1-5的常规射孔枪管取样，进行各项性能测试，将试验所获得的结果列于表3中。
表3列出了实施例1-5的高强高韧射孔枪管和对比例1-5的常规射孔枪管经测试后所测得的数据结果。
表3.
Figure PCTCN2017113460-appb-000005
从表3可以看出，本案各实施例的屈服强度、抗拉强度和横向冲击功都显著高于各对比例的屈服强度、抗拉强度和横向冲击功，说明本案各实施例的强度高、韧性好。此外，各实施例屈服强度的极差在60MPa以内，并且抗拉强度的极差也在60MPa以内，说明了各实施例的周向强度均匀。
结合表1至表3可以看出，其中，对比例1的C和V的质量百分比低于本案所限定的元素质量范围，因而导致其淬透性低，热处理之后所获得的强度偏低；对比例2的C和Cr元素的质量百分比较高，导致其带状成分偏析组织严重，因此对比例2的横向冲击功显著降低，屈服强度的极差和抗拉强度的极差均较大；对比例3没有添加B和Ti元素，导致其横向冲击功降低，屈服强度的极差和抗拉强度的极差均较大；对比例4中由于Ca的质量百分比过高，导致其形成粗大的非金属夹杂物，因而使对比例4脆性增加，横向冲击功降低，此外，对比例4的Ti-3.4*N＜0，因而热处理后易形成BN，不利于对比例4的强度和韧性提高；对比例5中Mo含量偏高并且Ca/S比值小于1.5，导致对比例5形成粗大的MnS夹杂物和Mo的碳化物，降低了其横向冲击韧性。
图1为实施例5的高强高韧射孔枪管的微观组织照片。如图1所示，实施例5的微观组织为回火索氏体，且不具有带状成分偏析组织，MnS夹杂物的级别在0.5级以下。
图2为对比例2的常规射孔枪管的微观组织照片。如图2所示，对比例2由于C和Cr元素的质量百分比较高，带状成分偏析组织严重。
图3为对比例5的常规射孔枪管的微观组织照片。如图3所示，对比例5中形成粗大的MnS夹杂物。
需要注意的是，以上列举的仅为本发明的具体实施例，显然本发明不限于以上实施例，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 (12)

  1. 一种高强高韧射孔枪管，其特征在于，其化学元素质量百分配比为：
    C：0.15％-0.22％、Si：0.1％-0.4％、Mn：0.5％-1％、Cr：0.3％-0.7％、Mo：0.3％-0.7％、Nb：0.01％-0.04％、V：0.1％-0.2％、Ti：0.02％-0.05％、B：0.0015％-0.005％、Al：0.01％-0.05％、Ca：0.001％-0.004％、N≤0.008％，余量为Fe和其他不可避免的杂质。
  2. 如权利要求1所述的高强高韧射孔枪管，其特征在于，其还满足0<(Ti-3.4*N)<0.025％。
  3. 如权利要求1或2所述的高强高韧射孔枪管，其特征在于，其还满足Ca/S≥1.5。
  4. 如权利要求1所述的高强高韧射孔枪管，其特征在于，其微观组织为回火索氏体。
  5. 如权利要求1所述的高强高韧射孔枪管，其特征在于，其晶粒级别在9级以上，所述高强高韧射孔枪管中的MnS夹杂物的级别在0.5级以下。
  6. 如权利要求1所述的高强高韧射孔枪管，其特征在于，其屈服强度为896-1103MPa，抗拉强度≥965MPa，0度横向夏比冲击功≥130J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
  7. 如权利要求1所述的高强高韧射孔枪管，其特征在于，其屈服强度为965-1173MPa，抗拉强度≥1034MPa，0度横向夏比冲击功≥130J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
  8. 如权利要求1所述的高强高韧射孔枪管，其特征在于，其屈服强度为1069-1276MPa，抗拉强度≥1138MPa，0度横向夏比冲击功≥120J，所述高强高韧射孔枪管的屈服强度的极差在60MPa以内，所述高强高韧射孔枪管的抗拉强度的极差也在60MPa以内。
  9. 如权利要求1-8中任意一项所述的高强高韧射孔枪管的制造方法，其特征在于，包 括步骤：
    (1)冶炼；
    (2)铸造：浇铸成圆坯，浇铸过程中采用电磁搅拌工艺，电磁搅拌采用的电流为600-650A，频率为8-20Hz，以降低管坯枝晶偏析，同时控制浇铸过程中的钢水过热度低于30℃；
    (3)轧制；
    (4)热处理；
    (5)热定径。
  10. 如权利要求9所述的制造方法，其特征在于，在所述步骤(3)中，管坯在1200～1240℃下均热；然后穿孔，穿孔温度为1180～1240℃；控制轧制温度为950～1000℃；再加热炉温度为950-1000℃；张力减径温度为900～950℃。
  11. 如权利要求9所述的制造方法，其特征在于，在所述步骤(4)中，先淬火：淬火温度为880-920℃，保温30-60min；然后回火：回火温度为550-650℃，保温时间50-80min。
  12. 如权利要求9所述的制造方法，其特征在于，在所述步骤(5)中，热定径温度为500-550℃。
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