JP6456986B2 - Ultra-high strength and ultra-tough oil well pipe and method for producing the same - Google Patents

Ultra-high strength and ultra-tough oil well pipe and method for producing the same Download PDF

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JP6456986B2
JP6456986B2 JP2016575505A JP2016575505A JP6456986B2 JP 6456986 B2 JP6456986 B2 JP 6456986B2 JP 2016575505 A JP2016575505 A JP 2016575505A JP 2016575505 A JP2016575505 A JP 2016575505A JP 6456986 B2 JP6456986 B2 JP 6456986B2
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曉 明 董
曉 明 董
忠 ▲フア▼ 張
忠 ▲フア▼ 張
林 柏
林 柏
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宝山鋼鉄股▲分▼有限公司
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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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Description

本発明は、冶金製品およびその製造方法に関して、特に油井管およびその製造方法に関する。   The present invention relates to a metallurgical product and a manufacturing method thereof, and more particularly to an oil well pipe and a manufacturing method thereof.

現在、世界中の深井、超深井の油ガス資源の開発はますます重視されている。わが国の西部の油田資源埋蔵は極めて深く、その地質構造が複雑である。最も深い油ガス井は８０００ｍを超えたため、油ガス井を採掘する油井管の強度についての要求は顕著的に向上されている。公知のように、鋼級が高くなることと、材料の降伏強度が増大されることに連れて、材料の硬度が相応的に増大され、材料の靱性が徐徐に低下され、表面欠陥に対する材料の感度がさらに増大される恐れがある。深井と超深井を採掘するための油井管は、強度と靱性についての要求が非常に高いである。高強度を満足すると共に、靱性の指標をできるだけ向上して、生産使用の安全性を保証できる。   Currently, the development of oil and gas resources in Fukai and Ultra-Fukai around the world is increasingly emphasized. The oil field reserves in the western part of Japan are extremely deep and the geological structure is complicated. Since the deepest oil and gas well exceeds 8000 m, the demand for the strength of the oil well pipe for mining the oil and gas well is remarkably improved. As is well known, as the steel grade increases and the yield strength of the material increases, the hardness of the material increases correspondingly, the toughness of the material decreases gradually, and the material's resistance to surface defects increases. Sensitivity may be further increased. Oil well pipes for mining deep wells and ultra deep wells have very high demands on strength and toughness. Satisfying high strength and improving the toughness index as much as possible to ensure the safety of production use.

だが、鋼の強度、靱性および可塑性は一般的にトレードオフの関係を持つ。つまり、高い強度を有する鋼はその可塑性と靱性が一般的により低いである。同様に、鋼により高い可塑性と靱性をさせると、鋼の強度が低下される。そうすると、高い靱性と高い強度を有する鋼材料についての開発は極めて困難である。今、工業応用を実現できた油井管の強度は１７０ｋｓｉであるが、該油井管の衝撃靱性は５０−８０Ｊだけである。関係な指導文献によれば、圧力容器に用いられる高強度鋼の衝撃靱性はその降伏強度の１０％に達成する必要である。そうすると、国内の各大油田、例えば、タリム油田も深井と超深井用の油井管性能に対して同様な標準を提出した。だが、現有の強度１５０ｋｓｉ（降伏強度１０３４ＭＰａ）以上である高強度鋼の衝撃靱性の性能は該標準よりも遥かに低いである。   However, steel strength, toughness and plasticity generally have a trade-off relationship. That is, steel with high strength is generally lower in plasticity and toughness. Similarly, increasing the plasticity and toughness of steel reduces the strength of the steel. Then, it is very difficult to develop a steel material having high toughness and high strength. At present, the strength of an oil well pipe capable of realizing industrial application is 170 ksi, but the impact toughness of the oil well pipe is only 50-80 J. According to the relevant teaching literature, the impact toughness of high strength steel used for pressure vessels needs to reach 10% of its yield strength. In doing so, each major oil field in the country, such as the Tarim oil field, submitted similar standards for oil well pipe performance for Fukai and Ultra-Fukai. However, the impact toughness performance of high strength steels with an existing strength of 150 ksi (yield strength 1034 MPa) or higher is much lower than the standard.

中国特許文献ＣＮ１０１５８６４５０Ａ（公開日：２００８年８月２７日、名称：「高強度と高靱性のある油井管およびその製造方法」）は油井管用の鋼種に関する。該鋼種の化学元素成分（ｗｔ％）は、Ｃ：０．２２〜０．４％、Ｓｉ：０．１７〜０．３５％、Ｍｎ：０．４５〜０．６０％、Ｃｒ：０．９５〜１．１０％、Ｍｏ：０．７０〜０．８０％、Ａｌ：０．０１５〜０．０４０％、Ｎｉ＜０．２０％、Ｃｕ＜０．２０％、Ｖ：０．０７０〜０．１００％、Ｃａ＞０．００１５％、Ｐ＜０．０１０％、Ｓ＜０．００３％であり、残部が鉄である。該文献は該油井管の製造方法を提供した。該方法は、１）配料精錬、２）連続鋳造・連続圧延、および３）管加工を含んだ。該文献の鋼種の強度は１１００Ｍｐａであるが、横向衝撃靱性は９０Ｊだけであり、靱性の指標はより低いである。   Chinese Patent Document CN101586450A (publication date: August 27, 2008, name: “oil well pipe having high strength and high toughness and manufacturing method thereof”) relates to a steel grade for oil well pipe. The chemical element components (wt%) of the steel types are: C: 0.22 to 0.4%, Si: 0.17 to 0.35%, Mn: 0.45 to 0.60%, Cr: 0.95 -1.10%, Mo: 0.70-0.80%, Al: 0.015-0.040%, Ni <0.20%, Cu <0.20%, V: 0.070-0. 100%, Ca> 0.0015%, P <0.010%, S <0.003%, and the balance is iron. The document provided a method for manufacturing the oil well pipe. The method included 1) distribution refining, 2) continuous casting and continuous rolling, and 3) pipe processing. The strength of the steel grade in this document is 1100 Mpa, but the lateral impact toughness is only 90 J, and the toughness index is lower.

中国特許文献ＣＮ１０１２５０６７１Ａ （公開日：２００９年１１月２５日、名称：「高強度と高靱性のある油井管およびその製造方法」）は油井管用の鋼種に関する。該鋼種の化学元素成分（ｗｔ％）は、Ｃ：０．１６〜０．２８、Ｓｉ：≦０．５、Ｍｎ：０．３〜１．１０、Ｃｒ：０．３〜１．１０、Ｍｏ：０．６０〜０．９５、Ａｌ：０．０１５〜０．０６０、その内、酸可溶Ａｌｓ／Ａｌ≧０．８、Ｎｉ：＜０．６０、 Ｃｕ：０．０５〜０．２５、Ｖ：０．０６〜０．２０、Ｃａ＞０．００１５、Ｎｂ：≦０．０５、Ｔｉ：≦０．０５、Ｐ＜０．０１０、Ｓ＜０．００２、Ｏ：＜０．００２４、Ｈ：＜０．０００２、Ｎ：＜０．００８、Ｂ：０．０〜０．００５であり、残部が鉄である。該文献の油井管の横向衝撃靱性は８０Ｊだけであり、靱性の指標もより低いである。   Chinese Patent Document CN101250671A (Release Date: November 25, 2009, Name: “Oil Well Pipe with High Strength and Toughness and Method for Producing the Same”) relates to a steel grade for oil well pipe. The chemical element components (wt%) of the steel types are: C: 0.16-0.28, Si: ≦ 0.5, Mn: 0.3-1.10, Cr: 0.3-1.10, Mo : 0.60 to 0.95, Al: 0.015 to 0.060, of which acid-soluble Als / Al ≧ 0.8, Ni: <0.60, Cu: 0.05 to 0.25, V: 0.06-0.20, Ca> 0.0015, Nb: ≦ 0.05, Ti: ≦ 0.05, P <0.010, S <0.002, O: <0.0024, H : <0.0002, N: <0.008, B: 0.0 to 0.005, and the balance is iron. The oil well pipe of the literature has a lateral impact toughness of only 80 J and a lower index of toughness.

日本特許文献ＪＰ平１１−１３１１８９Ａ（公開日：１９９９年５月１８日、名称：「１種鋼管の製造方法」）は１種鋼管の製造方法を公開した。該製造方法は、７５０〜４００℃温度範囲で加熱した後に、２０％或いは６０％以上の変形量の範囲で圧延を施して、降伏強度９５０Ｍｐａ以上であり、良好な靱性を有する鋼管製品を獲得したことを提出した。だが、該方法は加熱温度が低いため、圧延の難度が大きいである。尚、圧延温度が低くなると、マルテンサイト組織が生成しやすい。該微細組織は油井管製品に許されない微細組織である。   Japanese Patent Document JP Hei 11-131189A (Release Date: May 18, 1999, Name: “Method for Producing Type 1 Steel Pipe”) disclosed a method for producing Type 1 steel pipe. In this manufacturing method, after heating in a temperature range of 750 to 400 ° C., rolling was performed in a deformation amount range of 20% or 60% or more, and a steel pipe product having a yield strength of 950 Mpa or more and good toughness was obtained. Submitted that. However, this method has a high degree of difficulty in rolling because of the low heating temperature. When the rolling temperature is lowered, a martensite structure is likely to be generated. The fine structure is a fine structure that is not allowed for oil well pipe products.

本発明の目的は、超高強度・超高靱性油井管を提供するものである。該油井管は、超高強度と超高靱性を有し、その強度が１５０ｋｓｉ鋼級以上になると共に、その０°横向シャルピー衝撃功が１５０ｋｓｉ鋼級の降伏強度の１０％以上であるため、深井、超深井の油ガス田が油井管へ提出した強度と靱性との要求を満足できる。   An object of the present invention is to provide an ultra-high strength and ultra-high toughness oil well pipe. The oil well pipe has ultra-high strength and ultra-high toughness, and its strength is 150 ksi steel grade or higher, and its 0 ° transverse Charpy impact is 10% or more of the yield strength of 150 ksi steel grade. It can satisfy the requirements of strength and toughness submitted to the oil well pipe by the oil and gas field of Ultra Fukai.

前記目的を実現するために、本発明は、下のような超高強度・超高靱性油井管を提出した。   In order to achieve the above object, the present invention has submitted the following ultra-high strength and ultra-tough oil well pipe.

超高強度・超高靱性油井管は、化学元素の質量百分率表示で、
Ｃ：０．１２〜０．１８％；
Ｓｉ：０．１〜０．４％；
Ｍｎ：１．１〜１．６％；
Ｃｒ：０．１〜０．４％；
Ｍｏ：０．２〜０．５％；
Ｎｂ：０．０２〜０．０４％；
Ｔｉ：０．０２〜０．０５％；
Ｂ：０．００１５〜０．００５％；
Ａｌ：０．０１〜０．０５％；
Ｃａ：０．０００５〜０．００５％；
Ｎ≦０．００８％を含有し、
且つ０＜（Ｔｉ−３．４Ｎ）≦０．０２％、Ｔｉ／Ｂ≧１０を満足し、
残部がＦｅおよび他の不可避不純物である。 Ultra-high strength and ultra-tough oil well pipes are expressed in mass percentages of chemical elements.
C: 0.12-0.18%;
Si: 0.1 to 0.4%;
Mn: 1.1-1.6%;
Cr: 0.1 to 0.4%;
Mo: 0.2-0.5%;
Nb: 0.02-0.04%;
Ti: 0.02 to 0.05%;
B: 0.0015 to 0.005%;
Al: 0.01 to 0.05%;
Ca: 0.0005 to 0.005%;
N ≦ 0.008%,
And 0 <(Ti-3.4N) ≦ 0.02%, Ti / B ≧ 10 is satisfied,
The balance is Fe and other inevitable impurities.

本技術方案中の不可避不純物は主にＰとＳ元素であり、Ｐ≦０．０１５％、Ｓ≦０．００３％であるようにコントロールされる。   Inevitable impurities in this technical plan are mainly P and S elements, and are controlled so that P ≦ 0.015% and S ≦ 0.003%.

本発明の前記超高強度・超高靱性油井管中の各化学元素についての設計原理は下のようである。   The design principle for each chemical element in the ultra-high strength / ultra-tough oil well pipe of the present invention is as follows.

Ｃ：Ｃは炭化物を形成する元素であり、鋼の強度を向上できる。Ｃの含有量が０．１２ｗｔ％よりも低いであると、鋼の焼入性が低下され、鋼の靱性が低下される。Ｃの含有量が０．１８ｗｔ％よりも高いであると、鋼の偏析を顕著的に劣化させ、鋼の靱性の低下をも引き起こす。油井管の高強度と高靱性への要求を達成するために、本発明の技術方案において、Ｃ元素の含有量を０．１２〜０．１８ｗｔ％にすることが必要である。   C: C is an element that forms carbides, and can improve the strength of steel. When the C content is lower than 0.12 wt%, the hardenability of the steel is lowered and the toughness of the steel is lowered. When the content of C is higher than 0.18 wt%, the segregation of the steel is remarkably deteriorated and the toughness of the steel is also lowered. In order to achieve the demand for high strength and high toughness of the oil country tubular goods, it is necessary to make the content of C element 0.12 to 0.18 wt% in the technical solution of the present invention.

Ｓｉ：Ｓｉはフェライトに固溶し、鋼の降伏強度を向上できる。しかし、Ｓｉ元素の添加量が高すぎることは望ましくない。Ｓｉ元素が高すぎると、鋼の加工性と靱性を劣化させる。Ｓｉ元素が０．１ｗｔ％未満であると、油井管が酸化されやすい。そうすると、Ｓｉの含有量を０．１０〜０．４０ｗｔ％にすべきである。   Si: Si dissolves in ferrite and can improve the yield strength of steel. However, it is not desirable that the amount of Si element added is too high. If the Si element is too high, the workability and toughness of the steel deteriorate. If the Si element is less than 0.1 wt%, the oil well pipe is likely to be oxidized. Then, the Si content should be 0.10 to 0.40 wt%.

Ｍｎ：Ｍｎはオーステナイトの形成元素であり、鋼の焼入性を向上できる。 本発明の前記超高強度・超高靱性油井管の鋼種体系において、Ｍｎ含有量が１．１ｗｔ％未満であると、鋼の焼入性が顕著的に低下され、鋼のマルテンサイトの比率を減少して鋼の靱性を低下する。Ｍｎの含有量が１．６ｗｔ％を超えると、鋼中の組織偏析が顕著的に増加され、熱圧延組織の均一性と衝撃性能へ影響が出る。該原因に基づいて、本発明の技術方案においてＭｎ含有量を１．１０〜１．６０ｗｔ％にした。   Mn: Mn is an austenite forming element and can improve the hardenability of steel. In the steel type system of the ultra-high strength and ultra-tough oil well pipe of the present invention, if the Mn content is less than 1.1 wt%, the hardenability of the steel is significantly reduced, and the martensite ratio of the steel is reduced. Decrease and reduce the toughness of the steel. When the Mn content exceeds 1.6 wt%, the structure segregation in the steel is remarkably increased, which affects the uniformity of the hot rolled structure and the impact performance. Based on this cause, the Mn content was 1.10 to 1.60 wt% in the technical solution of the present invention.

Ｃｒ：Ｃｒは鋼の焼入性を強烈的に向上する元素であり、強炭化物を形成する元素である。焼き戻しの時に析出された強炭化物が鋼の強度を向上できる。だが、Ｃｒ含有量が０．４ｗｔ％を超えると、晶界に粗大なＭ２３Ｃ６炭化物は析出されやすいため、鋼の靱性を低下する。Ｃｒ含有量が０．１ｗｔ％未満であると、鋼の焼入性を向上しにくいため、添加効果が明確ではない。本発明の前記の超高強度・超高靱性油井管では、Ｃｒ含有量を０．１〜０．４ｗｔ％に設計した。 Cr: Cr is an element that strongly improves the hardenability of steel and is an element that forms strong carbides. Strong carbides precipitated during tempering can improve the strength of the steel. However, if the Cr content exceeds 0.4 wt%, coarse M 23 C 6 carbide is likely to be precipitated at the crystal boundaries, so that the toughness of the steel is lowered. If the Cr content is less than 0.1 wt%, it is difficult to improve the hardenability of the steel, so the effect of addition is not clear. In the ultra-high strength / ultra-tough oil well pipe of the present invention, the Cr content was designed to be 0.1 to 0.4 wt%.

Ｍｏ：Ｍｏは、主に炭化物と固溶強化の形式によって鋼の強度と焼戻し安定性を向上する。本発明の技術方案では、Ｃ含有量が低いため、Ｍｏ含有量が０．５ｗｔ％以上を越えると、ＭｏはＣとより多い炭化物析出相を形成しにくいため、添加合金の浪費を引き起こす。Ｍｏ含有量が０．２ｗｔ％未満であると、油井管の強度は高強度の要求に満足できない。該原因に基づいて本発明では、Ｍｏ含有量を０．２〜０．５ｗｔ％にした。   Mo: Mo improves the strength and tempering stability of steel mainly by the form of carbide and solid solution strengthening. In the technical solution of the present invention, since the C content is low, when the Mo content exceeds 0.5 wt% or more, Mo hardly forms a carbide precipitation phase with C, which causes waste of the added alloy. If the Mo content is less than 0.2 wt%, the strength of the oil well pipe cannot satisfy the requirement for high strength. Based on the cause, in the present invention, the Mo content is set to 0.2 to 0.5 wt%.

Ｎｂ：Ｎｂは、鋼中の細晶と析出強化の元素であり、Ｃ含有量の低減による強度の低下を補う。Ｎｂ含有量が０．０２ｗｔ％未満であると、添加作用は明確ではない。Ｎｂ含有量が０．０４ｗｔ％を超えると、粗大なＮｂ（ＣＮ）を形成しやすいため、鋼の靱性を低下する。そうすると、本発明の技術方案では、Ｎｂ含有量を０．０２〜０．０４ｗｔ％にコントロールする。   Nb: Nb is an element of fine crystals and precipitation strengthening in steel, and compensates for a decrease in strength due to a reduction in the C content. When the Nb content is less than 0.02 wt%, the addition action is not clear. When the Nb content exceeds 0.04 wt%, coarse Nb (CN) is easily formed, and thus the toughness of the steel is lowered. Then, in the technical solution of the present invention, the Nb content is controlled to 0.02 to 0.04 wt%.

Ｔｉ：Ｔｉは、強炭窒化物を形成する元素であり、鋼中のオーステナイト晶粒を顕著的に細化でき、Ｃ含有量の低減による強度の低下を補う。Ｔｉ含有量＞０．０５ｗｔ％であると、粗大なＴｉＮを形成しやすいため、材料の靱性を低下する恐れがある。Ｔｉ含有量＜０．０２ｗｔ％であると、ＴｉがＮと十分に反応してＴｉＮを形成できないため、鋼中のＢがＮと反応してＢＮの脆性相を形成する恐れがあり、材料の靱性を低下する。本発明の超高強度・超高靱性油井管では、Ｔｉ含有量を０．０２〜０．０５ｗｔ％にコントロールする必要がある。   Ti: Ti is an element that forms strong carbonitrides, can remarkably reduce austenite grains in steel, and compensates for a decrease in strength due to a reduction in C content. If the Ti content is> 0.05 wt%, coarse TiN is likely to be formed, which may reduce the toughness of the material. If the Ti content is less than 0.02 wt%, Ti cannot sufficiently react with N to form TiN, so that B in the steel may react with N to form a brittle phase of BN. Reduce toughness. In the ultra-high strength / ultra-tough oil well pipe of the present invention, it is necessary to control the Ti content to 0.02 to 0.05 wt%.

Ｂ：Ｂは鋼の焼入性を顕著的に向上する元素である。Ｃ含有量が低いである鋼種において、Ｂ元素はＣ含有量の低減による焼入性の劣化問題を解決できる。Ｂ含有量が０．００１５ｗｔ％未満であると、鋼の焼入性を向上する作用は顕著ではない。Ｂ含有量が０．００５ｗｔ％を超えると、ＢＮ脆性相を形成しやすいため、鋼の靱性を低下する。そうすると、本発明の技術方案では、Ｂ含有量を０．００１５〜０．００５ｗｔ％に設定する。   B: B is an element that significantly improves the hardenability of steel. In steel types with low C content, B element can solve the problem of deterioration of hardenability due to reduction of C content. When the B content is less than 0.0015 wt%, the effect of improving the hardenability of the steel is not remarkable. If the B content exceeds 0.005 wt%, a BN brittle phase is likely to be formed, so that the toughness of the steel is reduced. Then, in the technical solution of the present invention, the B content is set to 0.0015 to 0.005 wt%.

Ａｌ：Ａｌ元素は良好な脱酸素固窒元素であり、晶粒を細化できる。重量百分率でその含有量を０．０１〜０．０５％にすることが好ましい。   Al: Al element is a good deoxygenated solid nitrogen element, and can refine crystal grains. The content is preferably 0.01 to 0.05% by weight percentage.

Ｃａ：Ｃａは鋼液を浄化する元素であり、ＭｎＳ球化を促進でき、鋼材の衝撃靱性を向上できる。だが、Ｃａ含有量が高すぎると、鋼中に粗大な非金属異物を形成しやすい。そうすると、本発明の技術方案では、Ｃａ含有量を０．０００５〜０．００５ｗｔ％にコントロールする。   Ca: Ca is an element that purifies the steel liquid, can promote MnS spheroidization, and can improve the impact toughness of the steel material. However, if the Ca content is too high, coarse non-metallic foreign matter tends to be formed in the steel. Then, in the technical solution of the present invention, the Ca content is controlled to 0.0005 to 0.005 wt%.

Ｎ：本技術方案では、できるだけＮ元素の含有量を少ない範囲にすることが好ましい。
同時に、ＢとＮがＢＮ脆性相を形成することによって鋼材の靱性指標が低下してしまうことを回避して、ＴｉとＮとが十分に結合することを保証するために、Ｔｉ、ＢおよびＮは下式をさらに満足する必要である。 N: In this technical scheme, it is preferable to make the content of N element as small as possible.
At the same time, in order to avoid that the toughness index of the steel material is lowered due to B and N forming a BN brittle phase, and to ensure that Ti and N are sufficiently bonded, Ti, B and N Needs to satisfy the following formula.

０＜（Ｔｉ−３．４Ｎ）≦０．０２％；且つＴｉ／Ｂ≧１０。
また、本発明の前記超高強度・超高靱性油井管はＶ元素をさらに含有する。Ｖ元素範囲は０＜Ｖ≦０．１ｗｔ％である。 0 <(Ti-3.4N) ≦ 0.02%; and Ti / B ≧ 10.
Moreover, the ultra-high strength / ultra-tough oil well pipe of the present invention further contains a V element. The V element range is 0 <V ≦ 0.1 wt%.

Ｖ元素は鋼中の晶粒を細化できる。該元素と形成された炭化物は鋼の強度を大幅に向上できる。だが、Ｖ元素の添加量が一定程度になると、その増強効果は明確ではない。そうすると、本発明の技術方案に対しては、Ｖ元素を添加すれば、その添加量は≦０．１０ｗｔ％である。   V element can make crystal grains in steel finer. The carbide formed with the element can greatly improve the strength of the steel. However, the enhancement effect is not clear when the amount of V element added becomes constant. If it does so, with respect to the technical solution of this invention, if V element is added, the addition amount will be <= 0.10 wt%.

さらに、本発明の前記超高強度・超高靱性油井管中のミクロ組織は焼戻ソルバイトである。   Furthermore, the microstructure in the ultra-high strength and ultra-tough oil well pipe of the present invention is tempered sorbite.

油井管が良好な強靱性の配合を獲得するために、鋼中のミクロ組織は焼戻ソルバイトである。該種ミクロ組織は最高の強靱性を有する。該種ミクロ組織はマルテンサイト組織から転化される。鋼材料を焼入れた後に形成されたマルテンサイト組織が多いほど、その後に得られた焼戻ソルバイト組織も多くなれる。   The microstructure in the steel is tempered sorbite so that the wellbore acquires a good toughness formulation. The seed microstructure has the highest toughness. The seed microstructure is converted from a martensite structure. The more martensite structures formed after quenching the steel material, the more tempered sorbite structures obtained thereafter.

鋼管管生地の凝結過程中で枝晶が偏析されて、圧延後の管体に大量な偏析帯が存在されている。該偏析帯にＣ、Ｍｎ、ＣｒおよびＭｏなどの合金元素が富集され、局部に合金成分の分布が不均一であるため、偏析帯に形成された炭化物は多い且つ粗大である。同時に、偏析帯にある鋼の硬度と強度がより高いため、その靱性がより低い。油井管の成分偏析を低下するために、Ｃ、Ｍｎ、ＣｒおよびＭｏなどの合金元素を減少する手段を使用してもよい。一方、油井管が良好な強靱性の配合を獲得するために、鋼材料のミクロ組織は焼戻ソルバイトである。該種ミクロ組織は最高の強靱性を有する。該種ミクロ組織はマルテンサイト組織から転化される。鋼材料を焼入れた後に形成されたマルテンサイト組織が多いほど、その後に得られた焼戻ソルバイト組織も多くなれる。そうすると、焼入性を向上して、より多いマルテンサイト組織を獲得するのは材料の強靱性を保証するキーポイントである。Ｃ、Ｍｎ、ＣｒおよびＭｏなどの合金元素を減少することによって低偏析組織を獲得し、鋼の靱性を向上する措置の採用は、鋼の焼入性を低下するはずであり、鋼の強靱性をさらに低下する。該内容に基づいて、高強度・高靱性鋼種は鋼の偏析と焼入性を合理的にバランスする必要である。本発明の技術方案では、低炭と低合金の成分体系を採用して低偏析のミクロ組織を獲得すると共に、ＢとＴｉをさらに加入して焼入性を向上して鋼の靱性を増加して均一な焼戻ソルバイトを獲得することを保証できる。   Branch crystals are segregated during the setting process of the steel tube dough, and a large amount of segregation zones exist in the rolled tube. Since the segregation zone is rich in alloy elements such as C, Mn, Cr and Mo and the distribution of alloy components is uneven in the local area, the carbides formed in the segregation zone are many and coarse. At the same time, the hardness and strength of the steel in the segregation zone is higher, so its toughness is lower. In order to reduce the component segregation of the oil country tubular goods, means for reducing alloy elements such as C, Mn, Cr and Mo may be used. On the other hand, the microstructure of the steel material is tempered sorbite in order for the oil well pipe to obtain a good toughness blend. The seed microstructure has the highest toughness. The seed microstructure is converted from a martensite structure. The more martensite structures formed after quenching the steel material, the more tempered sorbite structures obtained thereafter. In this case, improving the hardenability and obtaining a larger martensite structure is a key point for guaranteeing the toughness of the material. Adopting measures to acquire low segregation structure by reducing alloy elements such as C, Mn, Cr and Mo and improve the toughness of steel should reduce the hardenability of steel, and toughness of steel Is further reduced. Based on this content, high strength and high toughness steel grades need to reasonably balance steel segregation and hardenability. The technical solution of the present invention adopts a low-carbon and low-alloy component system to obtain a low segregation microstructure, and further adds B and Ti to improve hardenability and increase steel toughness. And ensure uniform tempering sorbite.

相応的に、本発明は超高強度・超高靱性油井管の製造方法をさらに提供した。該方法は、精錬工程、連続鋳造工程、穿孔工程、圧延工程、サイジング工程、熱処理工程を含む。   Correspondingly, the present invention further provides a method for producing an ultra-high strength and ultra-tough oil well pipe. The method includes a refining process, a continuous casting process, a piercing process, a rolling process, a sizing process, and a heat treatment process.

さらに、本発明の前記超高強度・超高靱性油井管の製造方法の前記連続鋳造工程において、溶鋼の過熱度を３０℃未満にして、連続鋳造の引き上げ速度を１．８〜２．２ｍ／ｍｉｎである。   Furthermore, in the continuous casting step of the production method of the ultra-high strength / ultra-tough oil well pipe of the present invention, the superheat degree of the molten steel is made less than 30 ° C., and the pulling speed of continuous casting is set to 1.8 to 2.2 m / min.

連続鋳造の引き上げ速度を１．８〜２．２ｍ／ｍｉｎにコントロールするのは鋼中の成分偏析を低下するためである。   The reason for controlling the pulling speed of continuous casting to 1.8 to 2.2 m / min is to reduce component segregation in the steel.

好ましくは、本発明の前記超高強度・超高靱性油井管の製造方法において、前記穿孔工程では、連続鋳造工程で得られた丸ビレットを１２００〜１２４０℃の炉内で均一的に加熱して、穿孔温度を１１８０〜１２４０℃にする。   Preferably, in the method for producing an ultra-high strength / ultra-tough oil country tubular good of the present invention, in the drilling step, the round billet obtained in the continuous casting step is uniformly heated in a furnace at 1200 to 1240 ° C. The drilling temperature is 1180-1240 ° C.

より好ましくは、本発明の前記超高強度・超高靱性油井管の製造方法において、前記圧延工程では、最終圧延温度を９００〜９５０℃にする。   More preferably, in the manufacturing method of the ultra-high strength / ultra-tough oil well pipe of the present invention, the final rolling temperature is set to 900 to 950 ° C. in the rolling step.

より好ましくは、本発明の前記超高強度・超高靱性油井管の製造方法において、前記サイジング工程では、サイジング温度が８５０〜９００℃である。   More preferably, in the method for manufacturing an ultra-high strength / ultra-tough oil country tubular good according to the present invention, the sizing temperature is 850 to 900 ° C. in the sizing step.

より好ましくは、本発明の前記超高強度・超高靱性油井管の製造方法において、前記熱処理工程では、オーステナイト化温度を９００〜９３０℃にして、３０〜６０ｍｉｎ保温後に焼入れして、４５０〜５５０℃で焼き戻し、保温時間を５０〜８０ｍｉｎにして、最後に４００〜５５０℃で熱サイジングを行う。   More preferably, in the method for producing an ultra-high strength / ultra-tough oil country tubular good according to the present invention, in the heat treatment step, the austenitizing temperature is set to 900 to 930 ° C., and after quenching for 30 to 60 minutes, 450 to 550 is performed. Tempering is performed at a temperature of 50 to 80 minutes, and finally heat sizing is performed at a temperature of 400 to 550 ° C.

より低い焼戻温度を使用して、鋼材がより高い温度を獲得できるようにしたため、強靱性を向上したと共に、合金の添加コストをも大幅に減少した。   A lower tempering temperature was used to allow the steel to gain higher temperatures, thus improving toughness and significantly reducing the cost of alloy addition.

本発明の前記超高強度・超高靱性油井管は、１５０ｋｓｉ以上鋼級であり、超高強度と超高靱性を有する油井管の製造に用いられる。   The ultra-high strength and ultra-high toughness oil well pipe of the present invention is a steel grade of 150 ksi or more, and is used for manufacturing an oil well pipe having ultra-high strength and ultra-high toughness.

本発明の前記超高強度・超高靱性油井管で得られた１５０ｋｓｉ鋼級油井管は、その降伏強度が１０３４〜１２４１ＭＰａであり、引張強度≧１１０３ＭＰａであり、伸び率が２０％〜３０％であり、０°横向シャルピー衝撃功が１５０ｋｓｉ鋼級の降伏強度の１０％以上（≧１２０Ｊ）であり、靱脆遷移温度が−７０℃以下である。   The 150 ksi steel grade oil well pipe obtained from the ultra-high strength / high toughness oil well pipe of the present invention has a yield strength of 1034 to 1241 MPa, a tensile strength ≧ 1103 MPa, and an elongation of 20% to 30%. Yes, the 0 ° transverse Charpy impact is 10% or more (≧ 120 J) of the yield strength of the 150 ksi steel grade, and the tough / brittle transition temperature is −70 ° C. or less.

本発明の前記超高強度・超高靱性油井管で得られた１５５ｋｓｉ鋼級油井管は、その降伏強度が１０６９〜１２７６ＭＰａであり、引張強度≧１１３８ＭＰａであり、伸び率が２０％〜２５％であり、０°横向シャルピー衝撃功が１５５ｋｓｉ鋼級の降伏強度の１０％以上（≧１２０Ｊ）であり、靱脆遷移温度が−６０℃以下である。   The 155 ksi steel grade oil well pipe obtained with the ultra high strength / high toughness oil well pipe of the present invention has a yield strength of 1069 to 1276 MPa, a tensile strength ≧ 1138 MPa, and an elongation of 20% to 25%. Yes, the 0 ° transverse Charpy impact is 10% or more (≧ 120 J) of the yield strength of the 155 ksi steel grade, and the tough / brittle transition temperature is −60 ° C. or less.

本発明の前記超高強度・超高靱性油井管は、Ｂを添加して鋼の焼入性を増加したため、普通鋼種に添加されたＣｒとＭｏなどの合金元素を代替したことによって油井管の合金添加コストを低下して、強度が高く、且つ靱性がよい。   The ultra-high strength and ultra-tough oil well pipe of the present invention increases the hardenability of steel by adding B. Therefore, by replacing alloy elements such as Cr and Mo added to ordinary steel grade, The alloy addition cost is reduced, the strength is high, and the toughness is good.

本発明の前記超高強度・超高靱性油井管の製造方法は、熱処理工程に対する制御で鋼材がより高い強度とより良い靱性を獲得できるようになった。過程操作が簡単になり、大規模の生産製造を実現しやすいため、良好な経済利益を有する。   The manufacturing method of the ultra-high strength / ultra-tough oil well pipe of the present invention has made it possible to obtain higher strength and better toughness of the steel material by controlling the heat treatment process. The process operation is simple and it is easy to realize large-scale production manufacturing, so it has good economic benefits.

実施例Ａ５中の超高強度・超高靱性油井管の金属組織を示した。The metal structure of the ultra-high strength / ultra-tough oil well pipe in Example A5 is shown. 実施例Ａ５中の超高強度・超高靱性油井管の析出相形態を示した。The precipitation phase morphology of the ultra-high strength and ultra-tough oil well pipe in Example A5 was shown. 比較例Ｂ１中の油井管の金属組織を示した。The metal structure of the oil well pipe in Comparative Example B1 is shown. 比較例Ｂ２中の油井管の析出相形態を示した。The precipitation phase form of the oil well pipe in Comparative Example B2 was shown. 比較例Ｂ３中の油井管の析出相形態を示した。The precipitation phase form of the oil well pipe in Comparative Example B3 was shown.

以下、具体的な実施例に基づいて、本発明の前記超高強度・超高靱性油井管およびその製造方法をさらに説明する。だが、具体的な実施例および関係な説明は本発明の技術方案の不当限定になれない。   Hereinafter, the ultra-high strength / ultra-tough oil well pipe of the present invention and the manufacturing method thereof will be further described based on specific examples. However, specific embodiments and related descriptions are not unduly limited to the technical solutions of the present invention.

実施例Ａ１−Ａ５と比較例Ｂ１−Ｂ４
下の工程の通りに、実施例Ａ１−Ａ５と比較例Ｂ１−Ｂ４の油井管を製造した。 Example A1-A5 and Comparative Examples B1-B4
The oil well pipe of Example A1-A5 and Comparative Example B1-B4 was manufactured as the following process.

１）精錬：実施例Ａ１−Ａ５と比較例Ｂ１−Ｂ４中の各化学元素の質量百分率の配合を表１のようにコントロールした。   1) Refining: The composition of mass percentage of each chemical element in Examples A1-A5 and Comparative Examples B1-B4 was controlled as shown in Table 1.

２）連続鋳造：連続鋳造して管生地を形成して、溶鋼の過熱度を３０℃未満にして、連続鋳造の引き上げ速度を１．８〜２．２ｍ／ｍｉｎにした。   2) Continuous casting: A tube material was formed by continuous casting, the superheat degree of the molten steel was set to less than 30 ° C, and the pulling speed of continuous casting was set to 1.8 to 2.2 m / min.

３）穿孔：連続鋳造工程で得られた丸ビレットを１２００〜１２４０℃の環形炉内で均一的に加熱して、穿孔温度を１１８０〜１２４０℃にした。   3) Drilling: The round billet obtained in the continuous casting process was uniformly heated in a ring furnace at 1200 to 1240 ° C., so that the drilling temperature was 1180 to 1240 ° C.

４）圧延：最終圧延温度を９００〜９５０℃にした。
５）サイジング：サイジング温度を８５０〜９００℃にした。 4) Rolling: The final rolling temperature was 900 to 950 ° C.
5) Sizing: The sizing temperature was 850 to 900 ° C.

６）熱処理：オーステナイト化温度を９００〜９３０℃にして、３０〜６０ｍｉｎ保温後に焼入れして、４５０〜５５０℃で焼戻して、保温時間を５０〜８０ｍｉｎにして、最後に４００〜５５０℃で熱サイジングを行った。   6) Heat treatment: Austenitizing temperature is 900 to 930 ° C, quenching is performed after incubation for 30 to 60 minutes, tempering is performed at 450 to 550 ° C, incubation time is set to 50 to 80 minutes, and finally heat sizing is performed at 400 to 550 ° C. Went.

表１は、実施例Ａ１−Ａ５と比較例Ｂ１−Ｂ４中の各化学元素の質量百分率の配合を挙げた。   Table 1 listed the mass percentage formulations for each chemical element in Example A1-A5 and Comparative Examples B1-B4.

Figure 0006456986
Figure 0006456986

表２は、実施例Ａ１−Ａ５と比較例Ｂ１−Ｂ４の各工程のパラメーターを挙げた。   Table 2 lists the parameters of each step of Example A1-A5 and Comparative Example B1-B4.

Figure 0006456986
Figure 0006456986

表３は、実施例Ａ１−Ａ５と比較例Ｂ１−Ｂ４中の油井管の力学性能を示した。   Table 3 shows the mechanical performance of the oil well pipes in Examples A1-A5 and Comparative Examples B1-B4.

Figure 0006456986
Figure 0006456986

表３から分かるように、前記各実施例Ａ１−Ａ５中の油井管のいずれも、その降伏強度が≧１０５０Ｍｐａ（１５０ｋｓｉ鋼級以上の強度を達成した）、引張強度が≧１０９０Ｍｐａ、０°横向衝撃功が≧１２８Ｊ、伸び率が≧２３％、靱脆遷移温度が≦−６０℃だった。つまり、実施例Ａ１−Ａ５中の油井管のいずれも超高強度と超高靱性を有したため、深井、超深井を採掘する油井管を製造するのに適合である。反面、比較例Ｂ１中のＭｎとＣｒが本発明の技術方案に限定された範囲を超えたことと、比較例Ｂ２中でＢとＴｉを添加しなかったことと、比較例Ｂ３中のＣ、Ｍｎ、ＣｒおよびＭｏが本発明の技術方案に限定された範囲を超えたことと、比較例Ｂ４中のＴｉとＮの元素が０＜（Ｔｉ−３．４Ｎ）≦０．０２％、 Ｔｉ／Ｂ≧１０の条件を満足しなかったことがあったため、比較例Ｂ１−Ｂ４中の油井管の少なくとも１項の力学性能は高強度と高靱性の油井管の標準を達成しなかった。   As can be seen from Table 3, all of the oil well pipes in Examples A1-A5 had a yield strength of ≧ 1050 Mpa (achieved a strength of 150 ksi grade or higher), a tensile strength of ≧ 1090 Mpa, and 0 ° lateral impact. Gong was ≧ 128 J, the elongation was ≧ 23%, and the tough / brittle transition temperature was ≦ −60 ° C. That is, since all of the oil well pipes in Examples A1-A5 had ultra high strength and ultra high toughness, they are suitable for manufacturing oil well pipes for mining Fukai and ultra deep wells. On the other hand, Mn and Cr in Comparative Example B1 exceeded the range limited to the technical solution of the present invention, B and Ti were not added in Comparative Example B2, and C in Comparative Example B3, Mn, Cr and Mo exceeded the range limited to the technical solution of the present invention, and Ti and N elements in Comparative Example B4 were 0 <(Ti-3.4N) ≦ 0.02%, Ti / Since the condition of B ≧ 10 was sometimes not satisfied, the mechanical performance of at least one term of the oil well pipe in Comparative Examples B1-B4 did not achieve the standard of the high strength and high toughness well pipe.

図１は、実施例Ａ５中の超高強度・超高靱性油井管の金属組織を示し、図２は、実施例Ａ５中の超高強度・超高靱性油井管の析出相形態を示した。   FIG. 1 shows the metal structure of the ultra-high strength / ultra-tough oil well pipe in Example A5, and FIG. 2 shows the precipitated phase morphology of the ultra-high strength / ultra-tough oil well pipe in Example A5.

図１が示した通りに、実施例Ａ５中の油井管の金属組織に成分偏析によって形成された帯状組織が発見されていない。図２が示した通りに、実施例Ａ５中の油井管の析出相の炭化物は細小であり、その分布が均一である。そうすると、実施例Ａ５中の超高強度・超高靱性油井管はその強度が１５０ｋｓｉ鋼級以上になり、その０°横向衝撃靱性が１２０Ｊ以上になった。   As shown in FIG. 1, no band-like structure formed by component segregation in the metal structure of the oil well pipe in Example A5 has been found. As shown in FIG. 2, the carbide of the precipitated phase of the oil well pipe in Example A5 is fine and the distribution thereof is uniform. Then, the ultra-high strength / ultra-tough oil well pipe in Example A5 had a strength of 150 ksi steel grade or higher, and its 0 ° lateral impact toughness was 120 J or higher.

図３は、比較例Ｂ１中の油井管の金属組織を示した。
比較例Ｂ１中のＣとＭｎとの含有量がより低いため、鋼の焼入性が低くなってしまった。図３が示した通りに、比較例Ｂ１の金属組織により多いフェライト組織が存在されているため、熱処理後の油井管の強度が不足であり、０°横向衝撃功も高くない。そうすると、超高強度・超高靱性油井管に加工することに適応できない。 FIG. 3 shows the metal structure of the oil well pipe in Comparative Example B1.
Since the contents of C and Mn in Comparative Example B1 were lower, the hardenability of the steel was lowered. As shown in FIG. 3, since more ferrite structure exists in the metal structure of Comparative Example B1, the strength of the oil well pipe after heat treatment is insufficient, and the 0 ° lateral impact effect is not high. If it does so, it cannot adapt to processing into a super high strength and super high toughness oil well pipe.

図４は、比較例Ｂ２中の油井管の析出相形態を示し、図５は、比較例Ｂ３中の油井管の析出相形態を示した。   FIG. 4 shows the precipitated phase morphology of the oil well pipe in Comparative Example B2, and FIG. 5 shows the precipitated phase morphology of the oil well pipe in Comparative Example B3.

管生地の凝結過程中で枝晶偏析によって圧延後の管体に大量な偏析帯が存在されているため、図４のように、比較例Ｂ２の偏析帯にＣ、Ｍｎ、ＣｒおよびＭｏなどの合金元素が富集され、局部に合金成分の分布が不均一であるため、偏析帯に形成された炭化物は多く且つ粗大である。   Since a large amount of segregation zones exist in the tube after rolling due to branching segregation during the tube dough condensation process, as shown in FIG. 4, the segregation zones of Comparative Example B2, such as C, Mn, Cr, and Mo Since the alloy elements are concentrated and the distribution of the alloy components is uneven in the local area, the carbides formed in the segregation zone are many and coarse.

図５が示した通りに、比較例Ｂ３中のＣ、Ｃｒ、Ｍｏなどの合金元素は本発明の技術方案に限定された範囲を超えたため、熱処理後の油井管の偏析は酷くなった。偏析が酷くなった場合、油井管の靱性が不足になり、鋼の靱性指標が低下された。   As shown in FIG. 5, since the alloy elements such as C, Cr, and Mo in Comparative Example B3 exceeded the range limited to the technical solution of the present invention, segregation of the oil well pipe after the heat treatment became severe. When segregation became severe, the toughness of the oil well pipe became insufficient and the toughness index of steel was lowered.

注意すべきことは、前記挙げられたものが本発明の具体的な実施例だけである。本発明は前記の実施例に限定されなくて、多い類似な変化例がある。当分野の当業者が本発明の公開内容から直接的に得られた変化例、或いは連想できた変化例も本発明の保護範囲に属される。   It should be noted that the above are only specific embodiments of the present invention. The present invention is not limited to the embodiments described above, and there are many similar variations. Variations obtained directly or associable by those skilled in the art directly from the disclosed contents of the present invention also belong to the protection scope of the present invention.

Claims (9)

化学元素の質量百分率表示で、Ｃ：０．１２〜０．１８％、Ｓｉ：０．１〜０．４％、Ｍｎ：１．１〜１．６％、Ｃｒ：０．１〜０．４％、Ｍｏ：０．２〜０．５％、Ｎｂ：０．０２〜０．０４％、Ｔｉ：０．０２〜０．０５％、Ｂ：０．００１５〜０．００５％、Ａｌ：０．０１〜０．０５％、Ｃａ：０．０００５〜０．００５％、Ｎ≦０．００８％を含有し、且つ０＜（Ｔｉ−３．４Ｎ）≦０．０２％、Ｔｉ／Ｂ≧１０を満足し、残部がＦｅおよび他の不可避不純物であり、
そのミクロ組織が焼戻ソルバイトであることを特徴とし、
その降伏強度が１０３４〜１２４１ＭＰａであり、引張強度が１１０３ＭＰａ以上であり、伸び率が２０％〜３０％であり、０°横向シャルピー衝撃功が１２０Ｊ以上であり、靱脆遷移温度が−７０℃以下であることを特徴とする超高強度・超高靱性油井管。 In terms of mass percentage of chemical elements, C: 0.12 to 0.18%, Si: 0.1 to 0.4%, Mn: 1.1 to 1.6%, Cr: 0.1 to 0.4 %, Mo: 0.2-0.5%, Nb: 0.02-0.04%, Ti: 0.02-0.05%, B: 0.0015-0.005%, Al: 0.0. 01 to 0.05%, Ca: 0.0005 to 0.005%, N ≦ 0.008%, and 0 <(Ti-3.4N) ≦ 0.02%, Ti / B ≧ 10 satisfied, Ri balance Fe and other inevitable impurities der,
Its microstructure is tempered sorbite,
Its yield strength is 1034 to 1241 MPa, tensile strength is 1103 MPa or more, elongation is 20% to 30%, 0 ° transverse Charpy impact is 120 J or more, and tough and brittle transition temperature is −70 ° C. or less. Ultra-high strength and ultra-tough oil well pipe characterized by 化学元素の質量百分率表示で、Ｃ：０．１２〜０．１８％、Ｓｉ：０．１〜０．４％、Ｍｎ：１．１〜１．６％、Ｃｒ：０．１〜０．４％、Ｍｏ：０．２〜０．５％、Ｎｂ：０．０２〜０．０４％、Ｔｉ：０．０２〜０．０５％、Ｂ：０．００１５〜０．００５％、Ａｌ：０．０１〜０．０５％、Ｃａ：０．０００５〜０．００５％、Ｎ≦０．００８％を含有し、且つ０＜（Ｔｉ−３．４Ｎ）≦０．０２％、Ｔｉ／Ｂ≧１０を満足し、残部がＦｅおよび他の不可避不純物であり、
そのミクロ組織が焼戻ソルバイトであることを特徴とし、
その降伏強度が１０６９〜１２７６ＭＰａであり、引張強度が１１３８ＭＰａ以上であり、その伸び率が２０％〜２５％であり、０°横向シャルピー衝撃功が１２０Ｊ以上であり、靱脆遷移温度が−６０℃以下であることを特徴とする超高強度・超高靱性油井管。 In terms of mass percentage of chemical elements, C: 0.12 to 0.18%, Si: 0.1 to 0.4%, Mn: 1.1 to 1.6%, Cr: 0.1 to 0.4 %, Mo: 0.2-0.5%, Nb: 0.02-0.04%, Ti: 0.02-0.05%, B: 0.0015-0.005%, Al: 0.0. 01 to 0.05%, Ca: 0.0005 to 0.005%, N ≦ 0.008%, and 0 <(Ti-3.4N) ≦ 0.02%, Ti / B ≧ 10 Satisfied, the balance is Fe and other inevitable impurities,
Its microstructure is tempered sorbite,
The yield strength is 1069 to 1276 MPa, the tensile strength is 1138 MPa or more, the elongation is 20% to 25%, the 0 ° transverse Charpy impact is 120 J or more, and the tough brittle transition temperature is −60 ° C. ultra high strength and ultra high-toughness OCTG you equal to or less than. Ｖ元素を、０＜Ｖ≦０．１ｗｔ％でさらに含有することを特徴とする請求項１または２に記載の超高強度・超高靱性油井管。 The ultra-high strength and ultra-tough oil well pipe according to claim 1 or 2 , further comprising an element V in a range of 0 <V ≦ 0.1 wt%. 精錬工程、連続鋳造工程、穿孔工程、圧延工程、サイジング工程、熱処理工程を含むことを特徴とする請求項１〜３のいずれかに記載の超高強度・超高靱性油井管の製造方法。 Refining process, step continuous casting, perforation step, rolling step, the sizing method of manufacturing an ultra-high strength, ultra high-toughness OCTG according to any one of claims 1 to 3, characterized in that it comprises a heat treatment step. 前記連続鋳造工程において、溶鋼の過熱度を３０℃の未満にし、連続鋳造の引き上げ速度を１．８〜２．２ｍ／ｍｉｎにすることを特徴とする請求項４に記載の超高強度・超高靱性油井管の製造方法。 The super high strength and super strength according to claim 4 , wherein in the continuous casting step, the superheat degree of the molten steel is set to less than 30 ° C, and the pulling speed of the continuous casting is set to 1.8 to 2.2 m / min. A method for producing a tough oil well pipe. 前記穿孔工程において、連続鋳造工程で得られた丸ビレットを１２００〜１２４０℃の炉内で均一的に加熱して、穿孔温度を１１８０〜１２４０℃にすることを特徴とする請求項４に記載の超高強度・超高靱性油井管の製造方法。 5. The drilling process according to claim 4 , wherein the round billet obtained in the continuous casting process is uniformly heated in a furnace at 1200 to 1240 ° C. to set the drilling temperature to 1180 to 1240 ° C. 5. Manufacturing method of ultra-high strength and ultra-tough oil well pipe. 前記圧延工程において、最終圧延温度を９００〜９５０℃にすることを特徴とする請求項４に記載の超高強度・超高靱性油井管の製造方法。 The method for producing an ultra-high strength and ultra-tough oil well pipe according to claim 4 , wherein a final rolling temperature is set to 900 to 950 ° C in the rolling step. 前記サイジング工程において、サイジング温度が８５０〜９００℃であることを特徴とする請求項４に記載の超高強度・超高靱性油井管の製造方法。 5. The method for producing an ultrahigh strength / ultra high toughness well pipe according to claim 4 , wherein a sizing temperature is 850 to 900 ° C. in the sizing step. 前記熱処理工程において、オーステナイト化温度を９００〜９３０℃にして、３０〜６０ｍｉｎ保温後に焼入れして、４５０〜５５０℃で焼戻して、保温時間を５０〜８０ｍｉｎにして、最後に４００〜５５０℃で熱サイジングを行うことを特徴とする請求項４に記載の超高強度・超高靱性油井管の製造方法。 In the heat treatment step, the austenitizing temperature is set to 900 to 930 ° C., quenched after holding for 30 to 60 min, tempered at 450 to 550 ° C., set to 50 to 80 min, and finally heated at 400 to 550 ° C. Sizing is performed, The manufacturing method of the ultra-high-strength and ultra-tough oil well pipe of Claim 4 .
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US20170159157A1 (en) 2017-06-08

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