WO2013018564A1 - Procédé de laminage commandé d'un tube en acier sans soudure présentant d'excellentes propriétés de résistance et de ténacité à basse température - Google Patents

Procédé de laminage commandé d'un tube en acier sans soudure présentant d'excellentes propriétés de résistance et de ténacité à basse température Download PDF

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Publication number
WO2013018564A1
WO2013018564A1 PCT/JP2012/068547 JP2012068547W WO2013018564A1 WO 2013018564 A1 WO2013018564 A1 WO 2013018564A1 JP 2012068547 W JP2012068547 W JP 2012068547W WO 2013018564 A1 WO2013018564 A1 WO 2013018564A1
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Prior art keywords
rolling
piercing
temperature
steel tube
reducing
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English (en)
Inventor
Chihiro Hayashi
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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Priority to CN201280034212.0A priority Critical patent/CN103649344B/zh
Priority to KR1020147003904A priority patent/KR101660601B1/ko
Priority to EP12746130.9A priority patent/EP2739758B1/fr
Publication of WO2013018564A1 publication Critical patent/WO2013018564A1/fr
Anticipated expiration legal-status Critical
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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 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
    • C21D9/14—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

Definitions

  • the present invention relates to a controlled rolling method of a seamless steel tube excellent in strength and low-temperature toughness, which is applied in a process of making a seamless steel tube.
  • Examples of a process of making a seamless steel tube include a
  • Mannesmann-plug mill process a Mannesmann-mandrel mill process, Mannesmann- assel mill and a Mannesmann-push-bench mill process, and others.
  • a solid billet (round steel bar) heated at a predetermined temperature in a heating furnace is pierced and formed into a hollow piece in a hollow bar shape through a piercing-rolling mill of an inclined rolling process, and this hollow piece is formed into a hollow shell mostly by reducing a wall thickness thereof by using an elongation rolling mill such as a rotary elongator and a plug mill, a mandrel mill, an assel mill or a push-bench mill.
  • the resultant hollow shell is formed into a seamless steel tube in a predetermined size mostly by reducing an outer diameter thereof by using a reducing rolling mill such as a sizer or a stretch-reducer.
  • FIGS. 1 are drawings of explaining configurations of apparatuses used in the Mannesmann-mandrel mill process, and (a) illustrates a rotary hearth type heating furnace, (b) illustrates a rotary piercing mill (inclined cross roll piercing mill) (c) illustrates a mandrel mill (elongation rolling mill), (d) illustrates a reheating furnace, and (e) illustrates a stretch reducer (reducing rolling mill), respectively.
  • a full float mandrel mill was commonly used at the beginning, in which a mandrel bar is inserted into the inside of a hollow shell and this hollow shell along with the inserted mandrel bar is continuously rolled by grooved caliber rolls, which is an innovation of a mandrel bar operating process; but recently, a retained mandrel mill (restrained mandrel mill) has been more widely used as a mandrel mill ensuring high efficiency and high quality.
  • a full retract process is commonly employed, and in the production of a small-diameter seamless steel tube, a semi-float process is commonly employed.
  • an extractor is disposed on a delivery side of a mandrel mill, and a hollow shell is pulled out by the mandrel mill during the rolling operation. If a temperature of metal of the shell on the delivery side of the mandrel mill is sufficiently high, the hollow shell can be pulled out by a sizing mill (sizer) instead of an extractor, so that this hollow shell can be subjected to a reducing rolling into a final target size, which can dispense with a reheating furnace.
  • a sizing mill sizer
  • a sizer is used in the production of a medium-diameter seamless steel tube, and a stretch reducer is used in the production of a small-diameter seamless steel tube.
  • a sizer a sinking sizer or a reducer whose rate of the number of revolutions of rolls in each stand is invariable was used at the beginning, but in recent years, a triple-roll type sizer or stretch reducer whose respective stands are independently driven has been widely used.
  • the above mentioned triple-roll type stretch reducer includes 24 to 28 stands at maximum, and these independently driven stands can have tension force as much as 85% of deformation resistance at maximum to act between these stands, which enables not only outer diameter reduction but also wall thickness adjustment in a considerably wide range.
  • a triple-roll type sizer includes 8 to 12 stands at maximum, and has fewer stands than those of a stretch reducer, so that large tension force cannot be expected between these stands.
  • a triple-roll type sizer attains outer diameter reduction per stand which is much smaller than that of a stretch reducer.
  • the controlled rolling technology has been developed as a production technique for source material of a UOE large-diameter welded steel pipe.
  • Source material of a UOE large-diameter welded steel tube is produced through a reverse rolling process by using a thick plate rolling mill.
  • Such a thick plate rolling technique has been remarkably progressed in order to satisfy demands for high strength, improvement of low temperature toughness and less alloy elements of a line pipe.
  • strengthening mechanism of steel includes solid-solution strengthening, precipitation strengthening, precipitation hardening, fine grain strengthening and transformation strengthening and others.
  • the solid- solution strengthening involves increase in alloy elements, which conflicts with the demand for less alloy elements.
  • the grain refinement is the only method for coping with both of strength and toughness, and it could be said that the progress of material in the rolling technology is attributable to the efforts of the technical development for attaining grain refinement.
  • the controlled rolling method is a rolling technique for attaining grain refinement only through the rolling process by appropriately controlling processing heat history such as chemical compositions, heating temperature, rolling temperature and rolling reduction rate, and has been widely employed in the production of source materials for a high-strength and high-toughness line pipe.
  • the controlled rolling method can be considered in three phases of the metallurgical mechanism. Specifically, the controlled rolling method can be categorized into three phases as follows.
  • Phase 1 rolling in the recrystallization temperature region of the ⁇ phase at a relatively higher temperature (950°C or more).
  • Phase 2 rolling in the non-recrystallization temperature region of the ⁇ phase at a lower temperature (950°C or less, Ar3 transformation point or more).
  • FIG. 2 is a diagram of iron - carbon equilibrium.
  • FIG. 3 is a drawing of explaining three phases of the metallurgical mechanism in the controlled rolling step, and representing the change of microstructure in respective rolling temperature regions in the above mentioned three phases.
  • the source of FIG. 3 is cited from " 'Today and future of manufacturing technologies of steel tube and pipe, 1 12 th , 1 13 th Nishiyama memorial Seminars,' The Iron and Steel Institute of Japan", and it should be noted that this drawing had been a metallurgical conceptual diagram before the controlled rolling method was developed, so that this drawing does not reflect a current metallurgical conceptual diagram after the controlled rolling method was developed.
  • the ⁇ grains that coarsened due to heating get refined through repetitive rolling-recrystallization in the recrystallization temperature region. If the ⁇ grains are rolled in the low temperature region where the ⁇ grains are unlikely to be recrystallized, the ⁇ grains are elongated without being recrystallized, so as to form deformation zones and annealing twins inside the grains. At the time of the ⁇ - ⁇ - ⁇ transformation, the deformation bands and the annealing twins along with the ⁇ grain boundary contribute as formation sites of a transformation nuclei, which results in refinement of a grains.
  • the untransformed ⁇ grains become further more elongated so as to form deformation bands inside the grains.
  • the transformed a grains are also subjected to the rolling so that subgrains are formed in the grains, which results in further refinement of the a grains.
  • Intensified dual phase region rolling realizes increase in strength thanks to the grain refinement effects, but at the same time, promotes strong rolling texture, and generates separations in Charpy and DWTT fracture surfaces, which results in decrease in fracture transition temperature.
  • the dual phase region rolling has been utilized as far as the toughness in accordance with the toughness requirement is not impaired, but gradually phased out as the controlled cooling technology is developed.
  • Controlled rolled bainitic steel (acicular ferrite steel) has been developed for the purpose of grain refinement through controlled rolling and increase in strength by transformation strengthening.
  • Increase in amount of bainite significantly enhances the strength, which is advantageous to high-strength steel of X 70 or more.
  • the amount of bainite increases along with increase in amount of Mn, and at the same time the Ar3 point becomes lower, thereby refining the a grains and enhancing the strength and the toughness.
  • Slight addition of B into Nb and TiC contributes to generation of bainite, thereby attaining high strength without deteriorating toughness.
  • Patent Literature 1 Japanese Patent Application Publication No. 06-240357
  • Patent Literature 2 Japanese Patent Application Publication No. 11-302785
  • Patent Literature 3 Japanese Patent Application Publication No. 2001-240913
  • the controlled rolling method is a thermo-mechanical treatment method developed in a rolling step of a thick plate which is source material of UOE large-diameter welded steel pipe, and the achievement thereof significantly depends on the fact that a thick plate rolling mill applies reverse rolling. Therefore, the above technique cannot be applied directly to a hot strip mill that applies oneway rolling.
  • the low-temperature rolling in the non-recrystallization region of the ⁇ phase should be carried out at least in the elongation rolling step.
  • the non-recrystallized ⁇ grains cannot be elongated and extended because while the outer-diameter rolling reduction is carried out, the wall-thickness reduction is not carried out in this reducing rolling step.
  • the elongation rolling process entails the low-temperature rolling in the non- recrystallization temperature region of the ⁇ phase.
  • the Ar3 transformation point varies according to the C content of a shell material, as illustrated in FIG. 2: approximately 850°C for a low-carbon steel of 0.10%C; 800°C for a medium-carbon steel of 0.30%C; and 770°C for a medium- carbon steel of 0.50%C.
  • the non-recrystallization region of the ⁇ phase falls within the temperature range from 100°C to 180°C at most, which is extremely narrow temperature range. Hence, it is not easy to maintain the rolling temperature in the elongation rolling step within this narrow temperature range.
  • the rolling of a seamless steel tube is one way rolling, and its rolling speed is high, and its cooling speed is further higher than the rolling speed since the metal of shell is cooled on both inner and outer surfaces, accordingly it is further more difficult to control the rolling temperature of the seamless steel tube than the case of the thick plate rolling.
  • FIG. 4 is a drawing of showing the respective relations between the rolling temperature and the deformation resistance: (a) in low-carbon killed steel; (b) in 0.5%Mo steel; and (c) in 1.0%Cr steel.
  • This source is cited from the literature " 'Rolling Theory and Its Application', The Iron and Steel Institute of Japan".
  • the deformation resistance varies based on the chemical compositions and the strain rate of source material, and in the comparison of the rolling temperature between 1200°C and 900°C, the temperature decrease by 300°C causes triple increase in deformation resistance.
  • FIG. 5 is a drawing of illustrating influence of rolling temperature on hot deformation of medium carbon steel.
  • the hot deformability is represented by the number of torsion at fracture in a torsion test, and the source of this is cited from '"Rolling Theory and Its Application', The Iron and Steel Institute of Japan.
  • the present invention has been made in light of the above mentioned problems from (1) to (3), and has an object to provide a specific controlled rolling method in a process of making a seamless steel tube, so as to produce a seamless steel tube excellent in strength and low-temperature toughness, along with use of a controlled cooling process.
  • the present invention relates to the controlled rolling technology of a seamless steel tube, and the controlled cooling technique is an associated technique following completion of the controlled rolling step.
  • the present invention does not have an object to provide new findings in the controlled cooling process, but intends to realize the controlled rolling technology in producing a seamless steel tube.
  • the present inventers have focused attention on that, when performing controlled rolling in a process of making a seamless steel tube, it is preferable to perform thin-wall piercing at high reduction rate by using an inclined cross piercing mill through the diameter-expansion piercing method, and it is effective to perform piercing at a higher temperature within the recrystallization region of the ⁇ phase in the piercing-rolling step, to cope with significant increase in rolling load and significant deterioration of hot deformability in a piercing-rolling mill and an elongation rolling mill in case of the low- temperature rolling.
  • the present invention has been made based on the above focus, and the summaries of the present invention consists in the following controlled rolling method of a seamless steel tube.
  • a controlled rolling method of a seamless steel tube comprising: in the piercing-rolling step, performing piercing-rolling in a recrystallization region of a ⁇ phase (950°C or more); in the elongation rolling step, performing elongation rolling within a non- recrystallization region of a ⁇ phase (950°C to Ar3 transformation point); in the reducing rolling step, performing reducing rolling in a (a + ⁇ ) dual phase temperature region (Ar3 transformation point to Arl transformation point); and performing controlled cooling or quenching immediately after the reducing rolling.
  • the controlled rolling method of a seamless steel tube according to the present invention can solve the problems of significant increase in hot deformation resistance and significant deterioration of hot deformability (hot workability) due to low-temperature rolling, and can produce a seamless steel tube excellent in strength and low-temperature toughness, along with use of the controlled cooling process.
  • FIGS. 1 are drawings of explaining configurations of apparatuses used in the Mannesmann-mandrel mill process, and (a) illustrates a rotary hearth type heating furnace, (b) illustrates a rotary piercing mill (inclined cross roll piercing mill) (c) illustrates a mandrel mill (elongation rolling mill), (d) illustrates a reheating furnace, and (e) illustrates a stretch reducer (reducing rolling mill), respectively.
  • FIG. 2 is a diagram of iron - carbon equilibrium.
  • FIG. 3 is a drawing of explaining the three phases of the metallurgical mechanism in the controlled rolling step.
  • FIGS. 4 are drawings of showing the respective relations between the rolling temperature and the deformation resistance: (a) in low-carbon killed steel; (b) in 0.5%Mo steel; and (c) in 1.0%Cr steel.
  • FIG. 5 is a drawing of illustrating influence of rolling temperature on hot deformation of medium carbon steel.
  • FIG. 6 is a drawing of illustrating the piercing principle of the diameter- expansion piercing method by using an inclined cross piercing mill.
  • FIG. 7 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the rolling torque in the piercing-rolling.
  • FIG. 8 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the rolling power.
  • FIG. 9 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the number of rotary forging times.
  • FIG. 10 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the circumferential shear strain ⁇ .
  • the controlled rolling method of a seamless steel tube according to the present invention is a controlled rolling method to be applied to a process of making a seamless steel tube, that is, the steps of making a seamless steel tube including: a heating furnace ⁇ a piercing-rolling mill ⁇ an elongation rolling mill (reheating furnace) ⁇ a reducing rolling mill.
  • piercing-rolling is carried out in the
  • the recrystallization temperature region of the ⁇ phase (approximately 950°C or more)
  • the elongation rolling and the reducing rolling are carried out within the non-recrystallization temperature region of the ⁇ phase (approximately 950°C to Ar3 transformation point), and then the controlled cooling or the quenching is carried out immediately after the reducing rolling.
  • the controlled rolling method of a seamless steel tube according to the present invention is a controlled rolling method that is applied to the process of making a seamless steel tube, in which in the piercing-rolling step, the piercing- rolling is carried out in the recrystallization temperature region of the ⁇ phase (950°C or more), then, in the elongation rolling step, the elongation rolling is carried out in the non-recrystallization temperature region of the ⁇ phase (950°C to Ar3
  • the reducing rolling is carried out in the ( ⁇ + ⁇ ) dual phase temperature region (Ar3 transformation point to Arl transformation point), and the controlled cooling or the quenching is carried out immediately after this reducing rolling. Note that this method is limitedly applied to the case of using a sizer as a reducing rolling mill.
  • the moderately low-temperature rolling should be carried out in the piercing-rolling step, and the piercing be carried out at a higher temperature within the recrystallization temperature region of the ⁇ phase, preferably at the temperature of 1050°C or more.
  • the cooling speed of a hollow piece after the piercing becomes higher even if processing heat is generated in the piercing-rolling step, so that the non- recrystallization temperature region of the ⁇ phase can be maintained relatively easily in the elongation rolling step.
  • an inclined cross piercing mill having cone-type main rolls is employed in the piercing-rolling step, so as to not only drastically reduce load in the piercing-rolling by performing the thin-wall piercing at high reduction rate through the diameter-expansion piercing method, and but also undertake, in the piercing- rolling step, substantially half of the amount of wall thickness reduction that should occur in the elongation rolling step, thereby drastically reducing load in the elongation rolling.
  • FIG. 6 is a drawing of illustrating the piercing principle of the diameter- expansion piercing method by using an inclined cross piercing mill.
  • the diameter- expansion piercing suppresses the rotary forging effect in front of a plug.
  • the feed angle ⁇ and the roll cross angle ⁇ are defined respectively in the same drawing.
  • FIG. 7 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the rolling torque in the piercing-rolling.
  • FIG. 8 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the rolling power.
  • ⁇ denotes the roll cross angle
  • ⁇ denotes the feed angle, respectively.
  • the source of FIG. 6 to FIG. 8 is cited from " 'Production Method of Steel Tube', The Iron and Steel Institute of Japan".
  • FIG. 9 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the number of rotary forging times.
  • FIG. 10 is a drawing of showing influences of the expansion ratio, the roll cross angle and the feed angle on the circumferential shear strain y ⁇ .
  • ⁇ denotes the roll cross angle
  • ⁇ denotes the feed angle, respectively in FIG. 9 and FIG. 10.
  • the source of FIG. 9 and FIG. 10 is cited from " 'Production Method of Steel Tube', The Iron and Steel Institute of Japan".
  • the controlled rolling method of a seamless steel tube according to the present invention, influencing on strength and low-temperature toughness based on the following Examples.
  • the rolling temperature in each step in the Examples is represented by the temperature on the delivery side of each rolling mill.
  • a 147.0 mm ⁇ medium-carbon round steel bar having a chemical composition of 0.30 %C - 1.10 %Mn - 0.30 %Mo was used as a test sample, and this sample was rolled into a size of 76.2 mm ⁇ x 4.0 mm t by a small-diameter Mannesmann mandrel mill process including a heating furnace ⁇ an inclined cross piercing mill ⁇ a mandrel mill ⁇ a reheating furnace ⁇ a stretch reducer.
  • the rolling condition in each step is as follows.
  • Rolling temperature 1 110°C (recrystallization temperature region of ⁇ phase)
  • Rolling condition roll cross angle: 10°
  • roll feed angle 12°
  • expansion ratio
  • Heating temperature 920°C
  • a 225.0 mm ⁇ medium-carbon round steel bar having a chemical composition of 0.40 %C - 1.20 %Mn - 0.35 %Mo was used as a test sample, and this sample was rolled into a size of 273.0 mm ⁇ x 6.5 mm t by a medium-diameter Mannesmann mandrel mill process including a heating furnace ⁇ an inclined cross piercing mill ⁇ a mandrel mill ⁇ sizer.
  • the rolling condition in each step is as follows.
  • Rolling temperature 1090°C (recrystallization temperature region of ⁇ phase)
  • Rolling condition roll cross angle: 20°
  • roll feed angle 10°
  • expansion ratio 1.488
  • piercing ratio 2.55
  • a 225.0 mm ⁇ low-carbon round steel bar having a chemical composition of 0.10 %C - 0.65 %Mn - 0.05 %Mo was used as a test sample, and this sample was rolled into a size of 273.0 mm ⁇ x 6.5 mm t by a medium-diameter Mannesmann mandrel mill process including a heating furnace ⁇ an inclined cross piercing mill ⁇ a mandrel mill ⁇ sizer.
  • the rolling condition in each step is as follows.
  • the rolling size in each step is the same as that in Example 2.
  • Rolling temperature 1070°C (recrystallization temperature region of ⁇ phase)
  • Rolling condition roll cross angle: 20°
  • roll feed angle 10°
  • expansion ratio 1.488
  • piercing ratio 2.55
  • the reducing rolling step performs the ( + ⁇ ) dual phase region rolling, but the rolling of reducing wall thickness was not carried out although the outer diameter reduction rolling, while slight reduction, was carried out, so that no grains were elongated and no side effects such as separations were observed.
  • a stretch reducer is used as a reducing rolling mill, it is preferable to avoid to perform the reducing rolling in the ( + ⁇ ) dual phase region as much as possible. Strains are accumulated by the outer-diameter reduction rolling in back-to-back multiple stands, which may cause separations in a Charpy test or the like. In the case of using a stretch reducer in the reducing rolling step, a reheating furnace is disposed, thus, there are no hindrances in the reducing rolling in the non- recrystallization temperature region of the ⁇ phase.
  • the strength required for an oil well tube and a line pipe is usually 740 Mpa or more in terms of YS, and the required low-temperature toughness is usually -80°C in terms of vTrs.
  • the controlled rolling method is the specific subject matter of the present invention, but the controlled cooling process is not the subject of the present invention.
  • the description of "cold water quenching" in the item of the "controlled cooling” merely indicates a simulation of ultimate controlled cooling by using the existing quenching system.
  • the present invention can solve the problems of significant increase in hot deformation resistance and significant deterioration of hot deformability (hot workability) due to low temperature rolling, resulted from applying the controlled rolling method to the process of making a seamless steel tube, and can produce a seamless steel tube excellent in strength and low-temperature toughness, along with use of the controlled cooling process.

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Abstract

La présente invention concerne un procédé de laminage commandé d'un tube en acier sans soudure présentant d'excellentes propriétés de résistance et de ténacité à basse température à appliquer à un processus de fabrication d'un tube en acier sans soudure. Le procédé de laminage commandé de l'invention fait appel à la réalisation d'un perçage-laminage dans la région de recristallisation de la phase γ (température supérieure ou égale à environ 950 °C); la réalisation d'un laminage d'allongement et d'un laminage de réduction à l'intérieur de la région de non-recristallisation de la phase γ (température allant de 950 °C au point de transformation Ar3) lors de l'étape de laminage d'allongement et lors de l'étape de laminage de réduction; et la réalisation d'un refroidissement ou d'une trempe commandé(e) immédiatement après le laminage de réduction. Si un calibreur est utilisé pendant l'étape de laminage de réduction, le laminage dans la région de température des deux phases (α + γ) (température allant du point de transformation Ar3 au point de transformation Ar1) est effectué pendant l'étape de laminage de réduction. Le procédé de laminage commandé de la présente invention peut résoudre des problèmes d'augmentation significative de la résistance à la déformation à chaud et de détérioration significative de la capacité de déformation à chaud (capacité de façonnage à chaud) dus au laminage à basse température et permet de produire un tube en acier sans soudure présentant d'excellentes propriétés de résistance et de ténacité à basse température, conjointement avec l'utilisation d'un procédé de refroidissement commandé.
PCT/JP2012/068547 2011-08-01 2012-07-17 Procédé de laminage commandé d'un tube en acier sans soudure présentant d'excellentes propriétés de résistance et de ténacité à basse température Ceased WO2013018564A1 (fr)

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CN201280034212.0A CN103649344B (zh) 2011-08-01 2012-07-17 强度和低温韧性优异的无缝钢管的控制轧制方法
KR1020147003904A KR101660601B1 (ko) 2011-08-01 2012-07-17 강도와 저온 인성이 우수한 이음매 없는 강관의 제어 압연 방법
EP12746130.9A EP2739758B1 (fr) 2011-08-01 2012-07-17 Procédé de laminage commandé d'un tube en acier sans soudure présentant d'excellentes propriétés de résistance et de ténacité à basse température

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JP2011-168473 2011-08-01
JP2011168473A JP5177261B2 (ja) 2011-08-01 2011-08-01 強度と低温靱性に優れた継目無鋼管の制御圧延方法

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WO2016164788A1 (fr) * 2015-04-10 2016-10-13 The Nanosteel Company, Inc. Aptitude au formage de bord améliorée dans des alliages métalliques
US10465260B2 (en) 2015-04-10 2019-11-05 The Nanosteel Company, Inc. Edge formability in metallic alloys
CN111589869A (zh) * 2020-01-09 2020-08-28 西北工业大学 一种2219铝合金管的高强韧二辊斜轧穿孔方法
CN113430359A (zh) * 2021-05-19 2021-09-24 西北工业大学 一种大尺寸炮钢棒材的高强韧轧制方法
CN114589203A (zh) * 2022-01-25 2022-06-07 大冶特殊钢有限公司 一种适用于低温的09MnNiD无缝钢管的制备方法

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