EP2952592B1 - Fertigungsverfahren und fertigungsvorrichtung für nahtlose stahlrohre mit ausgezeichneter zähigkeit - Google Patents

Fertigungsverfahren und fertigungsvorrichtung für nahtlose stahlrohre mit ausgezeichneter zähigkeit Download PDF

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EP2952592B1
EP2952592B1 EP14746700.5A EP14746700A EP2952592B1 EP 2952592 B1 EP2952592 B1 EP 2952592B1 EP 14746700 A EP14746700 A EP 14746700A EP 2952592 B1 EP2952592 B1 EP 2952592B1
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pipe
pipe body
quenching
tempering
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French (fr)
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EP2952592A4 (de
EP2952592A1 (de
Inventor
Takeshi Suzuki
Kenichiro Eguchi
Yasuhide Ishiguro
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JFE Steel Corp
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JFE Steel Corp
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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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for cooling
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a method and a facility for manufacturing a seamless steel pipe excellent in toughness. These are used in particular for manufacturing a product pipe with excellent toughness by performing quenching and tempering, which is thermal refining, on a pipe body, which is an intermediate product (semimanufactured product) of a seamless steel pipe of a steel grade such as stainless steel having a low Ms point (martensitic transformation start temperature) and a low Mf point (martensitic transformation finish temperature).
  • excellent in toughness refers to, for example, the quality of satisfying ISO standard 13680. That is to say, it means that, when a Charpy impact test is performed on three transverse test pieces (in C direction) which are taken from the central part of the wall thickness of a product pipe at a test temperature of -10°C, the average absorbed energy (vE -10 ) of the three test pieces is 40 J or more, and the number of test pieces whose absorbed energy is less than 40 J is one or less, where the absorbed energy thereof is 27 J or more (2/3 or more of the required value of 40 J).
  • Examples of related art for manufacturing a seamless steel pipe include the following techniques.
  • Patent Literature 1 discloses a technique for manufacturing a product having high strength and high toughness by controlling a heating temperature and a cooling rate when a quenching heat treatment is performed in order to manufacture a 13Cr seamless stainless steel pipe having a large wall thickness.
  • Patent Literature 2 discloses a facility for minimizing a decrease in productive efficiency when a quenching treatment is performed on a steel grade on which quenching treatment cannot be performed at a high cooling rate. In the facility, however, the heat treatment is performed on a first-in first-out basis as long as no trouble occurs.
  • Patent Literature 3 discloses a method for manufacturing a seamless steel pipe composed of a martensite-ferrite dual phase steel.
  • Patent Literature 4 discloses a technique for decreasing a variation in hardness in the longitudinal direction of a steel pipe after quenching has been performed using a quenching method in which a quenching liquid is made to flow in one direction through the steel pipe, by controlling the flow rate of the liquid in accordance with the measured values of temperatures of the liquid which are determined on the entrance side and exit side of the pipe.
  • a pipe body which is an intermediate product of a seamless steel pipe of a steel grade of, for example, martensitic stainless steel, is subjected to a heat treatment for quenching and tempering so as to be controlled to at the required level of strength and toughness after having been made into a pipe having a predetermined size by performing tube rolling using hot working.
  • the pipe body is heated to a temperature equal to or higher than the Ac 1 point and equal to or lower than the Ac 3 point in a heating furnace and then rapidly cooled to near room temperature by performing, for example, water cooling first in a quenching treatment, and the rapidly cooled pipe body is heated to a temperature equal to or lower than the Ac 1 point in another heating furnace and then allowed to cool in a subsequent tempering treatment (refer to, for example, Patent Literature 1).
  • a subsequent tempering treatment (refer to, for example, Patent Literature 1).
  • facilities by which such heat treatments are performed are continuously linable, and treatment conditions such as heating temperatures and heating times are respectively set in accordance with various kinds of products.
  • a desired area ratio of a martensite phase is achieved by performing quenching and tempering described above.
  • an Ms point and an Mf point widely vary in accordance with steel chemical composition which characterizes the steel grade, and there is even a steel grade having an Ms point lower than 100°C and an Mf point lower than room temperature.
  • the temperature of the pipe body after quenching has been performed is commonly confirmed by determining the surface temperature thereof.
  • a quenching method and a quenching facility for decreasing a variation in hardness in the longitudinal direction of a pipe body by performing flow control of a quenching liquid are known (refer to, for example, Patent Literature 4), however, there is a problem in that it is difficult to realize not only a decrease in material variability due to non-uniform microstructure distribution in the wall thickness direction of a pipe body of specific steel grades but also the maintenance of a satisfactory productive efficiency for the whole heat treatment line at the same time in the case where the specific steel grades and other steel grades are subjected to a heat treatment in the same heat treatment line as described above.
  • the present inventors diligently conducted investigations in order to solve the problems described above, and as a result, found that there is a significant decrease in material variability described above and that there is an improvement in the average value of data (average value of vE -10 ) within the range of the material variability described above, by discriminating pipe bodies made of steel grades having an Ms point lower than 200°C from pipe bodies made of the other steel grades, and in the case of former, after water cooling has been performed for quenching, by additionally leaving the pipe bodies at room temperature until the temperature difference between the portion having the highest temperature and the portion having the lowest temperature in a cross section in a direction at a right angle to the pipe axis (in the wall thickness direction) becomes less than 2.0°C. In the case of latter, it is appropriate that the pipe bodies be subjected to ordinary quenching and tempering.
  • the present invention has been completed on the basis of the knowledge described above, and the subject matter of the present invention is as follows.
  • Fig. 1 is a schematic plan view illustrating an example of a heat treatment line used for the present invention.
  • Fig. 1 is a schematic plan view illustrating an example of a heat treatment line used for the present invention.
  • a pipe body also called pipe A for convenience
  • a pipe body which has been judged to be a pipe having an Ms point of 200°C or higher
  • a heating furnace for quenching 2 is heated to an appropriate temperature corresponding to its steel grade using a heating furnace for quenching 2, and then cooled so that the temperature of the outer surface of the pipe body becomes almost equal to room temperature by immersing the pipe body in cooling water in a quenching water tank 3.
  • the pipe body is transported through a cooling bed 4 to a heating furnace for tempering 5 in which the pipe body is subjected to a tempering treatment at an appropriate temperature corresponding to its steel grade.
  • the Ms point is calculated using equation (1) described later.
  • a pipe body (also called pipe B for convenience), which has been judged to be a pipe having an Ms point lower than 200°C, is treated in the same pathway as a pipe A is treated until the pipe body is transported to the cooling bed 4.
  • a pipe B is transported to a holding bed (also called buffer line) 6, which is a different pathway from that to which the pipe A is transported, and left at room temperature on the buffer line 6 until the temperature difference (referred to as ⁇ T) between the portion having the highest temperature and the portion having the lowest temperature in a cross section in a direction at a right angle to the pipe axis becomes less than 2.0°C.
  • the pipe B is returned to the cooling bed 4 and subjected to a tempering treatment in the same pathway as the pipe A is treated.
  • the cooling bed 4 and the holding bed 6 are different facilities from each other in the example of the present invention. However, in the case where there is sufficient room on the cooling bed 4, some part of the cooling bed may be used as a holding bed.
  • examples of the specific steel grade described above include, for example, a steel grade having a chemical composition containing, by mass%, C: 0.005% to 0.05%, Si: 0.05% to 1.0%, Mn: 0.2% to 1.8%, P: 0.03% or less, S: 0.005% or less, Cr: 11% to 20%, Ni: 1.5% to 10%, Mo: 1% to 5%, N: 0.15% or less, and the balance being Fe and inevitable impurities.
  • the chemical composition may further contain, by mass%, one, two, or more selected from among Al: 0.002% to 0.05%, Cu: 3.5% or less, Nb: 0.5% or less, V: 0.5% or less, Ti: 0.3% or less, Zr: 0.2% or less, W: 3% or less, B: 0.01% or less, Ca: 0.01% or less, and REM: 0.01% or less instead of some portion of Fe.
  • a martensitic transformation ratio that is, the amount of residual austenite at each position in the wall thickness direction of a pipe body is practically determined by the temperature distribution in the wall thickness direction of the pipe body (temperature distribution in a cross section in a direction at a right angle to the pipe axis) when starting tempering.
  • a difference (variation) in the amount of residual austenite at the positions in the wall thickness direction of the pipe body is non-negligible.
  • Such a variation in the amount of residual austenite is one of the factors which cause the material variability of a product.
  • a pipe B is left at room temperature until ⁇ T becomes less than 2.0°C according to the present invention.
  • the reason why the discrimination criterion for a pipe B is set to be that the pipe has an Ms point lower than 200°C is because it was found that, from the results of the experiments conducted by the present inventors, there is practically no problem with considering that this criterion is almost equivalent to the condition that the pipe has an Mf point lower than room temperature.
  • the Ms point is calculated using equation (1) below which has been derived using regression analysis regarding the relationship between the contents [mass%] of the constituents of the chemical composition of steel and the experimental data of the Ms point which were determined using the thermal expansion curves which were obtained in advance by conducting continuous cooling transformation experiments using thermal expansion test pieces having various chemical compositions for the specified steel grade described above.
  • a waiting time (lead time) from an end of quenching treatment (water cooling) to a start of tempering treatment is set in accordance with the steel grade which is going to be heat-treated.
  • a Ms point is determined in advance using equation (1) above, and a calculation device is prepared by combining measured data of an ambient temperature and surface temperature of a pipe body, and heat-transfer calculation.
  • Steel billets having the chemical compositions and the Ms points, which were calculated using equation (1), given in Table 1 were formed into pipes by performing hot working, and thereafter air-cooled to a temperature of 100°C to room temperature to obtain 10 pipe bodies having an outer diameter of 195.0 mm and a wall thickness of 27.0 mm which were used as starting materials of seamless steel pipes.
  • the pipe bodies were left at room temperature (in atmospheric air) for 8 hours or more, then charged into a heating furnace for tempering when ⁇ T (calculated value) became 1.2°C to 1.8°C , and subjected to a tempering treatment at a temperature of 600°C.
  • ⁇ T (calculated value) was 6.0°C when the pipe bodies were charged into the heating furnace for tempering.
  • V-notched test pieces S1, S2, and S3 which were taken from each of the tempered pipe bodies in accordance with JIS Z 2202 (sampling position was the central part of the wall thickness of the pipe body, the length of the test piece was 10 mm, the longitudinal direction of the test piece was the circumferential direction of the pipe body (C direction), and the depth direction of the V notch was the longitudinal direction of the pipe body (L direction)
  • a Charpy impact test was conducted in accordance with JIS Z 2242 and vE -10 was obtained.
  • Table 2 indicates, in the case of the examples of the present invention, the average value of vE -10 values (the number of the samples was 15) was 87.7 J, where there was no test piece having a vE -10 value of less than 40 J. In addition, the variation in the vE -10 value was very small as indicated by a standard deviation of 3.8 J. On the other hand, in the case of the comparative examples, the average value of the vE -10 values (the number of the samples was 15) was 81.7 J. However, there were two test pieces having a vE -10 value of less than 40 J.

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

Claims (2)

  1. Verfahren für die Herstellung eines nahtlosen Stahlrohrs, umfassend einen Vorgang zur Durchführung des Vergütens an einem Rohrkörper (1), der ein Zwischenprodukt eines nahtlosen Stahlrohrs mit einer chemischen Zusammensetzung ist, die in Massen-% besteht aus: C 0,005% bis 0,05%, Si: 0,05% bis 1,0%, Mn: 0,2% bis 1,8%, P: 0,03% oder weniger, S: 0,005% oder weniger, Cr: 11% bis 20%, Ni: 1,5% bis 10%, Mo: 1% bis 5%, N: 0,15% oder weniger, wahlweise eines, zwei oder mehr, ausgewählt aus Al: 0,002% bis 0,05%, Cu: 3,5% oder weniger, Nb: 0,5% oder weniger, V: 0,5% oder weniger, Ti: 0,3% oder weniger, Zr: 0,2% oder weniger, W: 3% oder weniger, B: 0,01% oder weniger, Ca: 0,01% oder weniger und REM: 0,01% oder weniger, wobei der Rest Fe und unvermeidliche Verunreinigungen sind, wobei das Verfahren umfasst: im Voraus Bestimmen, ob der Rohrkörper (1) aus einer Stahlsorte mit einem Ms-Punkt unter 200°C hergestellt ist oder nicht; zusätzliches Belassen des Rohrkörpers (1) aus einer Stahlsorte mit einem Ms-Punkt von weniger als 200°C bei Raumtemperatur, bis die Temperaturdifferenz zwischen dem Abschnitt mit der höchsten Temperatur und dem Abschnitt mit der niedrigsten Temperatur in einem Querschnitt in einer Richtung in einem rechtem Winkel zur Rohrachse nach der Abschreckbehandlung weniger als 2,0°C annimmt, und anschließendes Durchführen der Temperbehandlung; und andererseits Durchführen einer Temperbehandlung an dem Rohrkörper (1) einer Stahlsorte, die keinen Ms-Punkt von weniger als 200°C aufweist, ohne den Rohrkörper (1) bei Raumtemperatur zu belassen, nachdem eine Abschreckbehandlung durchgeführt wurde, wobei der Ms-Punkt unter Verwendung der Gleichung (1) berechnet wird: Ms ° C = 502 − 810 % C − 1230 % N − 13 % Mn − 30 % Ni − 12 % Cr − 54 % Cu − 6 % Mo
    Figure imgb0004
     wobei unter der Annahme, dass M ein Atomsymbol ist, das Symbol (%M) den Gehalt eines konstituierenden chemischen Elements darstellt, das durch das Symbol M in Gleichung (1) dargestellt wird, und (%M) dem Wert 0 zugewiesen wird, für den fall, dass das Symbol M für ein chemisches Element steht, das nicht in dem Stahl enthalten ist.
  2. Anlage zum Herstellen eines nahtlosen Stahlrohrs, umfassend eine Anlage, in der ein Rohrkörper (1), der ein Zwischenprodukt eines nahtlosen Stahlrohrs ist, einem Vergüten unterzogen wird, wobei die Anlage umfasst:
    eine Einrichtung zum Vorausbestimmen auf der Grundlage der in Anspruch 1 angegebenen Gleichung (1), ob der Rohrkörper (1) aus einer Stahlsorte mit einem Ms-Punkt unter 200°C hergestellt ist oder nicht,
    einen Heizofen zum Abschrecken (2),
    einen Abschreckwassertank (3),
    ein Kühlbett (4) und einen Heizofen zum Tempern (5),
    und ein Haltebett (6), in dem der Rohrkörper (1) aus einer Stahlsorte mit einem Ms-Punkt von weniger als 200°C zusätzlich bei Raumtemperatur belassen wird, bis die Temperaturdifferenz zwischen dem Abschnitt mit der höchsten Temperatur und dem Abschnitt mit der niedrigsten Temperatur in einem Querschnitt in einer Richtung rechtwinklig zur Rohrachse geringer wird als 2,0°C, bevor die Temperbehandlung ausgeführt wird.
EP14746700.5A 2013-01-31 2014-01-22 Fertigungsverfahren und fertigungsvorrichtung für nahtlose stahlrohre mit ausgezeichneter zähigkeit Active EP2952592B1 (de)

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JP2013016459A JP5907083B2 (ja) 2013-01-31 2013-01-31 靭性に優れた継目無鋼管の製造方法及び製造設備
PCT/JP2014/000297 WO2014119251A1 (ja) 2013-01-31 2014-01-22 靭性に優れた継目無鋼管の製造方法及び製造設備

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JP5487689B2 (ja) * 2009-04-06 2014-05-07 Ｊｆｅスチール株式会社 油井管用マルテンサイト系ステンレス継目無鋼管の製造方法
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JP5907083B2 (ja) 2016-04-20
EP2952592A4 (de) 2016-04-27
EP2952592A1 (de) 2015-12-09
US20150368734A1 (en) 2015-12-24
CN104968808B (zh) 2017-11-17
WO2014119251A1 (ja) 2014-08-07
CN104968808A (zh) 2015-10-07
JP2014148699A (ja) 2014-08-21

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