[go: up one dir, main page]

EP2889390B1 - Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion - Google Patents

Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion Download PDF

Info

Publication number
EP2889390B1
EP2889390B1 EP13830674.1A EP13830674A EP2889390B1 EP 2889390 B1 EP2889390 B1 EP 2889390B1 EP 13830674 A EP13830674 A EP 13830674A EP 2889390 B1 EP2889390 B1 EP 2889390B1
Authority
EP
European Patent Office
Prior art keywords
equal
steel
stainless steel
martensitic stainless
less
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP13830674.1A
Other languages
German (de)
English (en)
Other versions
EP2889390A4 (fr
EP2889390A1 (fr
Inventor
Shuji Hashizume
Tomomi Taniguchi
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
NKKTubes KK
Original Assignee
NKKTubes KK
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by NKKTubes KK filed Critical NKKTubes KK
Publication of EP2889390A1 publication Critical patent/EP2889390A1/fr
Publication of EP2889390A4 publication Critical patent/EP2889390A4/fr
Application granted granted Critical
Publication of EP2889390B1 publication Critical patent/EP2889390B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Definitions

  • the present invention relates to a martensitic stainless steel having a high strength, a high toughness, and a high corrosion resistance, particularly relates to martensitic stainless steel with a high strength, high toughness, and high corrosion resistance suitable for use in an environment containing a high temperature humid carbon dioxide gas in drilling for and transporting petroleum and natural gas, and to a method of producing the same.
  • the conventional martensitic stainless steel is excellent in a corrosion resistance against a humid carbon dioxide gas (hereinafter, referred to as "corrosion resistance") up to 180 °C, the corrosion resistance is not sufficient at temperatures of higher than 180 °C.
  • a steel pipe or the like used in drilling for or transporting petroleum or natural gas is placed under a high temperature and a high pressure environment, and therefore, it is also preferable that the steel pipe has a high strength as well as an excellent toughness.
  • Patent Literatures 1 to 7 disclose such stainless steels exhibiting corrosion resistances at temperatures of equal to or higher than about 180 °C.
  • a basic concept of the stainless steels disclosed in the literatures is that a corrosion resistance is maintained under an environment of a high temperature and humid dioxide gas by increasing an amount of Cr.
  • Patent Literatures 1 and 2 disclose high strength-stainless steel pipes for an oil well having C, Si, Mn, Cr, Ni, Mo, W, Cu, V, and N in specific compositions.
  • Patent Literature 1 produced a stainless steel having a strength up to 792 MPa in a yield stress, and investigated a toughness or the like thereof.
  • Patent Literature 2 no description is found concerning a strength, and only a toughness was investigated. An investigation concerning a higher strength stainless steel was not carried out in either of Patent Literatures 1 and 2.
  • Patent Literatures 3 to 7 Although there were examples investigating high strength steels which are equivalent to or higher than those of Patent Literatures 1 and 2, investigations concerning toughness thereof were not carried out. Generally, a stainless steel pipe is deteriorated in a toughness thereof by making a strength thereof higher. Therefore, it seems that the toughness of the stainless steels disclosed in the literatures cannot withstand completely drilling for or transportation of petroleum or natural gas.
  • GB 1 294 336 is concerned with a martensitic stainless steel alloy having the following composition: Carbon 0.2 maximum Manganese 3.5 maximum Silicon 2.5 maximum Phosphorus 0.05 maximum Sulfur 0.5 maximum Selenium 0.5 maximum Chromium 13.5 to 17 Nickel 4 to 9 Molybdenum 0.5 to 3 Copper 0.75 to 3 Columbium up to 10 ⁇ C Titanium up to 5 ⁇ C Cobalt 6 maximum Boron 0.01 maximum Zirconium up to 1 in total Vanadium Tantalum
  • JP H03-075336 A a martensitic stainless steel is described, which contains C, Si, Mn, Cr, Ni, Al and N.
  • the martensitic stainless steel is formed from a composition, in which C is reduced, by weight, to ⁇ 0.03%. Further components are ⁇ 1% Si, ⁇ 2% Mn, > 15 to 18% Cr, 1 to 5% Ni, 0.005 to 0.2% Al, 0.03 to 0.15% N and the balance Fe with impurities.
  • the steel having the above componental composition is austenitized at 900 to 1100°C, is thereafter cooled to form martensite and is then subjected to tempering treatment at 560°C to the Ac1 temperature or below. Next, the steel, after subjected to the tempering treatment, is cooled at a cooling rate of more than that in air cooling.
  • an environment encountered by a steel pipe particularly, an oil well pipe has been severer and severer, and there is a necessity for a steel pipe having a high strength of equal to or higher than 758 MPa, exhibiting an excellent corrosion resistance against a humid dioxide gas at temperatures of equal to or higher than 180 °C, and also being excellent in a toughness.
  • an aimed performance is set as follows in view of a performance requested for a steel pipe for drilling for or transportation of petroleum or natural gas including a carbon dioxide gas.
  • a steel pipe although a main object of the present invention is an oil well pipe, also a steel pipe for a line pipe for transportation for which a similar performance is requested can be an object.
  • the present inventors have acquired the following knowledge as a result of carrying out an intensive research in order to solve the problem described above.
  • a martensitic stainless steel containing a pertinent amount of V in the stainless steel, and further containing simultaneously a pertinent amount of Ta as an indispensable component is easy to disperse a precipitate of a fine carbide into a matrix of the stainless steel after a heat treatment as compared with a case of individually adding V or Ta or a case of simultaneously adding V and Nb, and the enhancement of strength while maintaining a toughness is facilitated. Also, the present inventors have found that its effect is more significant by further adding Nb in addition to V and Ta.
  • the present inventors have completed a novel martensitic stainless steel having a high toughness and a high strength and being excellent in a corrosion resistance under an environment at temperatures of equal to or higher than 180 °C and its production method, which martensitic stainless was not realized in the conventional martensitic stainless steel.
  • the martensitic stainless steel has been attained by making the steel contain certain amounts of V and Ta, or V, Ta, and Nb, adjusting a heat treatment condition in a certain range in order to stably acquire a strength of equal to or higher than 758 MPa in a constant range, and making the carbide precipitate to disperse uniformly in the matrix in consideration of a restriction of a metallographic structure described above.
  • the present invention provides a martensitic stainless steel having a high strength of equal to or higher than 758 MPa which can be used under a humid carbon dioxide gas environment at temperatures of equal to or higher than 180 °C while maintaining a toughness thereof, by improving a corrosion resistance of the conventional high strength-martensitic stainless steel by limiting an alloy composition and a production condition in certain ranges.
  • the present invention is as follows.
  • martensitic stainless steel with a high strength, high toughness, and high corrosion resistance which is excellent in a toughness, and in which a corrosion resistance is good against carbon dioxide gas corrosion under an environment at a temperature of equal to or higher than 180 °C, can be obtained by specifying an alloy composition and a production condition.
  • a content of each alloy element in the steel is a value based on a mass in which a total of the steel is 100 % unless specified otherwise.
  • C is a strong austenite forming element, and an element which is indispensable also for achieving a high strength in a stainless steel.
  • C is bonded with Cr and is precipitated as a carbide thereof, which deteriorates a corrosion resistance and a toughness of the steel.
  • a content of C is less than 0.005 %, a sufficient strength is not achieved, and when the content of C exceeds 0.05 %, the deterioration becomes significant, and therefore, the content is set at 0.005 to 0.05 %.
  • Si is an element which is necessary as a deoxidizer
  • Si is also a strong ferrite forming element.
  • an upper limit of the content is set at 1.0 %, preferably 0.5 %, further preferably 0.3 %.
  • Mn is effective as a deoxidizer and a desulfurizing agent. However, Mn reduces a corrosion resistance of the stainless steel, and therefore, an upper limit of the content is set at 2.0 %, preferably 0.5 %, further preferably 0.3 %.
  • Cr is a basic element constituting the martensitic stainless steel, and is an important element which manifests a corrosion resistance.
  • the corrosion resistance is taken into consideration under a severe environment at temperatures of equal to or higher than 180 °C, when the content is less than 16 %, a sufficient corrosion resistance is not achieved, when the content exceeds 18 %, its effect is saturated, and a problem is posed in view of economy, and therefore, the content is set at 16 to 18 %.
  • Ni is an element which enhances a corrosion resistance of a stainless steel and is extremely effective for stabilizing austenite.
  • the content thereof is less than 2.5 %, its effect is not sufficiently achieved and on the other hand, when the content is increased, a transformation temperature (Ac1 point) of martensite is lowered, restricting a tempering temperature in producing the martensitic stainless steel of the present invention.
  • the content of Ni is set at 2.5 to 6.5 %.
  • Mo is an element which is particularly effective for enhancing a corrosion resistance of the stainless steel.
  • the content thereof is less than 1.5 %, its effect is not exhibited, and when the content exceeds 3.5 %, it is difficult to control ferrite, and therefore, the content is set at 1.5 to 3.5 %.
  • V is a strong carbide forming element and contributes to increase the strength of the steel by making a crystal grain of carbide fine by uniformly precipitating the fine carbide within a matrix grain of the stainless steel and preventing the fine carbide from being precipitated preferentially on a grain boundary.
  • the carbide is precipitated finely and uniformly in this way, and therefore, an increase in the strength is achieved without lowering the toughness of the steel.
  • the content of V is less than 0.01 %, the effect of increasing the strength is not exhibited, when the content exceeds 0.08 %, the effect is saturated, and therefore, the content is set at 0.01 to 0.08 %, preferably 0.02 to 0.04 %.
  • Acid soluble Al (Sol.Al) is added for deoxidizing the stainless steel in a refining step and for enhancing the toughness of the steel by making a y grain fine through precipitation of AlN.
  • the content thereof is less than 0.005 %, a toughness enhancing effect is not achieved, on the contrary, when the content exceeds 0.10 %, the toughness may be reduced, and therefore, the content is set at 0.005 to 0.10%.
  • ⁇ N equal to or less than 0.05 %>
  • N is an element which is harmful in enhancing the corrosion resistance of the stainless steel, and is also an austenite forming element.
  • N is contained in an amount of exceeding 0.05 %, N is precipitated as a nitride in tempering when the martensitic stainless steel of the present invention is produced, and the corrosion resistance and the toughness of the steel are deteriorated, and therefore, an upper limit of the content is set at 0.05 %, preferably 0.02 %.
  • Ta is a strong carbide forming element and contributes to increase the strength of the steel by uniformly precipitating a fine carbide of Ta within a matrix grain of the stainless steel.
  • the fine carbide is uniformly precipitated, and therefore, an increase in the strength can be achieved without reducing the toughness of the steel.
  • by adding a certain amount of Ta along with V described above higher strength and toughness can be achieved than those in a case of adding either one of Ta and V.
  • the content of Ta is less than 0.01 %, an effect of enhancing the strength is not exhibited, when the content exceeds 0.06 %, its effect is generally saturated, and the addition is not preferable also in view of cost. Therefore, the content is set at 0.01 to 0.06%.
  • Nb may be included other than the basic components described above.
  • Nb is a strong carbide forming element and increases the strength of the stainless steel by making the crystal grain fine through precipitation of the fine carbide of Nb.
  • the content thereof exceeds 0.1 %, its effect is saturated, and therefore, the content is set equal to or less than 0.1 %, preferably equal to or less than 0.05 %.
  • the balance other than the components explained above consists of Fe and inevitable impurities.
  • inevitable impurities represented by P, S, and O when an amount of P is equal to or less than 0.04 % and that of S is equal to or less than 0.01 %, no hindrance is configured in producing a seamless steel pipe or an electric resistance welded steel pipe with a hot-rolled steel plate as a material thereof which is considered to embody the present invention.
  • all of the impurities are elements deteriorating the hot workability of the steel, and the smaller the contents, the more preferable it is.
  • inevitable impurities of O and the like the lower the content, the more preferable it is.
  • a martensitic stainless steel of 758 MPa or higher which can be used in a humid carbon dioxide gas environment at temperatures of equal to or higher than 180 °C while maintaining the toughness can be obtained by improving the corrosion resistance of the conventional high strength-martensitic stainless steel by adjusting the stainless steel used in the present invention to have the composition component range described above.
  • a 0.2 % proof stress of the martensitic stainless steel of the present invention is equal to or higher than 758 MPa and equal to or lower than 965 MPa
  • an absorbed energy thereof in a Charpy full size test at -20 °C is equal to or higher than 100 J, preferably, equal to or higher than 200 J
  • a corrosion rate thereof under an environment of a 20 % NaCl aqueous solution, 220 °C, and 10 atmospheric pressure-CO 2 is equal to or lower than 0.5 mm/year, preferably, equal to or lower than 0.3 mm/year.
  • the 0.2 % proof stress exceeds 965 MPa, in a case where a small amount of hydrogen is included in the stainless steel by corrosion or the like, a crack is liable to be brought about in the steel.
  • a pertinent strength, a high toughness, and a high corrosion resistance which can withstand the use in a severe environment are achieved by executing prescribed production conditions with a composition of the stainless steel as the metal composition described above.
  • the martensitic stainless steel of the present invention can be produced by the following production method.
  • the martensitic stainless steel with the component composition adjusted to the range described above is melted by a converter or an electric furnace and is made into a bloom, a slab or a billet by an ordinary ingot casting method followed by blooming or slabbing or a continuous casting method.
  • the bloom, slab or billet is subjected to hot working, and is provided with a prescribed shape of a seamless steel pipe or a steel plate as needed (in the martensitic stainless steel under this state, a strength, a toughness and the like aimed by the present invention are not achieved).
  • the hot-worked steel is heated at a temperature of equal to or higher than 800 °C, and equal to or lower than 980 °C to form austenite, successively quenched and cooled to a temperature of equal to or lower than 100 °C, and successively tempered at a temperature of equal to or higher than 500 °C and equal to or lower than 700 °C.
  • a description will be given of heating temperatures in quenching and tempering operations as follows.
  • the heating temperature is less than 800 °C, austenite is not formed in the stainless steel, an effect of quenching is not achieved, and therefore, a lower limit of the heating temperature is set at 800 °C.
  • a lower limit of the heating temperature is set at 800 °C.
  • an upper limit of the heating temperature is set at 980 °C.
  • tempering temperature equal to or higher than 500 °C and equal to or lower than 700 °C>
  • a tempering treatment is generally a treatment which is carried out for providing a toughness to a steel. According to the present invention, in addition to the provision of the toughness, this is a step indispensable for enhancing strength of a stainless steel by uniformly dispersing and precipitating fine carbides of V and Ta. However, when a tempering temperature exceeds 700 °C, a 0.2 % proof stress of equal to or higher than 758 MPa is not achieved, and therefore, an upper limit of the tempering temperature is set at 700 °C.
  • the tempering temperature is lower than 500 °C, the precipitation of the carbide is not sufficient, the aimed 0.2 % proof stress and the aimed toughness are not achieved, and therefore, a lower limit of the tempering temperature is set at 500 °C.
  • the present inventors produced martensitic stainless steels by melting invented steels N1 to N8 and comparative steels C1 to C5 having chemical compositions shown in Table 1 described below as test steels (martensitic stainless steels), producing steel plates having a thickness of 12 mm by hot rolling, thereafter, carrying out heat treatments (quenching and tempering treatments) shown in Table 2 described below.
  • the steel plates were cooled down to room temperature by water after the quenching heat treatment, thereafter, subjected to a tempering heat treatment.
  • the comparative steels C1 and C5 are steels which do not include Ta.
  • the comparative steel C2 is a steel in which a content of V does not reach the lower limit of the present invention
  • the comparative steel C3 is a steel in which contents of Cr and Mo do not reach the lower limits of the present invention
  • the comparative steel C4 is a steel in which a content of Ta exceeds the upper limit value of the present invention.
  • Table 3 described below shows a test result of the mechanical properties and the corrosion resistance.
  • C1 and C5 are steels which do not include Ta
  • C2 is a steel in which the V content does not reach the lower limit of the present invention
  • C3 is a steel in which Cr and Mo contents do not reach the lower limits of the present invention
  • C4 is a steel in which the Ta content exceeds the upper limit value of the present invention.
  • any of the components are deviated from the ranges of the present invention, and therefore, as for results thereof, the aimed 0.2 % proof stress, toughness or corrosion resistance are not achieved.
  • the strength of 758 MPa class could not be achieved, and also concerning the toughness and the corrosion resistance, target values could not be achieved.
  • the martensitic stainless steel of the present invention has the corrosion resistance, maintains the toughness despite the high strength equal to or higher than 758 MPa, can be used in the humid carbon dioxide gas environment at temperatures equal to or higher than 180 °C, and can preferably be applied as a steel pipe for drilling for or transporting petroleum or natural gas including the carbon dioxide gas (martensitic stainless steel pipe for an oil well or a gas well or a line pipe).

Landscapes

  • 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 Steel (AREA)

Claims (4)

  1. Acier inoxydable martensitique constitué de, en % en masse, C : 0,005 % à 0,05 %, Si : inférieur ou égal à 1,0 %, Mn : inférieur ou égal à 2,0 %, Cr: 16 à 18%, Ni : 2,5 à 6,5 %, Mo : 1,5 à 3,5 %, W : inférieur ou égal à 3,5 %, Cu : inférieur ou égal à 3,5 %, V: 0,01 à 0,08 %, Sol.Al : 0,005 à 0,10 %, N : inférieur ou égal à 0,05 %, Ta : 0,01 à 0,06%, et facultativement Nb : inférieur ou égal à 0,1%, le reste étant Fe avec des impuretés inévitables.
  2. Acier inoxydable martensitique selon la revendication 1, dans lequel une limite élastique conventionnelle à 0,2 % de celui-ci est supérieure ou égale à 758 MPa et inférieure ou égale à 965 MPa, une énergie absorbée de celui-ci dans un test en taille réelle de Charpy à -20 °C est supérieure ou égale à 100 J, et un taux de corrosion de celui-ci dans un environnement d'une solution aqueuse de NaCl à 20 %, 220 °C, CO2 à 10 pressions atmosphériques est inférieur ou égal à 0,5 mm/an.
  3. Tuyau en acier inoxydable martensitique pour un puits de pétrole, un puits de gaz, ou un tuyau de canalisation comprenant l'acier inoxydable martensitique selon la revendication 1 ou 2.
  4. Procédé de production d'un acier inoxydable martensitique comprenant les étapes suivantes :
    la soumission de l'acier inoxydable martensitique ayant une composition telle que définie dans la revendication 1 à un travail à chaud,
    ensuite la formation d'austénite dans l'acier à une température supérieure ou égale à 800 °C et inférieure ou égale à 980 °C et successivement la trempe et le refroidissement de l'acier à une température inférieure ou égale à 100 °C,
    suivie par le revenu de l'acier à une température supérieure ou égale à 500 °C et inférieure ou égale à 700 °C.
EP13830674.1A 2012-08-24 2013-04-24 Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion Active EP2889390B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2012184802A JP6045256B2 (ja) 2012-08-24 2012-08-24 高強度高靭性高耐食マルテンサイト系ステンレス鋼
PCT/JP2013/062004 WO2014030392A1 (fr) 2012-08-24 2013-04-24 Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion

Publications (3)

Publication Number Publication Date
EP2889390A1 EP2889390A1 (fr) 2015-07-01
EP2889390A4 EP2889390A4 (fr) 2016-05-11
EP2889390B1 true EP2889390B1 (fr) 2018-04-18

Family

ID=50149711

Family Applications (1)

Application Number Title Priority Date Filing Date
EP13830674.1A Active EP2889390B1 (fr) 2012-08-24 2013-04-24 Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion

Country Status (5)

Country Link
US (2) US20150191809A1 (fr)
EP (1) EP2889390B1 (fr)
JP (1) JP6045256B2 (fr)
BR (1) BR112015003178B1 (fr)
WO (1) WO2014030392A1 (fr)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013119980A1 (fr) * 2012-02-08 2013-08-15 Chevron U.S.A. Inc. Équipement utilisable dans des environnements corrosifs et ses procédés de fabrication
JP6237873B2 (ja) * 2014-11-19 2017-11-29 Ｊｆｅスチール株式会社 油井用高強度ステンレス継目無鋼管
EP3404120B1 (fr) 2016-01-13 2020-03-04 Nippon Steel Corporation Procédé de fabrication de tuyau en acier inoxydable pour puits de pétrole et tuyau en acier inoxydable pour puits de pétrole
DE112016006874T5 (de) * 2016-12-27 2019-02-14 Honda Motor Co., Ltd. Nichtrostender Stahl
CN110408854B (zh) * 2019-08-14 2020-10-20 王平 一种贝氏体不锈钢及其制备方法
US12497676B2 (en) 2019-10-01 2025-12-16 Jfe Steel Corporation Stainless steel seamless pipe and method for manufacturing same
US12291766B2 (en) 2019-10-01 2025-05-06 Jfe Steel Corporation Stainless steel seamless pipe and method for manufacturing same
MX2022011506A (es) * 2020-03-19 2022-10-07 Jfe Steel Corp Tubo de acero inoxidable sin soldadura y metodo para fabricar un tubo de acero inoxidable sin soldadura.
MX2022012713A (es) 2020-04-13 2022-11-07 Nippon Steel Corp Material de acero inoxidable martensitico y metodo para producir material de acero inoxidable martensitico.
CN118464558B (zh) * 2024-05-09 2025-03-25 天津大学 饱氧液态铅铋环境下稳定获得铁素体马氏体钢脆化的方法

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3574601A (en) * 1968-11-27 1971-04-13 Carpenter Technology Corp Corrosion resistant alloy
AT345322B (de) * 1970-10-23 1978-09-11 Suedwestfalen Ag Stahlwerke Verfahren zur herstellung verbesserter, martensitischer chromstaehle mit guter duktilitaet
US5939018A (en) * 1984-10-10 1999-08-17 Kawasaki Steel Corporation Martensitic stainless steels for seamless steel pipe
JP2826819B2 (ja) * 1987-02-27 1998-11-18 日新製鋼株式会社 加工性に優れ溶接軟化のない高強度ステンレス鋼材の製造方法
JP2814528B2 (ja) 1989-03-15 1998-10-22 住友金属工業株式会社 油井用マルテンサイト系ステンレス鋼材とその製造方法
JP2791804B2 (ja) * 1989-08-16 1998-08-27 新日本製鐵株式会社 高強度かつ耐食性の優れたマルテンサイト系ステンレス鋼
JP2742949B2 (ja) * 1989-08-16 1998-04-22 新日本製鐵株式会社 耐食性の優れたマルテンサイト系ステンレス鋼およびその製造方法
JP2742948B2 (ja) * 1989-08-16 1998-04-22 新日本製鐵株式会社 耐食性の優れたマルテンサイト系ステンレス鋼およびその製造方法
US5496421A (en) * 1993-10-22 1996-03-05 Nkk Corporation High-strength martensitic stainless steel and method for making the same
JP3539250B2 (ja) * 1998-12-09 2004-07-07 Ｊｆｅスチール株式会社 高耐応力腐食割れ性を有する６５５Ｎｍｍ−２級低Ｃ高Ｃｒ合金油井管およびその製造方法
US20020164261A1 (en) * 2001-03-02 2002-11-07 Martin James W. Cast shaped article made from high strength, precipitation-hardenable stainless steel and a process for making same
US6743305B2 (en) * 2001-10-23 2004-06-01 General Electric Company High-strength high-toughness precipitation-hardened steel
US6890393B2 (en) * 2003-02-07 2005-05-10 Advanced Steel Technology, Llc Fine-grained martensitic stainless steel and method thereof
CN1891846A (zh) * 2005-07-05 2007-01-10 住友金属工业株式会社 马氏体不锈钢
JP4893196B2 (ja) * 2006-09-28 2012-03-07 Ｊｆｅスチール株式会社 高靭性でかつ耐食性に優れた油井用高強度ステンレス鋼管
MX2010010435A (es) 2008-03-28 2010-11-05 Sumitomo Metal Ind Acero inoxidable usado para material tubular destinado a pozos petroleros.
AR073884A1 (es) 2008-10-30 2010-12-09 Sumitomo Metal Ind Tubo de acero inoxidable de alta resistencia excelente en resistencia a la fisuracion bajo tension por sulfuros y a la corrosion de gas de acido carbonico en alta temperatura.
JP5446335B2 (ja) 2009-03-10 2014-03-19 Ｊｆｅスチール株式会社 油井用高強度ステンレス鋼管の評価方法
AR076669A1 (es) * 2009-05-18 2011-06-29 Sumitomo Metal Ind Acero inoxidable para pozos de petroleo, tubo de acero inoxidable para pozos de petroleo, y metodo de fabricacion de acero inoxidable para pozos de petroleo
EP2565287B1 (fr) * 2010-04-28 2020-01-15 Nippon Steel Corporation Acier inoxydable haute résistance pour puits de pétrole et tube d'acier inoxydable haute résistance pour puits de pétrole

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
JP2014043595A (ja) 2014-03-13
EP2889390A4 (fr) 2016-05-11
US20180002791A1 (en) 2018-01-04
WO2014030392A1 (fr) 2014-02-27
BR112015003178A2 (pt) 2018-05-22
EP2889390A1 (fr) 2015-07-01
US20150191809A1 (en) 2015-07-09
BR112015003178B1 (pt) 2019-04-24
JP6045256B2 (ja) 2016-12-14

Similar Documents

Publication Publication Date Title
EP2889390B1 (fr) Acier inoxydable martensitique à haute résistance, haute ténacité et haute résistance à la corrosion
EP2918697B1 (fr) Tuyau sans soudure en acier inoxydable hautement résistant pour puits de pétrole, et procédé de fabrication de celui-ci
EP2341161B1 (fr) Tuyau en acier inoxydable à haute limite élastique présentant une résistance élevée à la corrosion fissurante en présence d'hydrogène sulfuré et une résistance à la corrosion en présence de dioxyde de carbone à haute température
US10240221B2 (en) Stainless steel seamless pipe for oil well use and method for manufacturing the same
US10597760B2 (en) High-strength steel material for oil well and oil well pipes
JP5924256B2 (ja) 耐食性に優れた油井用高強度ステンレス鋼継目無管およびその製造方法
EP3219820B1 (fr) Tôle d'acier à base d'alliage à base de nickel et son procédé de fabrication
EP2520684B1 (fr) Matériau d'acier austénitique à ductilité supérieure
EP3202938B1 (fr) Acier de haute résistance pour puits de pétrole, et conduit de puits de pétrole
EP3287536B1 (fr) Acier inoxydable martensitique
JP5499575B2 (ja) 油井管用マルテンサイト系ステンレス継目無鋼管およびその製造方法
CN111479945A (zh) 具有优秀硬度和冲击韧性的耐磨损钢及其制造方法
EP3722448B1 (fr) Acier riche en mn, et procédé de fabrication de celui-ci
EP1873270B1 (fr) Acier faiblement allié
KR101301617B1 (ko) 고강도 고인성 소재 및 이를 이용한 타워 플랜지 제조방법
EP4389921A1 (fr) Matériau en acier inoxydable martensitique pour environnement hydrogène gazeux et son procédé de fabrication
EP3889302A1 (fr) Tôle d'acier chrome-molybdène présentant une excellente résistance au fluage et son procédé de fabrication
JP5793556B2 (ja) 高耐食性を有する８６２ＭＰａ級低Ｃ高Ｃｒ鋼管及びその製造方法
EP4414463A1 (fr) Tuyau en acier inoxydable sans soudure à haute résistance pour puits de pétrole
US20100096048A1 (en) 655 mpa grade martensitic stainless steel having high toughness and method for manufacturing the same
KR102326684B1 (ko) 크리프 강도와 고온 연성이 우수한 크롬강판 및 그 제조방법

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20150224

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAX Request for extension of the european patent (deleted)
RA4 Supplementary search report drawn up and despatched (corrected)

Effective date: 20160413

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 8/00 20060101ALI20160407BHEP

Ipc: C21D 9/08 20060101ALI20160407BHEP

Ipc: C22C 38/48 20060101ALI20160407BHEP

Ipc: C22C 38/46 20060101ALI20160407BHEP

Ipc: C21D 8/02 20060101ALI20160407BHEP

Ipc: C22C 38/44 20060101ALI20160407BHEP

Ipc: C22C 38/02 20060101ALI20160407BHEP

Ipc: C22C 38/06 20060101ALI20160407BHEP

Ipc: C22C 38/04 20060101ALI20160407BHEP

Ipc: C21D 6/00 20060101ALI20160407BHEP

Ipc: C22C 38/42 20060101ALI20160407BHEP

Ipc: C22C 38/00 20060101AFI20160407BHEP

Ipc: C22C 38/58 20060101ALI20160407BHEP

R17P Request for examination filed (corrected)

Effective date: 20150224

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/48 20060101ALI20171127BHEP

Ipc: C22C 38/46 20060101ALI20171127BHEP

Ipc: C21D 8/00 20060101ALI20171127BHEP

Ipc: C22C 38/06 20060101ALI20171127BHEP

Ipc: C22C 38/00 20060101AFI20171127BHEP

Ipc: C21D 6/00 20060101ALI20171127BHEP

Ipc: C22C 38/04 20060101ALI20171127BHEP

Ipc: C22C 38/44 20060101ALI20171127BHEP

Ipc: C22C 38/02 20060101ALI20171127BHEP

Ipc: C21D 8/02 20060101ALI20171127BHEP

Ipc: C22C 38/42 20060101ALI20171127BHEP

Ipc: C21D 9/08 20060101ALI20171127BHEP

Ipc: C22C 38/58 20060101ALI20171127BHEP

INTG Intention to grant announced

Effective date: 20180103

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 6

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 990551

Country of ref document: AT

Kind code of ref document: T

Effective date: 20180515

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602013036212

Country of ref document: DE

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20180418

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180718

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180718

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180719

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 990551

Country of ref document: AT

Kind code of ref document: T

Effective date: 20180418

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20180430

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180820

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602013036212

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180424

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180430

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180430

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180430

26N No opposition filed

Effective date: 20190121

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180424

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180424

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20180418

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180418

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20130424

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20180818

REG Reference to a national code

Ref country code: DE

Ref legal event code: R081

Ref document number: 602013036212

Country of ref document: DE

Owner name: TENARIS CONNECTIONS B.V., NL

Free format text: FORMER OWNER: NKK TUBES, KAWASAKI-SHI, KANAGAWA, JP

Ref country code: DE

Ref legal event code: R081

Ref document number: 602013036212

Country of ref document: DE

Owner name: JFE STEEL CORPORATION, JP

Free format text: FORMER OWNER: NKK TUBES, KAWASAKI-SHI, KANAGAWA, JP

REG Reference to a national code

Ref country code: GB

Ref legal event code: 732E

Free format text: REGISTERED BETWEEN 20230427 AND 20230503

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230527

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20250319

Year of fee payment: 13

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20250319

Year of fee payment: 13

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20250319

Year of fee payment: 13