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EP3559282B1 - Utilisation d'un objet en acier inoxydable duplex - Google Patents

Utilisation d'un objet en acier inoxydable duplex Download PDF

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EP3559282B1
EP3559282B1 EP17829629.9A EP17829629A EP3559282B1 EP 3559282 B1 EP3559282 B1 EP 3559282B1 EP 17829629 A EP17829629 A EP 17829629A EP 3559282 B1 EP3559282 B1 EP 3559282B1
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stainless steel
duplex stainless
solution
less
equal
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German (de)
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EP3559282A1 (fr
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Ulf KIVISÄKK
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Alleima AB
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Sandvik Materials Technology AB
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D1/26—Methods of annealing
    • 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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/58—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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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

Definitions

  • the present invention relates to a use of an object made of a duplex (ferritic-austenitic) stainless steel in sea water applications wherein this object has a surprisingly good resistance against hydrogen induced stress corrosion (HISC).
  • HISC hydrogen induced stress corrosion
  • Cathodic protection offshore for prevention of pitting corrosion of duplex and superduplex stainless steels used for subsea components on high temperature wells has been used for more than 20 years.
  • Cathodic protection is defined as an electrochemical protection by decreasing the corrosion potential to a level at which the corrosion rate of the metal is significantly reduced.
  • it is a technique to reduce corrosion of a metal surface by making that surface the cathode of an electrochemical cell.
  • the duplex stainless steel will be the cathode and another metal will be the anode (usually Zn).
  • HISC hydrogen induced stress corrosion cracking
  • JP2012140689A and JP2016053213A disclose duplex stainless steels for seawater applications.
  • duplex stainless steel used for manufacturing objects which are to be use in sea water applications, especially in applications where the duplex stainless steel will be used for cathodic protection (the duplex stainless steel will function as the cathode).
  • duplex stainless steel object has an element composition which together with the manufacturing method will provide good resistance against hydrogen induced stress corrosion (HISC).
  • HISC hydrogen induced stress corrosion
  • the use of the object comprises the use of the duplex stainless steel alloy as defined hereinabove or hereinafter in cathode protection, i.e. such as a cathode.
  • the object comprising the duplex stainless steel will have a high corrosion resistance and good structure stability.
  • the present duplex stainless steel has due to this complex optimization been found to combine several good properties, such as shown in the following disclosure.
  • the present invention provides an object of a duplex stainless steel, which object will have high corrosion resistance, high strength and toughness. Also, the object of the present invention is easy to manufacture and has good workability, which, for example enables extrusion into seamless tubes. Due to the its composition and its manufacturing process, the object will contain essentially no sigma phase (essentially no sigma phase is present). This is very advantageous as this means that the problems with corrosion, brittle fracture and nitride formation during welding are reduced and/or eliminated.
  • Solution annealing means that the object is heat treated in a temperature above the recrystallization temperature of the duplex stainless steel as defined hereinabove or hereinafter.
  • Carbon (C) is an impurity contained in duplex stainless steels.
  • the content of C exceeds 0.03 wt%, the corrosion resistance is reduced due to the precipitation of chromium carbide in the grain boundaries.
  • the content of C is less than or equal to 0.03 wt%, such as less than or equal to 0.02 wt%.
  • Si Silicon (Si) is an element which may be added for deoxidization. However, too much Si will promote the precipitation of intermetallic phases, such as sigma phase; therefore, the content of Si is 0.5 wt% or less.
  • Manganese (Mn) is used in most duplex stainless steels at levels up to about 1.0 wt%.
  • Mn has the ability to bind sulphur, which is an impurity, into MnS, which is favorable to the hot ductility.
  • the content of Mn is less than or equal to 1.0 wt%.
  • Nickel (Ni) is an austenite stabilizing element and needs to be present to achieve the desired phase balance between ferrite phase and austenite phase.
  • the content of Ni is from 6.0 to 7.0 wt%.
  • Chromium (Cr) is the most important element in a duplex stainless steel as Cr is essential for creating the passive oxide film, which will protect the duplex stainless steel from corrosion. Also, the addition of Cr will increase the solubility of nitrogen (N). If the Cr content is too low, the pitting resistance is reduced. If the Cr content is too high, the resistance against HISC is reduced. As shown in Figure 1 , a linear relation between the HISC- resistance and the equation Cr + 50N has been found meaning that the resistance against HISC within the duplex stainless steel as defined hereinabove or hereinafter is related to the content of both Cr and N. As can be seen from figure 1 , if the Cr and N are too high, then the resistance against HISC will be reduced. Accordingly, the content of Cr is from 23.0 to 24.0 wt%.
  • Molybdenum is an effective element in stabilizing the passive oxide film formed on the surface of the duplex stainless steel and is also effective in improving the stress corrosion cracking-and pitting resistance.
  • the content of Mo is less than 2.5 wt%, then the stress corrosion cracking-and pitting resistance is not high enough. If the Mo content is too high, there will be a risk for the formation of intermetallic phases which will make the material brittle. Accordingly, the content of Mo is of from 2.5 to 4.5 wt%, such as of from 2.8 to 4.0 wt%.
  • N Nitrogen
  • the content of N is of from 0.1 to 0.2 wt%, such as of from 0.12 to 0.20 wt%.
  • Phosphorus (P) is an impurity contained in the duplex stainless steel and it is well known that P will have a negative effect on the hot workability. Accordingly, the content of P is set at 0.03 wt% or less, such as 0.02 wt% or less.
  • Sulphur is an impurity contained in the duplex stainless steel, and it will deteriorate the hot workability at low temperatures. Accordingly, the allowable content of S is less than or equal to 0.03 wt%, such as less than or equal to 0.02 wt%.
  • Copper is an optional element which may or may not be included in the present duplex stainless steel depending on which scrap is used as a starting material for making the melt.
  • Cu as such may stabilize the passive film formed on the surface of the duplex stainless steel and may in low concentration improve the pitting resistance and the corrosion resistance. Therefore, the allowable content of Cu is less than or equal to 0.3 wt%, such as less than or equal to 0.2 wt%.
  • Aluminum (Al) is a deoxidizing element and may be optionally contained in the present duplex stainless steel. If the Al content is more than 0.10 wt%, the formation of intermetallic phases, such as sigma phase, will be promoted. Also, if Al is added at levels above 0.10 wt%, AlN or NiAl may be formed which will have an effect on the mechanical properties. Therefore, in order to obtain a duplex stainless steel having the properties as described hereinabove or hereinafter, the Al content is less than or equal 0.10 wt%.
  • duplex grades commonly used for these applications have a content of 25 wt% Cr and more than 0,25 wt% N.
  • Cr+50N is less than or equal to 34, such less than or equal to 33.
  • the process for manufacturing an object comprising of the duplex stainless steel as defined hereinabove or hereinafter must comprise a step of solution annealing before being used in sea water applications.
  • Solution annealing means that the object is heat treated and this step will improve the microstructure of the duplex stainless steel whereby the ductility and toughness will be increased.
  • the solution annealing should be performed at temperatures above the recrystallisation temperature of the duplex stainless steel. According to one embodiment, the solution annealing
  • the solution annealing is followed by rapid cooling in air or in water.
  • the solution annealing is performed after a cold working step, such as cold deformation, such as squeezing, bending, shearing, pilgering or drawing.
  • the microstructure of a duplex stainless steel is a two-phased structure comprising austenite islands embedded in a ferritic matrix.
  • the more closely packed austenite phase (FCC) has larger voids in the structure than the ferritic BCC structure.
  • FCC austenite phase
  • This structure will have implications for hydrogen diffusion and the hydrogen solubility.
  • the diffusion rate of hydrogen is much faster in the ferrite phase compared to austenite phase, while the solubility of hydrogen is higher in austenite phase than the ferrite phase. It has been shown that cracks due to HISC often start in the ferrite phase and that the austenite phase in many cases will act as a crack inhibitor.
  • the distribution of the two phases is balanced in the object in order to provide approximately equal amounts of ferrite phase and austenite phase in the solution-annealed condition.
  • the ferrite phase content of object is in the range of from 40% to 60 % by volume, such as in the range of from 45% to 55% by volume, balanced by the austenite phase.
  • duplex stainless steel as defined hereinabove or hereinafter for example during the manufacturing process in order to improve for example the processability, such as the hot workability, the machinability etc.
  • duplex stainless steel consist of all the elements as defined hereinabove or hereinafter in the ranges as defined hereinabove or hereinafter.
  • the balance in the duplex stainless steel is Iron (Fe) and unavoidable impurities.
  • unavoidable impurities are elements and compounds which have not been added on purpose, but cannot be fully avoided as they normally occur as impurities in e.g. the material used for manufacturing the duplex stainless steel.
  • Microstructural features such as the austenite spacing (the mean distance in the ferrite between the austenite areas) and grain size is influenced by the manufacturing method.
  • the austenite spacing can be reduced by a larger degree of hot working and/or cold working before the solution-annealing heat treatment.
  • a duplex stainless steel with smaller austenite spacing has better HISC-resistance.
  • the austenite spacing of the duplex stainless steel as defined hereinabove or hereinafter in solution-annealed condition is in the range of from 5-35 ⁇ m, such as in the range of from 5-20 ⁇ m, such as in the range of from 5-15 ⁇ m.
  • the pitting and crevice corrosion resistance of a stainless steel is primarily determined by the wt% content of Cr, Mo and N.
  • An index used to compare this resistance is the PRE (Pitting Resistance Equivalent), which is described as Cr+3.3Mo+16N.
  • the pitting corrosion resistance is dependent on the PRE value in both the ferrite phase and the austenite phase. This means that the phase with the lowest PRE value will set the limit for localized corrosion resistance of the duplex stainless steel.
  • the PRE of the duplex stainless steel according to the present invention is at least 31, such as at least 34.
  • the proof strength is the load to which a material can be deformed, without changing its dimension.
  • the proof strength (R p0.2 ) of the duplex stainless steel according to the present disclosure in solution annealed condition is in the range of from 450-700 MPa, such as in the range of from 475-650 MPa.
  • the elongation (A) of the duplex stainless steel according to the present invention in solution annealed condition is in the range of from 15-45%, such as in the range of from 20-45 %, such as in the range of from 25-45 %.
  • the duplex stainless steel object may be manufactured according to conventional methods, i.e. casting or forging, followed by hot working and cold working, solution annealing and an optional additional heat treatment.
  • the important step in the manufacturing method is the solution annealing step as this will set the final microstructure
  • the object comprised of duplex stainless steel as defined hereinabove or hereinafter is manufactured by a process comprising the following steps:
  • the duplex stainless steel object may be in the form of; a bar, a tube; a seamless or a welded tube, a constructive part, such as for example a flange and a coupling, a plate, a sheet or a strip, or a wire.
  • Table 1 shows the compositions of the duplex stainless steels used. Both inventive and comparative examples are shown below.
  • the points E1 and E2 stand for Example 1 and Example 2 of the present invention, while the points C1-C3 stands for the comparative examples 1-3.
  • Table 1 shows the compositions of the duplex stainless steels used. Both inventive and comparative examples are shown below.
  • the points E1 and E2 stand for Example 1 and Example 2 of the present invention, while the points C1-C3 stands for the comparative examples 1-3.
  • Table 1 shows the compositions of the duplex stainless steels used. Both inventive and comparative examples are shown below.
  • the points E1 and E2 stand for Example 1 and Example 2 of the present invention, while the points C1-C3 stands for the comparative examples 1-3.
  • the obtained ingots were forged to 130 x 60-70 mm billets in a hammer. Prior to forging, the ingots were heated to 1250-1280°C with a holding time of 2 hours. The forged billets were machined to 120 x 50 mm billets that were hot rolled to 10-12 mm in a Robertson rolling mill. Before hot rolling, the billets were heated to 1150°C-1220°C with a holding time of 1.5-2 hours. After the hot rolling, the billets were held at 1100°C-1120°C for 10 minutes then cooled in air to 900°C-950°C where they were quenched in oil. The duplex stainless steels billets were cold rolled to 7- 8 mm thickness and then heat treated by solution annealing at 1000-1150°C and thereafter cooled in air.
  • HISC-testing was performed at constant load with dead weight testers in a solution of 3 wt% NaCl at 4°C and subject to a cathodic protection at approximately 1050 mV SCE .
  • the testing time was 500 hours or until failure and the load correlated to the proof strength.
  • the samples were galvanostatically charged with hydrogen with a current density of 0.02 A/cm 2 .
  • the solution-annealed objects made of duplex stainless steel of the present invention have an advantageous microstructure with very good mechanical properties as well as corrosion properties. This means that objects made from said duplex stainless steel will withstand the load/stress and hydrogen ingress of hydrogen formed at the steel surface due to the cathodic protection in sea water applications. Accordingly, the duplex stainless steel objects will have increased life time, since minimization of the risk of equipment damage or any serious accidents by hydrogen induced stress corrosion will be low, if present at all.

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Claims (9)

  1. Utilisation d'un objet hypertrempé et écroui dans des applications en eau de mer constitué d'un acier inoxydable duplex composé des éléments suivants, la composition étant donnée en % en poids : C inférieur ou égal à 0,03 ; Si inférieur ou égal à 0,5 ; Mn inférieur ou égal à 1,0 ; Ni de 6,0 à 7,0 ; Cr de 23,0 à 24,0 ; Mo de 2,5 à 4,5 ; N de 0,1 à 0,2 ; P inférieur ou égal à 0,03 ; S inférieur ou égal à 0,03 ; Cu inférieur ou égal à 0,3 ; Al inférieur ou égal à 0,10 ;
    Optionnellement Ti, Ca, Ce et B selon une quantité d'au maximum 0,5 % en poids au total ;
    le reste étant du Fe et des impuretés inévitables ; où l'acier inoxydable duplex satisfait à l'équation Cr+50 ≤ 34 ;
    et où l'acier inoxydable duplex présente une teneur en phase ferritique dans la plage allant de 40 % à 60 % en volume mesurée conformément à l'ASTM E562 et une teneur en phase austénitique dans la plage allant de 40 à 60 % en volume ;
    et où l'espacement austénitique de l'acier inoxydable duplex se situe dans la plage allant de 5 à 35 µm mesuré conformément à DNV-RP-F112 ;
    et où le PRE = Cr+3,3Mo+16N de l'acier inoxydable duplex est au moins de 31 ;
    et où la limite conventionnelle d'élasticité (Rp0,2) de l'acier inoxydable duplex se situe dans la plage allant de 450 à 700 MPa ;
    et où l'allongement (A) de l'acier inoxydable duplex se situe dans la plage allant de 15 à 45 %.
  2. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon la revendication 1, où la teneur en N va de 0,12 à 0,20 % en poids.
  3. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon l'une quelconque des revendications précédentes, où la teneur en Mo va de 2,8 à 4,0 % en poids.
  4. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon l'une quelconque des revendications précédentes, où la teneur en Cu est inférieure ou égale à 0,2 % en poids.
  5. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon l'une quelconque des revendications précédentes, où l'acier inoxydable duplex satisfait à l'équation Cr+50N ≤ 33.
  6. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon l'une quelconque des revendications précédentes, où l'objet se présente sous la forme d'une barre, d'un tube, d'un tube sans soudure ou d'un tube soudé, d'une pièce de structure, d'une plaque, d'une tôle, d'une bande ou d'un fil.
  7. Utilisation d'un objet hypertrempé et écroui constitué d'acier inoxydable duplex selon l'une quelconque des revendications précédentes, où l'objet est fabriqué via le procédé comprenant les étapes suivantes :
    a. fusion ;
    b. coulage ;
    c. formage à chaud ;
    d. écrouissage ;
    e. hypertrempe et où l'hypertrempe est réalisée à une température supérieure à la température de recristallisation dudit acier inoxydable duplex.
  8. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon la revendication 7, où l'hypertrempe est réalisée à une température se situant dans la plage allant de 1030 à 1150 °C.
  9. Utilisation d'un objet hypertrempé et écroui constitué d'un acier inoxydable duplex selon l'une quelconque des revendications précédentes, où l'utilisation dans une application en eau de mer est à titre de cathode.
EP17829629.9A 2016-12-21 2017-12-18 Utilisation d'un objet en acier inoxydable duplex Active EP3559282B1 (fr)

Applications Claiming Priority (2)

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EP16205946 2016-12-21
PCT/EP2017/083410 WO2018114867A1 (fr) 2016-12-21 2017-12-18 Utilisation d'un objet en acier inoxydable duplex

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EP3559282B1 true EP3559282B1 (fr) 2022-03-09

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EP (1) EP3559282B1 (fr)
JP (1) JP7144418B2 (fr)
KR (1) KR20190099232A (fr)
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WO (1) WO2018114867A1 (fr)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA3192493A1 (fr) * 2020-08-21 2022-02-24 Jarvis B. Jenkins Recipient, regulateur et appareil de stockage de fluides portables
EP4234739A4 (fr) * 2020-10-23 2025-07-30 Nippon Steel Corp Joint soudé en acier inoxydable à deux phases
CN114107827B (zh) * 2021-12-08 2022-10-14 福州大学 一种3d打印用双相不锈钢粉末及其制备和打印方法
JP2023118656A (ja) * 2022-02-15 2023-08-25 日鉄ステンレス株式会社 二相ステンレス鋼および二相ステンレス鋼の製造方法
CN116024503B (zh) * 2022-12-09 2024-07-05 东北大学 一种具有高强度的节镍型双相不锈钢丝及其制备方法
CN118166291B (zh) * 2024-03-14 2025-09-23 山西太钢不锈钢股份有限公司 双相不锈钢、双相不锈钢管坯及其在油气开采中的应用

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3779043B2 (ja) * 1997-07-30 2006-05-24 株式会社日本製鋼所 二相ステンレス鋼
SE527175C2 (sv) * 2003-03-02 2006-01-17 Sandvik Intellectual Property Duplex rostfri ställegering och dess användning
SE527178C2 (sv) * 2003-03-02 2006-01-17 Sandvik Intellectual Property Användning av en duplex rostfri stållegering
JP2005194624A (ja) 2003-12-08 2005-07-21 Sumitomo Chemical Co Ltd 二相系ステンレス鋼製機器の防食方法
SE530711C2 (sv) * 2006-10-30 2008-08-19 Sandvik Intellectual Property Duplex rostfri stållegering samt användning av denna legering
JP5288980B2 (ja) * 2008-10-02 2013-09-11 新日鐵住金ステンレス株式会社 衝撃靭性に優れた二相ステンレス熱間圧延鋼材とその製造方法
FI121340B (fi) * 2008-12-19 2010-10-15 Outokumpu Oy Dupleksinen ruostumaton teräs
JP5726537B2 (ja) * 2011-01-06 2015-06-03 山陽特殊製鋼株式会社 靭性に優れた二相系ステンレス鋼
JP5717479B2 (ja) * 2011-03-14 2015-05-13 新日鐵住金ステンレス株式会社 耐応力腐食割れに優れる高強度高耐食性ステンレス鋼ボルトおよびその製造方法
JP5777387B2 (ja) 2011-04-19 2015-09-09 日本冶金工業株式会社 二相ステンレス鋼の光輝焼鈍方法
FI125854B (fi) * 2011-11-04 2016-03-15 Outokumpu Oy Dupleksi ruostumaton teräs
JP5803890B2 (ja) 2012-12-07 2015-11-04 Ｊｆｅスチール株式会社 耐孔食性に優れた二相ステンレスクラッド鋼の合せ材及びそれを用いた二相ステンレスクラッド鋼並びにその製造方法
JP5890330B2 (ja) * 2013-01-15 2016-03-22 株式会社神戸製鋼所 二相ステンレス鋼材および二相ステンレス鋼管
EP2947169A4 (fr) * 2013-01-15 2016-12-21 Kobe Steel Ltd Matière d'acier inoxydable duplex et tuyau d'acier inoxydable duplex
FI125734B (en) * 2013-06-13 2016-01-29 Outokumpu Oy Duplex ferritic austenitic stainless steel
JP6023029B2 (ja) 2013-09-25 2016-11-09 株式会社日立製作所 電気防食システムおよびそれを備えたポンプ装置
WO2015064128A1 (fr) * 2013-10-31 2015-05-07 Ｊｆｅスチール株式会社 Acier inoxydable à deux phases ferrite-martensite présentant une résilience aux basses températures, et son procédé de production
WO2015169572A1 (fr) * 2014-05-06 2015-11-12 Nv Bekaert Sa Filet d'aquaculture muni de fils d'acier revêtus
JP6482074B2 (ja) * 2014-09-02 2019-03-13 日本冶金工業株式会社 二相ステンレス鋼板とその製造方法
CN105624580B (zh) * 2016-03-07 2017-11-03 江苏科技大学 一种双相不锈钢丝及其制备方法

Non-Patent Citations (1)

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

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Publication number Publication date
CN110088305B (zh) 2021-05-14
EP3559282A1 (fr) 2019-10-30
WO2018114867A1 (fr) 2018-06-28
CA3045542A1 (fr) 2018-06-28
JP7144418B2 (ja) 2022-09-29
JP2020509201A (ja) 2020-03-26
KR20190099232A (ko) 2019-08-26
CN110088305A (zh) 2019-08-02
US20190376156A1 (en) 2019-12-12

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