EP3559282A1 - Use of a duplex stainless steel object - Google Patents

Use of a duplex stainless steel object

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Publication number
EP3559282A1
EP3559282A1 EP17829629.9A EP17829629A EP3559282A1 EP 3559282 A1 EP3559282 A1 EP 3559282A1 EP 17829629 A EP17829629 A EP 17829629A EP 3559282 A1 EP3559282 A1 EP 3559282A1
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EP
European Patent Office
Prior art keywords
stainless steel
duplex stainless
solution
less
equal
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.)
Granted
Application number
EP17829629.9A
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German (de)
French (fr)
Other versions
EP3559282B1 (en
Inventor
Ulf KIVISÄKK
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Alleima AB
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Sandvik Intellectual Property 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
    • 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
    • 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

Definitions

  • the present disclosure 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
  • 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-austenitic stainless steel which object is to be used in sea water applications.
  • This 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 present disclosure relates to the use of a solution-annealed object made of a duplex (ferritic-austenitic) stainless steel, having the following composition in weight% (wt%):
  • Si less than or equal to 0.5
  • Mn less than or equal to 1.0
  • the balance being Fe and inevitable impurities
  • the duplex stainless steel fulfills the condition that Cr+50N ⁇ 35; and wherein the duplex stainless steel has a ferrite content in the range of from 40% to 60 % by volume and an austenite content in the range of 40% to 60 % by volume; in sea water applications.
  • 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 disclosure 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 disclosure 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 .
  • 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 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 of from 5.0 to 7.0 wt , such as of from 6.0 to 7.0 wt .
  • Chromium 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 of from 22.0 to 26.0 wt%, such as of 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 0.10 to 0.20 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.
  • S Sulphur
  • S 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 , AIN 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 micro structure 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 micro structure 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% to55 % 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 process ability, such as the hot workability, the machinability etc.
  • examples of such elements are Titanium (Ti), Calcium (Ca), Cerium (Ce) and Boron (B). If added, these elements are in an amount of max 0.5 wt% in total.
  • the duplex stainless steel according to the present disclosure 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 may be below 35 ⁇ , such as in the range of from 5-35 ⁇ , such as in the range of from 5-20 ⁇ , such as in the range of from 5-15 ⁇ .
  • 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 disclosure may be 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 p o. 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 disclosure 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/or cold working, solution annealing and an optional additional heat treatment or be manufactured as a powder product by for example a hot isostatic pressure process (HIP).
  • HIP hot isostatic pressure process
  • 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: a. melting;
  • 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.
  • Figure 1 discloses HISC-testing at constant load at 4°C in 3 wt sodium chloride
  • Table 1 shows the compositions of the duplex stainless steels used. Both inventive and comparative examples are shown below.
  • the points El and E2 stand for Example 1 and Example 2 of the present disclosure, while the points C1-C3 stands for the comparative examples 1-3.
  • the mold was removed and the ingot was held at 1050°C for 2 hours and then quenched in water. A sample for chemical analysis was taken from each ingot. The chemical analyses were performed using X-Ray Fluorescence Spectrometry and Spark Atomic Emission Spectrometry and combustion technique.
  • 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.
  • 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 mVscE. The testing time was 500 hours or until failure and the load correlated to the proof strength. Prior the experiment, 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 disclosure 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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  • 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)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The present disclosure relates to the use of a solution-annealed object comprising a duplex stainless steel, having the following composition in weight% (wt %): C less than or equal to 0.03; Si less than or equal to 0.5; Mn less than or equal to 1.0; Ni 5.0 to 7.0; Cr 22.0 to 26.0; Mo 2.5 to 4.5; N 0.1 to 0.2; P less than or equal to 0.03; S less than or equal to 0.03; Cu less than or equal to 0.3; Al less than or equal to 0.10; the balance being Fe and inevitable impurities; wherein the duplex stainless steel fulfills the equation of Cr+50N ≤ 35; and wherein the duplex stainless steel has a ferrite phase content in the range of from 40% to 60 % by volume and an austenite phase content in the range of 40 to 60 % by volume; in sea water applications.

Description

USE OF A DUPLEX STAINLESS STEEL OBJECT
TECHNICAL FIELD
The present disclosure 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).
BACKGROUND ART
Cathodic protection (CP) 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. Thus, it is a technique to reduce corrosion of a metal surface by making that surface the cathode of an electrochemical cell. Hence, the duplex stainless steel will be the cathode and another metal will be the anode (usually Zn).
Even though duplex stainless steels have been a very good choice of material to use in conjunction with cathodic protection, some failures have been encountered over the past years relating to hydrogen induced stress corrosion cracking, also known as HISC. HISC is a non-ductile mode of failure having its origin in a combination between stresses, use of a cathodic protection system and use of a material with a susceptible microstructure and is caused by atomic hydrogen diffusion. This failure has an impact on the strength and the ductility of the duplex stainless steels as these materials due to HISC will become more prone to brittle cracking, especially during the application of high loads.
Hence, there exists still a need for further improvements of duplex (ferritic-austenitic) 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). DETAILED DESCRIPTION
It is therefore an aspect of the present disclosure to provide an object made of a duplex (ferritic-austenitic) stainless steel which object is to be used in sea water applications. This duplex stainless steel object has an element composition which together with the manufacturing method will provide good resistance against hydrogen induced stress corrosion (HISC). Thus, the present disclosure relates to the use of a solution-annealed object made of a duplex (ferritic-austenitic) stainless steel, having the following composition in weight% (wt%):
C less than or equal to 0.03;
Si less than or equal to 0.5;
Mn less than or equal to 1.0;
Ni 5.0 to 7.0;
Cr 22.0 to 26.0;
Mo 2.5 to 4.5;
N 0.1 to 0.2;
P less than or equal to 0.03;
S less than or equal to 0.03;
Cu less than or equal to 0.3;
Al less than or equal to 0.10;
the balance being Fe and inevitable impurities;
wherein the duplex stainless steel fulfills the condition that Cr+50N < 35; and wherein the duplex stainless steel has a ferrite content in the range of from 40% to 60 % by volume and an austenite content in the range of 40% to 60 % by volume; in sea water applications. According to one embodiment, 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.
By the optimizing the element composition of the present duplex stainless steel and the process for manufacturing the object, the object comprising the duplex stainless steel will have a high corrosion resistance and good structure stability. Hence, 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
Thus, the present disclosure 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 disclosure 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.
The process for manufacturing the present object as defined hereinabove or hereinafter must contain a step of solution annealing. 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.
The alloying elements and their compositional ranges of the duplex stainless steel according to the present disclosure will now be further described. Carbon (C), is an impurity contained in duplex stainless steels. When the content of C exceeds 0.03 wt , the corrosion resistance is reduced due to the precipitation of chromium carbide in the grain boundaries. Thus, the content of C is less than or equal to 0.03 wt , such as less than or equal to 0.02 wt . 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%. One important reason is that Mn has the ability to bind sulphur, which is an impurity, into MnS, which is favorable to the hot ductility. Thus, in order to have this effect, 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. Thus, the content of Ni is of from 5.0 to 7.0 wt , such as of 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 of from 22.0 to 26.0 wt%, such as of from 23.0 to 24.0 wt%.
Molybdenum (Mo), 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. When 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%.
Nitrogen (N), is an effective element for increasing the strength in duplex stainless steels by solution hardening. If the N content is too low, the mechanical properties and pitting resistance will be reduced. If the N is too high, the resistance against HISC will be reduced. As shown in Figure 1, a linear relation between the HISC- resistance and the equation Cr + 50N has been found, Therefore, the content of N is of from 0.10 to 0.20 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 (S), 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 (Cu), 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 , AIN 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 .
It has surprisingly been found that a solution-annealed object composed of duplex stainless steel as defined hereinabove or hereinafter and which fulfills the equation of Cr+50N is less than or equal to 35 (see Figure 1) will have a better resistance against HISC, the amounts of Cr and N in this equation is in weight . This means that the content of Cr is connected to the content of N meaning that the content of Cr and N in the hereinabove or hereinafter defined duplex stainless steel is found to be low (if compared to other known duplex stainless steels). It should be noted that according to the common general knowledge that a relation between Cr to N could not have been predicted because the susceptibility for HISC has earlier been attributed to the micro structure of the duplex stainless steel and not the chemical composition of the duplex stainless steel. It can further be noted that duplex grades commonly used for these applications have a content of 25 wt Cr and more than 0,25 wt N. According to one embodiment, Cr+50N is less than or equal to 34, such less than or equal to 33.
According to the present disclosure, 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 micro structure 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
temperature is in the range of from 1030 to 1150°C. According to one embodiment, 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 micro structure 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. 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. Hence, in the present disclosure, 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. Accordingly, 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% to55 % by volume, balanced by the austenite phase.
According to one embodiment, other elements may optionally be added to the duplex stainless steel as defined hereinabove or hereinafter for example during the manufacturing process in order to improve for example the process ability, such as the hot workability, the machinability etc. Examples of such elements are Titanium (Ti), Calcium (Ca), Cerium (Ce) and Boron (B). If added, these elements are in an amount of max 0.5 wt% in total. According to one embodiment, the duplex stainless steel according to the present disclosure 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. Examples of 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. According to one embodiment, the austenite spacing of the duplex stainless steel as defined hereinabove or hereinafter in solution-annealed condition may be below 35 μιη, such as in the range of from 5-35 μιη, such as in the range of from 5-20 μιη, such as in the range of from 5-15 μιη.
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. For duplex stainless steels, 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. Thus, according to one embodiment, the PRE of the duplex stainless steel according to the present disclosure may be 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 (Rpo.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.
Higher elongation means higher ductility and this property is considered in forming manufacturing processes. Thus, according to one embodiment of the present disclosure, the elongation (A) of the duplex stainless steel according to the present disclosure 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/or cold working, solution annealing and an optional additional heat treatment or be manufactured as a powder product by for example a hot isostatic pressure process (HIP). The important step in the manufacturing method is the solution annealing step as this will set the final microstructure
According to one embodiment, the object comprised of duplex stainless steel as defined hereinabove or hereinafter is manufactured by a process comprising the following steps: a. melting;
b. casting;
c. hot working;
d. cold working;
e. solution annealing. 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.
The present disclosure is further illustrated by the following non-limiting examples. BRIEF DESCRIPTION OF DRAWINGS
Figure 1 discloses HISC-testing at constant load at 4°C in 3 wt sodium chloride
(NaCl) thus simulating the environment which a duplex stainless steel is exposed to in sea water.
EXAMPLES
Five different heats with different compositions were melted as 270 kg heats in a high frequency induction furnace and cast to ingots using a 9 "mould. Table 1 shows the compositions of the duplex stainless steels used. Both inventive and comparative examples are shown below. In Table 1, the points El and E2 stand for Example 1 and Example 2 of the present disclosure, while the points C1-C3 stands for the comparative examples 1-3.
Table 1. Chemical composition of different heats
After casting, the mold was removed and the ingot was held at 1050°C for 2 hours and then quenched in water. A sample for chemical analysis was taken from each ingot. The chemical analyses were performed using X-Ray Fluorescence Spectrometry and Spark Atomic Emission Spectrometry and combustion technique. 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. After the final heat treatment step, 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 mVscE. The testing time was 500 hours or until failure and the load correlated to the proof strength. Prior the experiment, the samples were galvanostatically charged with hydrogen with a current density of 0.02 A/cm2.
When analyzing the results from HISC-testing, it was surprisingly found that the solution annealed duplex stainless steels with a lower Cr and N content had better resistance against HISC. A linear relation between the maximum load without failure in the HISC-testing related to the proof strength (Rpo.2) at 4 C°and a linear relation to the equation Cr+50N were observed as can be seen from Figure 1. In Figure 1, the points El and E2 stand for Example 1 and Example 2 of the present disclosure while the points C1-C3 stands for the comparative examples 1-3. Hence, the objects made of a duplex stainless steel must fulfill the equation that Cr+50xN is less than or equal to 35 to have improved HISC resistance.
Further, the solution annealed duplex stainless objects was analysed. Tensile testing (RPo,2 and Rm) was performed at room temperature in order to determine the yield strength.
Elongation (A) was measured according to ISO 6892-1. The ferrite content was measured according to ASTM E562. The austenite spacing was measured according to DNV-RP- Fl 12. These experimental results are shown in Table 2. Table 2. Experimental results Rpo,2 (MPa) Rm A(%) Ferrite Austenite spacing PRE
(MPa) (%) (μηι)
El 506» 693 29 51 13.7 35.8
E2 536 769 35 45 10 39.5
CI 618 829 31 56 34 43.8
C2 568 794 34 48 19 41.4
C 3 594 798 32 52 23 41.2
In Table 2, the points El and E2 stand for Example 1 and Example 2 of the present disclosure, while the points C1-C3 stands for the comparative examples 1-3.
As can be seen from the results in Table 3, the solution-annealed objects made of duplex stainless steel of the present disclosure 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.

Claims

1. Use of a solution-annealed object comprising a duplex stainless steel, having the following composition in weight (wt %):
C less than or equal to 0.03;
Si less than or equal to 0.5;
Mn less than or equal to 1.0;
Ni 5.0 to 7.0;
Cr 22.0 to 26.0;
Mo 2.5 to 4.5;
N 0.1 to 0.2;
P less than or equal to 0.03;
S less than or equal to 0.03;
Cu less than or equal to 0.3;
Al less than or equal to 0.10;
the balance being Fe and inevitable impurities;
wherein the duplex stainless steel fulfills the equation of Cr+50N < 35; and wherein the duplex stainless steel has a ferrite phase content in the range of from 40% to 60 % by volume and an austenite phase content in the range of 40 to 60 % by volume; in sea water applications.
2. The use of a solution-annealed object comprising a duplex stainless steel according to claim 1, wherein the content of Cr is of from 23.0 to 24.0 wt%.
3. T The use of a solution-annealed object comprising of a duplex stainless steel according to claim 1 or claim 2, wherein the content of Ni is of from 6.0 to 7.0 wt%.
4. The use of a solution-annealed object comprising of a duplex stainless steel
according to anyone of proceeding claims, wherein the content of N is of from 0.12 to 0.20 wt%.
5. The use of a solution-annealed object comprising of a duplex stainless steel according to anyone of proceeding claims, wherein the content of Mo is of from 2.8 to 4.0 wt%.
6. The use of a solution-annealed object comprising of a duplex stainless steel
according to anyone of proceeding claims, wherein the content of Cu is less than or equal to 0.2wt .
7. The use of a solution-annealed object comprising of a duplex stainless steel
according to anyone of proceeding claims, wherein the duplex stainless steel fulfills the equation of Cr+50N < 34.
8. The use of a solution-annealed object comprising of a duplex stainless steel
according to anyone of proceeding claims, wherein the duplex stainless steel fulfills the equation of Cr+50N < 33.
9. The use of a solution-annealed object comprising of a duplex stainless steel
according to anyone of proceeding claims, wherein the object is in the form of; a bar, a tube, a seamless or a welded tube, a constructive part, a plate, a sheet, a strip or a wire.
10. The use of a solution-annealed object made of duplex stainless steel according to anyone of proceeding claims, wherein the object is manufactured by the process comprising the following steps:
a. melting;
b. casting;
c. hot working;
d. cold working;
e. solution annealing and wherein the solution annealing is performed at a temperature above the recristallisation temperature of said duplex stainless steel.
11. The use of a solution-annealed object comprising of a duplex stainless steel according to claim 10, wherein the solution annealing is performed in a temperature of from in the range of from 1030-1150°C.
12. The use of a solution-annealed object comprising of a duplex stainless steel
according to anyone of proceeding claims, wherein the use in sea water application is as a cathode.
EP17829629.9A 2016-12-21 2017-12-18 Use of a duplex stainless steel object Active EP3559282B1 (en)

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