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EP3280826B1 - Procédé de production d'un tube en acier inoxydable duplex - Google Patents

Procédé de production d'un tube en acier inoxydable duplex Download PDF

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Publication number
EP3280826B1
EP3280826B1 EP16718275.7A EP16718275A EP3280826B1 EP 3280826 B1 EP3280826 B1 EP 3280826B1 EP 16718275 A EP16718275 A EP 16718275A EP 3280826 B1 EP3280826 B1 EP 3280826B1
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EP
European Patent Office
Prior art keywords
tube
stainless steel
duplex stainless
range
pilgering
Prior art date
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EP16718275.7A
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German (de)
English (en)
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EP3280826A1 (fr
Inventor
Jari PONSILUOMA
Maria HINDRUM
Josefin EIDHAGEN
Katarina PERSSON
Russell P. JONES
Åsa LARSSON
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Sandvik Intellectual Property AB
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Sandvik Intellectual Property AB
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Classifications

    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, wire, rods, tubes or like semi-manufactured products by drawing
    • B21C1/16—Metal drawing by machines or apparatus in which the drawing action is effected by means other than drums, e.g. by a longitudinally-moved carriage pulling or pushing the work or stock for making metal sheets, rods or tubes
    • B21C1/22—Metal drawing by machines or apparatus in which the drawing action is effected by means other than drums, e.g. by a longitudinally-moved carriage pulling or pushing the work or stock for making metal sheets, rods or tubes specially adapted for making tubular articles
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • 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
    • C22C38/02—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
    • C22C38/18—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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni

Definitions

  • the present disclosure relates to a method of producing a tube of a duplex stainless steel, in particular a duplex stainless steel suitable for use in fuel injection systems for injection of fuel into the combustion chamber of a combustion engine.
  • the requirements on a tube to be used as a GDI-rail are several, and must be considered when designing the duplex stainless steel to be used in such an application. It is thus of importance to select a chemical composition of the duplex stainless steel that, in combination with a properly chosen tube manufacturing process, results in a predetermined austenite/ferrite ratio, a requested corrosion resistance (resistance against general corrosion as well as against pitting corrosion), a microstructure essentially free from intermetallic phases, in particular sigma phase and chromium nitrides, a predetermined impact toughness, a predetermined tensile strength and a predetermined fatigue strength. Furthermore, the mechanical properties of the duplex steel should be such that the obtained tube will present a predetermined burst pressure, i.e. internal pressure until failure, which is high enough for the envisaged application, also when the wall thickness of the tube is relatively small, thereby enabling a GDI-rail that requires less space and weight. The corrosion and fatigue properties should guarantee the endurance of the tube over time.
  • Designing of a duplex stainless steel and the process of producing a tube thereof assumed to meet the requirements of a GDI-rail is therefore a complex task.
  • the selected chemical composition and the production process parameters must be tuned with regard to each other. Accordingly, once a nominal chemical composition has been decided for the duplex stainless steel, the production process parameters must also be selected with regard thereto.
  • the chemical composition of the duplex stainless steel should also promote a cost efficient production process. In other words, the chemical composition should not be such that it will require excessively complicated, energy-consuming or time-consuming production steps. A such example is given in JP S 63255322 .
  • the aspect of the present disclosure is to present a method of producing a tube of a duplex stainless steel that enables the production of a tube of said duplex stainless steel presenting properties making the tube suitable to applications in which there are high requirements on corrosion resistance (resistance against general corrosion as well as against pitting corrosion), a predetermined impact toughness, a predetermined tensile strength and a predetermined fatigue strength.
  • duplex stainless steel of said tube should present a microstructure essentially free from intermetallic phases, in particular sigma phase and chromium nitrides.
  • the chemical composition of the duplex stainless steel shall enable cost-efficient production of a tube thereof in terms of promoting the use of cost-efficient process steps.
  • the annealing temperature should be in the range of from 950 to 1060°C and the atmosphere should comprise a gas mixture of 1-6 vol% nitrogen and the remainder is selected from H 2 or an inert gas and the annealing should be performed in a time period of from 0.3-10 minutes
  • the upper temperature limit for the annealing step is set by the temperature at which the duplex stainless steel will start to melt.
  • the annealing temperature shall be further restricted.
  • the duplex stainless steel will become softer, which will increase the risk of damages during the annealing step.
  • the grain growth will increase making it more difficult to obtain a good process and grain size control.
  • annealing temperature which will balance the phase fraction, a too low temperature will cause too low ferrite content and a too high temperature will provide too high ferrite content.
  • the temperature of the annealing step will also influence the chemical composition of the ferrite and the austenite phase, so the annealing temperature needs to be balanced together with the chemical composition to ensure that both these phases will have good corrosion resistance.
  • the time period for which the tube is subjected to the annealing temperature should be between 0.3 to 10 minutes, such as 0.3 to 5 minutes, such as 0.3 to 2.5 -minutes. This time period needs to be long enough to ensure complete recrystallization. However, if said time period is too long, the obtained tube will have a coarse structure which will have a negative impact on the mechanical properties. The larger the thickness of the tube wall, the longer the annealing time. Wall thicknesses of from about 1 mm up to about 5 mm are conceived.
  • the atmosphere of the annealing step is very important.
  • An atmosphere comprising nitrogen will affect the content of nitrogen in the surface of the duplex stainless steel.
  • the role of nitrogen in the atmosphere is to maintain the nitrogen content of the material at the surface.
  • nitrogen will diffuse into and out from the material.
  • the nitrogen content should be selected so that the nitrogen content in the surface is maintained. It has been found that too low nitrogen content in the atmosphere where the annealing is performed will result in a net loss of nitrogen in the surface, which will affect the corrosion resistance and the mechanical properties of the duplex stainless steel as defined hereinabove or hereinafter negatively.
  • a PRE of at least about 23.0 indicates that, with the above-defined composition, all three of chromium, molybdenum and nitrogen are not allowed to be at their minimum simultaneously but must be combined such that the defined PRE-value is obtained.
  • the PRE-value is at least about 24.0.
  • the term "about” as used hereinabove and hereinafter indicates +/- 10% of an integer.
  • the temperature range of the annealing step (step g) is of from 970°C to 1040°C. According to yet another embodiment, said temperature range is of from 1000°C to 1040°C.
  • said annealing step comprises subjecting said tube to said temperature for a time period of from 0.5-5 minutes, such as of from 0.5 to 1.5 minutes.
  • the inert gas is argon or helium or a mixture thereof.
  • the content of nitrogen gas in the gas mixture is equal to or less than 4 vol%. According to another embodiment the content of nitrogen gas in said gas mixture is equal to or less than 3 vol%. According to yet one embodiment, the content of nitrogen gas in said gas mixture is equal to or above 1.5 vol%.
  • said hot extrusion step (step e) comprises subjecting said tube to hot extrusion at a temperature in the range of from 1100°C-1200°C and a cross-sectional area reduction thereof in the range of from 92-98%.
  • said hot extrusion step (step e) comprises subjecting said tube to hot extrusion at a temperature in the range of from 1100°C-1170°C and a cross-sectional area reduction thereof in the range of from 92-98%.
  • the cross-sectional area reduction is defined as (cross-sectional area (of tube) before extrusion minus cross-sectional area after extrusion)/(cross-sectional area before extrusion).
  • the extrusion temperature and deformation degree is chosen with regard to the chemical composition of the duplex stainless steel such that it will not have a detrimental effect on the microstructure of the duplex stainless steel or will result in cracks or the like therein that would be detrimental to the mechanical properties of the final product.
  • the cold deformation step (step f) comprises subjecting the tube to cold deformation without pre-heating the tube.
  • said cold deformation step (step f) comprises subjecting said tube to a cross sectional area reduction thereof in the range of 50-90%.
  • Cross-sectional area reduction is defined as (cross-sectional area (of tube) before pilgering minus cross-sectional area after pilgering)/(cross-sectional area before pilgering).
  • the chemical composition of the duplex stainless steel is selected to enable such cold deformation thereof without unwanted crack-generation in the material or any detrimental negative effects on the microstructure of the material.
  • the cold deformation is either pilgering or cold drawing.
  • Q is in the range of from 0.9-1.1.
  • said duplex stainless steel has the following composition, in weight%: C 0.01-0.025; Si 0.35-0.6; Mn 0.8-1.5; Cr 21-23.5; Ni 3.0-5.5; Mo 0.10-1.0; Cu 0.15-0.70; N 0.090-0.25; P less than or equal to 0.035; S less than or equal to 0.003; balance Fe and unavoidable impurities.
  • a duplex stainless steel with this chemical composition is particularly suitable to be subjected to the above-mentioned process steps with the above-mentioned process parameters.
  • the process steps and parameters as defined hereinabove or hereinafter are selected to be particularly suitable on a duplex stainless steel with this chemical composition and to result in a tube with properties that makes it particularly suitably in an application as GDI-rail for conduction of a fuel in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine.
  • the tube is a tube for conduction of a fuel in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine.
  • the present disclosure may, as an alternative, be defined as a process of producing a fuel conductor in a fuel injection system for injecting fuel into the combustion chamber of a combustion engine, wherein said process comprises the method defined hereinabove and/or hereinafter for producing a tube of duplex stainless steel.
  • Such a process includes attaching the tube of duplex stainless steel to a further structural member of said combustion engine by means of brazing.
  • the further structural member may be metal, typically austenitic or duplex steel.
  • the method of producing the tube including the selection of the chemical composition of the duplex stainless steel, also aims at achieving a tube with advantageous brazing properties, in particular a low susceptibility to liquid metal induced embrittlement (LMIE) caused by liquid metal penetration.
  • the brazing includes copper brazing, possibly in a continuous furnace at temperature in the range of from 1100°C-1140°C.
  • the tube has an outer diameter in the range of from 15-35 mm after said pilgering step. According to one embodiment, this tube is used as a GDI-rail in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
  • the tube has an outer diameter of from 7-10 mm after said pilgering step. According to one embodiment, this tube is used as a fuel line in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
  • Carbon, C has an austenite stabilizing effect and counteracts the transformation from austenitic to martensitic structure upon deformation of the duplex stainless steel.
  • C has a positive effect on the strength of the duplex stainless steel. Therefore, the content of C should be equal to or above 0.01 wt%. However, at too high levels, carbon tends to form unwanted carbides with other alloying elements. The content of C should therefore not be above 0.06 wt%. According to one embodiment, the content of C should not be above 0.025 wt%.
  • Chromium, Cr has strong impact on the corrosion resistance of the duplex stainless steel, especially pitting corrosion.
  • the PRE-value is above 23.0.
  • Cr improves the yield strength, and counteracts transformation of austenitic structure to martensitic structure upon deformation of the duplex stainless steel. Therefore, the content of Cr should be equal to or above 21.0 wt%.
  • the content of Cr is equal to or less than 24.5 wt%.
  • Cr also has a ferrite-stabilizing effect on the duplex stainless steel. According to one embodiment the content of Cr is equal to or less than 23.5 wt%.
  • Nickel, Ni has a positive effect on the resistance against general corrosion. Ni also has a strong austenite-stabilizing effect and counteracts transformation from austenitic to martensitic structure upon deformation of the duplex stainless steel. The content of Ni is therefore equal to or more than 2.0 wt%. According to another embodiment the content of Ni is equal to or more than 3.5 wt%. To some extent the austenite-stabilizing effect of Ni may be compensated for by adjusting the Cr content. The content of Ni should, however, not be more than or equal to 5.5 wt%.
  • the content of Si in the duplex stainless steel is not more than 1.5 wt%. According to one embodiment, the content of Si in the duplex stainless steel is not more than 0.6 wt%. According to one embodiment the content of Si may be as low as about 0 wt%. According to one embodiment, the content of Si should be equal to or more than 0.35 wt%.
  • Molybdenum Mo
  • Mo has a strong influence on the corrosion resistance of the duplex stainless steel. It heavily influences the PRE thereof.
  • Mo is added in amount of equal to or more than 0.01 wt%. It also has a ferrite-stabilizing effect on the duplex stainless steel. According to one embodiment, the content of Mo is above 0.10 wt%. Mo also increases the temperature at which unwanted sigma-phases are stable and promotes the rate of generation thereof. It is also a relatively expensive alloying element. Therefore, the content of Mo should be equal to or less than 1.0 wt%.
  • Copper, Cu has a positive effect on the corrosion resistance. Cu also counteracts transformation of austenite to martensite upon deformation of the duplex stainless steel. It is thus optional to purposively add Cu to the duplex stainless steel. Often, Cu is present in scrapped goods used for the production of steel, and is allowed to remain in the steel at moderate levels. According to one embodiment, the content of Cu may be equal to or more than 0.01 wt%. According to another embodiment, the content of Cu is equal to or more than 0.15 wt%. According to one embodiment, the content of Cu is equal to or less than 1.0 wt%. According to another embodiment, the content of Cu is equal to or less than 0.7 wt%.
  • Manganese, Mn has a deformation hardening effect on the duplex stainless steel, and it counteracts the transformation from austenitic to martensitic structure upon deformation of the duplex stainless steel. Mn also has an austenite stabilizing effect. According to one embodiment, the content of Mn in the duplex stainless steel should be equal to or above 0.8 wt%. However, Mn has a negative impact on the corrosion resistance in acids and chloride-containing environments, and it increases the tendency to generation of intermetallic phases. Therefore, the maximum content of Mn should not be above 2.0 wt%. According to one embodiment, the content of Mn is equal to or less than 1.0 wt%.
  • N has a positive effect on the corrosion resistance of the duplex stainless steel and also contributes to deformation hardening. It has a strong effect on the pitting corrosion resistance equivalent PRE. It also has a strong austenite stabilizing effect and counteracts transformation from austenitic structure to martensitic structure upon plastic deformation of the duplex stainless steel, and is therefore added in an amount of 0.05 wt% or higher.
  • the content of N should be equal to or more above 0.090 wt%. At too high levels, N tends to form chromium nitrides in the duplex stainless steel, which should be avoided due to its negative effect on ductility and corrosion resistance. Therefore, the content of N should be equal to or lower than 0.3 wt%. According to one embodiment, the content of N is equal to or less than 0.25 wt%.
  • Phosphorus, P is an impurity contained in the duplex stainless steel and it is well known that P affects the hot workability negatively. Accordingly, the content of P is set at 0.03 wt% or less.
  • S is an impurity contained in the austenitic stainless steel and it will deteriorate the hot workability. Accordingly, the allowable content of S is less than or equal to 0.03 wt%, such as less than or equal to 0.005 wt%.
  • the duplex stainless steel as defined hereinabove or herein after may optionally comprise one or more of the following elements selected from the group of Al, V, Nb, Ti, O, Zr, Hf, Ta, Mg, Ca, La, Ce, Y and B. These elements may be added during the manufacturing process in order to enhance e.g. deoxidation, corrosion resistance, hot ductility or machinability. However, as known in the art, the addition of these elements has to be limited depending on which element is present. Thus, if added the total content of these elements is less than or equal to 1.0 wt%.
  • impurities as referred to herein is intended to mean substances that will contaminate the duplex stainless steel when it is industrially produced, due to the raw materials such as ores and scraps, and due to various other factors in the production process, and are allowed to contaminate within the ranges not adversely affecting the duplex stainless steel as defined hereinabove or hereinafter.
  • the obtained melts were then processed accordingly: They were casted to bodies by using continuous casting. Round bars were then formed by forging and the tubes were then formed by boring a hole therein.
  • the diameter of the tubes was then reduced by by using hot extrusion at a temperature in the range of from 1120°C-1150°C, the obtained tubes had a cross-sectional area reduction of 96-98%.
  • the hot extrusion was followed by pickling to remove glass beads.
  • the diameter was further reduced by pilgering and subjecting the tubes to a cross sectional area reduction thereof in the range of 80-86%.
  • the pilgered tubes were then annealed in an atmosphere consisting of a gas mixture comprising about 2% nitrogen gas and remainder argon gas and subjecting the tubes to a temperature of about 1030°C for a time period of about 1 minute.
  • the obtained tubes were subjected to a straightening step.
  • Straightening was performed in a roll straightening machine with a combination of bending and ovalization.
  • the tubes were passed through a series of angled rollers which rotated the tube and applied to it a series of bending movements. During straightening the yield strength is exceeded in order to get a permanent change in shape to obtain a straight tube.
  • the obtained tubes had on outer diameter in the of 30 mm aand the tubes are to be used as a GDI-rail in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.
  • One additional tube of melt 1 was also manufactured according to the method disclosed above. This tube had an outer diameter of from 8 mm after the pilgering step. This tube was also used as a fuel line in a fuel injection system for conducting fuel to be injected into the combustion chamber of a combustion engine.

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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)
  • Manufacturing & Machinery (AREA)
  • Fuel-Injection Apparatus (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (13)

  1. Procédé de production d'un tube d'acier inoxydable duplex comprenant la composition suivante, en % en poids, C max 0,06 ; Cr 21-24,5 ; Ni 2,0-5,5 ; Si max 1,5 ; Mo 0,01-1,0 Cu 0,01-1,0 ; Mn max 2,0 ; N 0,05-0,3 ; P max 0,04 ; S max 0,03 ; et
    équilibre en Fe et impuretés inévitables,
    et ayant une valeur PRÉLIMINAIRE d'au moins 23,0,
    dans lequel le procédé comprend les étapes de :
    a) la fourniture d'une fonte de l'acier inoxydable duplex ;
    b) le moulage d'un corps de l'acier inoxydable duplex à partir de la fonte ;
    c) la formation d'une barre du corps ;
    d) la formation d'un tube de la barre par la génération d'un trou dans celle-ci ;
    e) la réduction du diamètre et/ ou de l'épaisseur de paroi du tube par extrusion chaude à une température dans la plage de 1 100°C et 1 200°C et une réduction de la zone transversale dans la plage de 92-98% ;
    f) la réduction supplémentaire du diamètre et/ ou de l'épaisseur de paroi du tube par déformation à froid par la soumission du tube à une réduction de la zone transversale dans la plage de 50 à 95 %, et
    g) le recuit du tube déformé à froid ;
    dans lequel, après l'étape g), l'acier inoxydable duplex du tube obtenu est constitué de 40-60% d'austénite et de 40-60% de ferrite et dans lequel l'étape g) comprend la soumission dudit tube à une température dans la plage de 950°C-1 060°C pendant une période de temps de 0,310 minutes et à une atmosphère constituée d'un mélange de gaz comprenant 1-6 % en vol. de gaz d'azote et le reste est du H2 ou un gaz inerte.
  2. Procédé selon la revendication 1, dans lequel la température est dans la plage de 970 °C-1040 °C.
  3. Procédé selon la revendication 1, dans lequel la température est dans la plage de 1000 °C-1 040°C.
  4. Procédé selon l'une quelconque des revendications 1 à 3, dans lequel l'étape de recuit comprend ledit tube soumis à ladite température pendant une période de temps de 0,5 à 5 minutes.
  5. Procédé selon l'une quelconque des revendications 1 à 4, dans lequel le gaz inerte est de l'argon ou de l'hélium ou un mélange de ceux-ci.
  6. Procédé selon l'une quelconque des revendications 1 à 5, dans lequel la teneur en gaz d'azote dans le mélange gazeux est égale ou inférieure à 4 % en vol.
  7. Procédé selon l'une quelconque des revendications 1 à 6, dans lequel la teneur en gaz d'azote dans le mélange gazeux est égale ou supérieure à 1,5 % en vol.
  8. Procédé selon l'une quelconque des revendications 1- 7, dans lequel l'étape f comprend la soumission, sans préchauffage, du tube à la déformation à froid.
  9. Procédé selon l'une quelconque des revendications 1 à 8, dans lequel la déformation à froid est un laminage.
  10. Procédé selon la revendication 9, dans lequel, dans ladite étape de laminage, la relation entre la réduction de l'épaisseur de paroi et la réduction de diamètre extérieur du tube est exprimée comme valeur Q, dans laquelle Valeur Q = Wallh − Wallt * Odh − Wallh / Wallh Odh − Wallh − Odt − Wallt ,
    Figure imgb0004
     dans lequel
    Wallh=paroi creuse=l'épaisseur de la paroi avant laminage
    Wallt=paroi du tube=l'épaisseur de la paroi après laminage
    Odh=OD creux=diamètre du tube avant laminage
    Odt=OD du tube=le diamètre du tube après laminage,
    et dans lequel Q est compris entre 0,5-2,5.
  11. Procédé selon la revendication 10, dans lequel Q se situe dans la plage de 0,9-1,1.
  12. Procédé selon l'une quelconque des revendications 1-11, dans lequel ledit acier inoxydable duplex comprend, en % en poids, : C 0,01-0,025 ; Si 0,35-0,6 ; Mn 0,8-1,5 ; Cr 21-23,5 ; Ni 3,0-5,5 ; Mo 0,10-1,0 ; Cu 0,15-0,70 ; N 0,090-0,25 ; P inférieur ou égal à 0,035 ; S inférieur ou égal à 0,003 ; équilibre en Fe et impuretés inévitables.
  13. Utilisation d'un tube qui a été fabriqué selon l'une quelconque des revendications 1-12 pour la conduction d'un carburant dans un système d'injection de carburant pour l'injection de carburant dans la chambre de combustion d'un moteur à combustion.
EP16718275.7A 2015-04-10 2016-04-08 Procédé de production d'un tube en acier inoxydable duplex Active EP3280826B1 (fr)

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PCT/EP2016/057831 WO2016162525A1 (fr) 2015-04-10 2016-04-08 Procédé de production d'un tube d'un acier inoxydable duplex

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Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102015226795A1 (de) * 2015-12-29 2017-06-29 Robert Bosch Gmbh Komponente einer hydraulischen Einrichtung, insbesondere einer Brennstoffeinspritzanlage für Brennkraftmaschinen
WO2017114849A1 (fr) * 2015-12-30 2017-07-06 Sandvik Intellectual Property Ab Un procédé de production d'un tube d'acier inoxydable austénitique
DE102016115550B4 (de) * 2016-08-22 2018-05-30 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines Kraftstoffverteilers
CN110088323B (zh) * 2016-12-21 2022-03-22 山特维克知识产权股份有限公司 包含双相不锈钢的制品及其用途
JP6369662B1 (ja) * 2017-01-10 2018-08-08 Ｊｆｅスチール株式会社 二相ステンレス鋼およびその製造方法
JP2020521047A (ja) * 2017-05-22 2020-07-16 サンドビック インテレクチュアル プロパティー アクティエボラーグ 新規な二相ステンレス鋼
EP3682105A1 (fr) * 2017-09-14 2020-07-22 Sandvik Materials Technology Deutschland GmbH Rampe de carburant de distributeur et procédé de fabrication d'une rampe de carburant de distributeur
CN108251750A (zh) * 2018-03-30 2018-07-06 鞍钢股份有限公司 一种节镍型含Cu厚规格双相不锈钢及其制备方法
KR102324087B1 (ko) * 2019-12-18 2021-11-10 한전원자력연료 주식회사 페라이트계 합금 및 이를 이용한 핵연료 피복관의 제조방법
CN111850254B (zh) * 2020-08-17 2022-06-21 綦江重配齿轮有限公司 一种防止花键轴中频淬火变形的方法
CN113652602A (zh) * 2021-07-07 2021-11-16 上海大学 高性能双相不锈钢钢丝绳合金材料及其制备方法
JP7377942B2 (ja) * 2022-01-19 2023-11-10 三菱重工パワー環境ソリューション株式会社 熱交換器および排煙処理装置

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63255322A (ja) * 1987-04-13 1988-10-21 Kawasaki Steel Corp 二相ステンレス継目無鋼管の製造方法
WO1996018751A1 (fr) * 1994-12-16 1996-06-20 Sumitomo Metal Industries, Ltd. Acier inoxydable duplex presentant une remarquable resistance a la corrosion
JP3041050B2 (ja) * 1995-06-05 2000-05-15 ポハング アイアン アンド スチール カンパニー リミテッド 二相ステンレス鋼およびその製造法
JP3387385B2 (ja) * 1997-09-25 2003-03-17 住友金属工業株式会社 ２相ステンレス鋼の光輝焼鈍方法
JP3632672B2 (ja) * 2002-03-08 2005-03-23 住友金属工業株式会社 耐水蒸気酸化性に優れたオーステナイト系ステンレス鋼管およびその製造方法
KR20030011758A (ko) * 2002-12-28 2003-02-11 성장현 고질소 2상 스테인리스강의 열처리 방법
EP1867748A1 (fr) * 2006-06-16 2007-12-19 Industeel Creusot Acier inoxydable duplex
CN103498113B (zh) * 2008-03-26 2016-03-09 新日铁住金不锈钢株式会社 焊接热影响区的耐蚀性和韧性良好的合金节省型双相不锈钢
JP4420140B2 (ja) * 2008-06-13 2010-02-24 住友金属工業株式会社 高合金継目無管の製造方法
WO2010082395A1 (fr) * 2009-01-19 2010-07-22 住友金属工業株式会社 Procédé de production de tuyau en acier inoxydable duplex
CN101633999B (zh) * 2009-05-26 2011-06-01 山西太钢不锈钢股份有限公司 一种奥氏体不锈钢及其钢管和钢管的制造方法
CN101956142B (zh) * 2009-07-13 2013-09-11 苏州奕欣特钢管业有限公司 一种双相钢无缝管及其加工方法
JP5360046B2 (ja) * 2010-12-28 2013-12-04 新日鐵住金株式会社 熱間押出管の製造方法
JP5746893B2 (ja) * 2011-03-30 2015-07-08 新日鐵住金ステンレス株式会社 表面処理二相ステンレス鋼及びその製造方法
FI126574B (fi) * 2011-09-07 2017-02-28 Outokumpu Oy Dupleksinen ruostumaton teräs
JP5846555B2 (ja) * 2011-11-30 2016-01-20 国立研究開発法人物質・材料研究機構 ニッケルフリー高窒素ステンレス製材料の圧延・抽伸加工方法、ニッケルフリー高窒素ステンレス製シームレス細管及びその製造方法
JP5865775B2 (ja) * 2012-03-16 2016-02-17 新日鐵住金株式会社 焼結排ガス集塵機用ステンレス鋼および焼結排ガス集塵機
CN103361564B (zh) * 2013-07-16 2015-07-15 江苏银环精密钢管有限公司 一种超级双相不锈钢无缝钢管及其制备方法

Non-Patent Citations (1)

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

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CA2979511A1 (fr) 2016-10-13
US20180066331A1 (en) 2018-03-08
CN107429365A (zh) 2017-12-01
KR20170133435A (ko) 2017-12-05
ES2788530T3 (es) 2020-10-21
CA2979511C (fr) 2023-03-28
JP6763876B2 (ja) 2020-09-30
EP3280826A1 (fr) 2018-02-14
JP2018513917A (ja) 2018-05-31
WO2016162525A1 (fr) 2016-10-13

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