EP4515011A1 - Utilisation d'un alliage nickel-fer-chrome ayant une résistance élevée dans des environnements hautement corrosifs et simultanément une bonne aptitude au traitement et une bonne résistance - Google Patents

Utilisation d'un alliage nickel-fer-chrome ayant une résistance élevée dans des environnements hautement corrosifs et simultanément une bonne aptitude au traitement et une bonne résistance

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Publication number
EP4515011A1
EP4515011A1 EP23724164.1A EP23724164A EP4515011A1 EP 4515011 A1 EP4515011 A1 EP 4515011A1 EP 23724164 A EP23724164 A EP 23724164A EP 4515011 A1 EP4515011 A1 EP 4515011A1
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Prior art keywords
content
alloy
use according
nickel
chromium
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EP23724164.1A
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German (de)
English (en)
Inventor
Heike Hattendorf
Nicole De Boer
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VDM Metals International GmbH
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VDM Metals International GmbH
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Publication of EP4515011A1 publication Critical patent/EP4515011A1/fr
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    • 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
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the invention relates to the use of a nickel-iron-chromium alloy with good high-temperature corrosion resistance in highly corrosive environments and at the same time good processability and strength.
  • Austenitic nickel-iron-chromium alloys with different nickel, chromium and iron contents have long been used in furnace construction and in the chemical and petrochemical industries. For this use, good high-temperature corrosion resistance, even in highly corrosive environments such as carburizing, sulfiding and chlorinating environments, and good high-temperature strength are required.
  • the high-temperature corrosion resistance of the alloys listed in Table 1 increases with increasing chromium content. All of these alloys form a chromium oxide layer (Cr20s) with an underlying, more or less closed, silicon oxide layer. Small additions of elements with a strong affinity for oxygen such as: B. Yttrium or cerium improve corrosion resistance. The chromium content is slowly consumed over the course of use in the area of application to build up the protective layer.
  • a higher chromium content increases the service life of the material, since a higher content of the element chromium, which forms the protective layer, delays the point in time at which the chromium content is below the critical limit and oxides other than Cr2Ü3 are formed, which are, for example, iron-containing and nickel-containing oxides .
  • a further increase in high-temperature corrosion resistance can be achieved by adding silicon or aluminum. Above a certain minimum content, these elements form a closed layer beneath the chromium oxide layer and thus reduce the consumption of chromium.
  • carburizing environments CO, H2, CH4, CO2, H2O mixtures
  • carbon can penetrate into the material, which can lead to the formation of internal carbides. These cause a loss of notched impact strength. Conversion processes can also occur due to chromium depletion of the matrix.
  • Nickel alloys are therefore generally more resistant to carburization than iron-based alloys because both carbon diffusion and carbon solubility are lower in nickel than in iron.
  • Increasing the chromium content results in greater carburization resistance by forming a protective chromium oxide layer, unless the oxygen partial pressure in the gas is insufficient to form this protective chromium oxide layer.
  • materials can be used that form a layer of silicon oxide or the even more stable aluminum oxide, both of which can form protective oxide layers even at significantly lower oxygen levels.
  • DE 41 30 139 C1 describes a heat-resistant, thermoformable austenitic nickel alloy, consisting of (in mass%) 0.05 to 0.15% carbon, 2.5 to 3.0% silicon, 0.2 to 0.5% manganese, max. 0.015% phosphorus, max. 0.005% sulfur, 25 to 30% chromium, 20 to 27% iron, 0.05 to 0.15% aluminum, 0.001 to 0.005% calcium, 0.05 to 0.15% rare earths, 0.05 to 0.20% nitrogen, with the remainder nickel and the usual smelting-related impurities.
  • the alloy described in DE 41 30 139 C1 is known under the names “NiCr28FeSiCe”, Alloy 45TM, Nicrofer 45TM or under the material number 2.4889 and is referred to below as “45TM”.
  • Alloy 45TM is very resistant to carburizing and sulfiding media, making it suitable for use in waste incineration plants or coal gasification plants.
  • Figure 1 shows the metallographically measured depth of corrosion attack on various alloys after aging for 2100 hours in a PRENFLO coal gasification pilot plant in Mariestenhausen in a gas containing H2S as a function of temperature for various alloys. Table 1 shows the composition of the alloys examined according to the state of the art. A high chromium and a high silicon content significantly reduces the depth of corrosion attack. Due to the high silicon content of > 2.5%, a silicon oxide layer can form under the protective chromium oxide layer, which results in the material's high corrosion resistance. 45TM with 26 to 29% chromium and 2.5 to 3% silicon shows the lowest depth of corrosion attack at all temperatures, followed by AC66 with 26 to 28% chromium and a maximum of 0.3% silicon.
  • alloy 45TM is very difficult to process. This can be seen, for example, during hot forming through crack formation. When welding, 45TM also tends to form cracks, which makes it impossible to perform its own welding (with a welding filler in the composition range of the material to be welded), which would be useful for reasons of corrosion protection practical use of the material is difficult.
  • the cause of the increased hot crack formation for austenitic FeCrNi weld metals with primary austenite solidification is the formation of low-melting phases due to silicon enrichments at the austenite grain boundaries (eutectic Fe-Fe2Si: 1212°C; eutectic NiSi-NisSi2: 964°C and NiSi: 996°C) as well as the increasing solidification area.
  • the heat resistance is, among other things, improved by a high carbon content.
  • high contents of solid solution strengthening elements such as chromium, aluminum, silicon, molybdenum and tungsten, also improve the high-temperature strength.
  • US 6,623,869 B1 describes a metallic material that contains the following components in mass%: not more than 0.2% carbon, 0.01 - 4% silicon, 0.05 - 2% manganese, not more than 0.04 % phosphorus, not more than 0.015% sulfur, 10 - 35% chromium, 30 - 78% nickel, not less than 0.005% aluminum, but less than 4.5% aluminum, 0.005 - 0.2% nitrogen and one or both of 0.015 - 3% copper and 0.015 - 3% cobalt, with the remainder being essentially iron.
  • the value of 40 Si + Ni + 5 AI + 40 N + 10 (Cu + Co) is not less than 50, whereby the symbols of the elements represent the alloy content of the respective elements.
  • the metallic material has a excellent corrosion resistance in an environment where metal dusting may occur and therefore can be used in furnace pipes, piping systems, heat exchanger tubes, etc. in a petroleum refinery or petrochemical plants. It can significantly improve the durability and safety of the system.
  • US 3,833,358 A describes an iron-based refractory alloy that offers high resistance to creep, thermal shock, thermal fatigue and intergranular oxidation as well as good weldability, essentially consisting of the following elements (in proportions by weight):
  • EP 0 812 926 A1 describes a nickel-based alloy whose strength increases with use, consisting of 0.06 - 0.14% carbon, 35 - 46% nickel, 22.5 - 26.5% chromium, 0 - 1.5% manganese, 0.5 - 2% silicon, 0.1 - 1% titanium, 0.05 - 2% aluminum, 1 - 3% molybdenum, 0.2 - % niobium, 0.1 - 1% tantalum , 0 - 0.3% tungsten, 0 - 0.008% boron, 0 - 0.05% zirconium and the balance of iron and incidental impurities.
  • WO 2007/124996 A1 describes a reaction container for use in the production of hydrogen sulfide by reaction between sulfur and hydrogen, wherein the reaction container and, if necessary, connecting lines as well as fittings and measuring and control elements consist partially or completely of a material that is resistant to the reaction mixture Contains aluminum.
  • the material contains the components 0 - 0.3% C, 0 - 2.5% Si, 0 - 2.5% Mn, 0 - 0.1% P, 0 - 0.3% S, 15.0 - 28.0% Cr, 0 - 1.0% Cu, 0 - balance % Fe, 1.0 - 5.0% Al, 0 - 2.5% Co, 0 - 1.5% Ti, 0 - 0, 4% Y and up to 70% Ni (% in wt.%).
  • US 5,021,215 A discloses a high-strength, heat-resistant steel with improved formability, which essentially consists of (wt.%):
  • B 0.001 - 0.01%
  • Zr 0.001 - 0.10%
  • at least one element of Ti 0.05 - 1.0%
  • Nb 0.1 - 2.0%
  • JPS 56163244 A describes improving the hot workability and oxidation resistance of an austenitic steel by adding a certain amount of C, Si, Mn, Ni, Cr, Al, B, a rare earth element and Ca to the steel. This is achieved by an austenitic steel containing the following composition in% by weight: ⁇ 0.2% C, 1.5 - 3.5% Si, ⁇ 2% Mn, 8 - 35% Ni, 15 - 30% Cr, ⁇ 2% AI, 0.0005 - 0.005% B, 0.005-0.1% of a rare earth element and 0.0005-0.02% Ca or additionally added 0.0005-0.03% Mg if required.
  • the resulting austenitic steel is refined in an ordinary steel mill furnace, and this molten steel is formed into a billet which is then hot rolled.
  • US 7,118,636 B2 describes a nickel-iron-chromium alloy containing a solidifying phase capable of maintaining a fine grain structure during forging and processing of the alloy at high temperatures.
  • the alloy contains a sufficient amount of titanium, zirconium carbon and nitrogen so that fine titanium and zirconium nitride are formed, although in the molten state of the alloy they are near their solubility limit.
  • a dispersion of the fine titanium and zirconium carbonitride precipitates forms as the melt solidifies and remains in the alloy during subsequent processing steps (at elevated temperatures) to prevent austenitic grain growth.
  • the nickel-iron-chromium alloy contains less than 0.05% by weight niobium, at least 0.05% zirconium, at least 0.05% carbon, at least 0.05% nitrogen, a carbon to nitrogen weight ratio of at least 1 to 2 to less than 1 to 1, sufficient titanium, zirconium and/or aluminum to be free of chromium carbides, and titanium, zirconium, carbon and nitrogen in sufficient amounts to form a uniform dispersion of fine titanium and zirconium carbonitride [( Ti to obtain alloy.
  • This nickel-iron-chromium alloy also consists of about 32% by weight to about 38% by weight iron, about 22% by weight to 28% chromium, about 0.10% to about 0.60% titanium, about 0.05% to about 0.30% zirconium, about 0.05% to about 0.30% carbon, about 0.05% to about 0.30% nitrogen, about 0.05% to about 0.5% Aluminum, up to 0.99% molybdenum, up to about 0.01% boron, up to about 1% silicon, up to about 1% manganese, the balance nickel and incidental impurities.
  • JPS 57134544 A describes improving the stress corrosion cracking resistance of oil drilling pipes by adding certain amounts of Mo, W, etc. to a high Cr-Ni steel as a material for pipes.
  • a high Cr-Ni steel as a material for pipes.
  • an alloy steel with a composition of ⁇ 0.10% C, ⁇ 1.0% Si, ⁇ 2.0% Mn, ⁇ 0.030% P, ⁇ 0.005% S, ⁇ 0.5% Al, 22.5 - 30% Cr, 25 - 60% Ni and Mo and / or W used the equations
  • the steel is used for an oil well pipe used in the highly corrosive, harsh environment of an oil well, natural gas well, etc.
  • the alloy can contain ⁇ 1% Cu and/or ⁇ 2% Co and/or ⁇ 0.10% of one or more of the rare earth elements, ⁇ 0.20% Y, ⁇ 0.10% Mg, ⁇ 0.10% Ca and ⁇ 0.5% Ti are added.
  • Oil well tubing can be manufactured with superior stress corrosion cracking resistance in the highly corrosive oil well environment containing H2S, CO2 and CI.
  • the object underlying this invention is therefore to design the use of a nickel-iron-chromium alloy which a) has good high-temperature corrosion resistance in a highly corrosive environment such as carburizing, sulfiding and chlorinating environments, comparable to that of the alloy 45TM, b) has sufficient workability, in particular weldability, as similar as possible to that of the alloy AC66, and c) has sufficient high temperature strength at 500°C similar to that of alloy AC66.
  • the object on which this invention is based is achieved by using a nickel-iron-chromium alloy with excellent high-temperature corrosion resistance as a powder, the powder consisting of spherical particles with a size of 5 to 250 pm, and this alloy containing (in mass % ): 35.0 to 38% nickel, 26.0 to 30.0% chromium,
  • the nickel content is between 35.0 and 38.0%, with preferred contents being able to be set within the following ranges:
  • the spread range for the element chromium is between 26.0 and 30.0%, with preferred ranges being set as follows:
  • the silicon content is between > 0.70 and 1.50%.
  • Silicon can preferably be set in the alloy within the expansion range as follows:
  • the aluminum content is between 0.40 and 1.30%, although preferred aluminum contents can also be set as follows:
  • Magnesium and/or calcium is also contained in levels of 0.0001 to 0.05%. It is preferably possible to set these elements in the alloy as follows:
  • the alloy contains 0.015 to 0.12% carbon. This can preferably be set in the alloy within the spread range as follows: > 0.015 to ⁇ 0.12%.
  • the alloy also contains phosphorus in levels between 0.001 and 0.030%. Preferred contents can be given as follows:
  • the alloy also contains oxygen in levels between 0.0001 and 0.100%.
  • the element sulfur is present in the alloy at a maximum of 0.010%.
  • Preferred contents can be given as follows:
  • Molybdenum is contained in the alloy with a content of less than 1.0%.
  • the molybdenum content can also be limited as follows:
  • the alloy contains less than 1.0% cobalt.
  • the cobalt content can also be restricted as follows:
  • the alloy may contain less than 0.5% copper.
  • the copper content can also be limited as follows:
  • Tungsten is contained in the alloy with a maximum content of 1.0%.
  • the tungsten content can also be limited as follows:
  • the rest of the alloy consists of iron and the usual manufacturing-related impurities.
  • the iron content can also be restricted as follows:
  • Preferred areas can be set with
  • Oxide layer Additions of oxygen-affining elements such as cerium, lanthanum, yttrium, zirconium and hafnium improve corrosion resistance. They do this by entering the Oxide layer can be installed and block the diffusion paths of oxygen on the grain boundaries.
  • the alloy can contain 0.001 to 0.20% of one or more of the elements cerium, lanthanum, yttrium, zirconium and hafnium, whereby the following formula must be met:
  • FRE 0.714*Ce + 0.720*La + 1 .124*Y + 1 .096*Zr + 0.560*Hf ⁇ 0.10 (2a) where Ce, La, Y, Zr and Hf are the concentration of the relevant elements in mass % are.
  • FRE can preferably be set as follows:
  • cerium mixed metal (abbreviation CeMM) can optionally be used in contents of 0.001 to 0.20%, whereby FRE must be modified as follows:
  • FRE 0.716*CeMM + 1 .124*Y + 1 .096*Zr + 0.560*Hf ⁇ 0.10 (3a) where CeMM, Y, Zr and Hf are the concentration of the relevant elements in mass %.
  • FRE When adding cerium mixed metal, FRE can preferably be set as follows:
  • Cerium, lanthanum, cerium mixed metal, zirconium and hafnium can preferably be contained in the alloy within the spread range as follows:
  • Yttrium can preferably be contained in the alloy within the spreading range as follows:
  • the element titanium can be present in the alloy in amounts of 0.0 to 0.50%. Titanium can preferably be contained in the alloy within the expansion range as follows:
  • the element niobium can be adjusted in contents of 0.0 to 0.2% in the alloy.
  • Niobium can preferably be contained in the alloy within the expansion range as follows:
  • the alloy can also contain 0.0 to 0.20% tantalum.
  • Preferred contents can be given as follows:
  • the alloy can contain a maximum of 0.50% vanadium.
  • the powder according to the invention is preferably produced in a vacuum inert gas atomization system (VIGA).
  • VIGA vacuum inert gas atomization system
  • the alloy is first melted, if necessary openly or in a vacuum, if necessary with subsequent ESR and/or VAR remelting.
  • the powder is then produced by atomizing the alloy melt in the vacuum inert gas atomization system (VIGA).
  • VIM vacuum induction melting furnace
  • the melt is heated in the crucible at 5 to 400°C above the melting point.
  • the metal flow rate during atomization is 0.5 to 80 kg Zmin and the gas flow rate is 2 to 150 m 3 / min.
  • the rapid cooling causes the metal particles to solidify into spherical shapes (spherical particles).
  • the inert gas used during atomization can contain 0.01 to 100% nitrogen if necessary.
  • the gas phase is then separated from the powder in a cyclone and the powder is then packaged.
  • the particles have a particle size of 5 to 250 pm, gas inclusions of 0.0 to 4% pore area (pores > 1 pm) in relation to the total area of evaluated objects, and a bulk density of 2 to the density of the alloy of approx. 8.5 g /cm 3 and are packed airtight under a protective gas atmosphere with argon.
  • the range for the particle size of the powder is between 5 and 250 pm, with preferred ranges being between 5 and 150 pm or 10 and 150 pm.
  • the preferred areas are carried out by separating particles that are too fine and those that are too coarse using a sieving and classifying process. These processes are carried out under a protective gas atmosphere and can be carried out once or several times.
  • the powder has gas inclusions of 0.0 to 4% pore area (pores > 1 pm) in relation to the total area of evaluated objects, with preferred ranges being: 0.0 to 2%
  • the powder has a bulk density of 2 to the density of the alloy of approximately 8.5 g/cm 3 , with preferred ranges being the following values.
  • the amount of gas inclusions in the powder allows for low residual porosity in the parts produced.
  • the inert gas in powder production can optionally be argon or a mixture of argon with 0.01 to ⁇ 100% nitrogen. Possible restrictions on the nitrogen content can be:
  • the inert gas can optionally be helium.
  • the inert gas should preferably have a purity of at least 99.996% by volume.
  • the nitrogen content should be from 0.0 to 10 ppmv, the oxygen content from 0.0 to 4 ppmv and an H2O content of ⁇ 5 ppmv.
  • the inert gas can preferably have a purity of at least 99.999% by volume.
  • the nitrogen content should be 0.0 to 5 ppmv
  • the oxygen content should be 0.0 to 2 ppmv
  • the dew point in the system is in the range of -10 to -120°C. It is preferably in the range from -30 to -100°C.
  • the pressure during powder atomization can preferably be 10 to 80 bar.
  • the powder produced in this way from the alloy can be used for any powder-using manufacturing process for producing components or layers on components.
  • the powder produced in this way can be used in particular for the additive manufacturing of components or layers on components.
  • Additive manufacturing also includes terms such as generative manufacturing, rapid technology, rapid tooling, rapid prototyping or the like.
  • Ultra-high speed laser deposition welding Selective electron beam welding or the like.
  • the components or layers on components produced using additive manufacturing are made up of layer thicknesses of 5 to 600 pm and, immediately after production, have a textured structure with grains stretched in the direction of construction and an average grain size of 2 to 1000 pm.
  • the preferred range is between 5 and 600 pm.
  • the powder made from the alloy can be used for binder jetting processes. In this process, components are built up in layers. However, in comparison to laser melting processes, an organic binder is introduced locally, which ensures the cohesion of the powder particles. After the binder has hardened, the so-called green part is freed from the unbound powder and then debinded and sintered.
  • the processes and extra devices for pre- and post-heating can be advantageous for the powder made from the alloy.
  • EBM process - electron beam melting can be considered as an example.
  • the powder bed is selectively melted layer by layer by the electron beam.
  • the process takes place under high vacuum. This process is therefore particularly suitable for hard materials that have lower ductility and/or for reactive materials.
  • the pre- and/or post-heating device can also be implemented in laser-based processes.
  • the powder made from the alloy can be used, if necessary, to produce the components using HIP (hot isostatic pressing) or conventional sintering and extrusion processes. Furthermore, a process combination of additive manufacturing and subsequent HIP treatment is possible. If necessary, it is also possible to then carry out hot forming and/or, if necessary, cold forming or alternating between hot and cold forming. If necessary, the component can be hot-formed at temperatures between 800 and 1290°C annealed for 0.1 to 70 hours, then hot formed, if necessary with intermediate annealing between 800 and 1290 ° C for 0.05 hours to 70 hours. If necessary, the surface of the material can be chemically and/or mechanically removed (even several times) in between and/or at the end of hot forming for cleaning.
  • HIP hot isostatic pressing
  • cold forming can be carried out with degrees of deformation up to 98%, if necessary with intermediate annealing between 800 and 1250 ° C for 0.05 minutes to 70 hours, if necessary under protective gas, such as argon or hydrogen, followed by cooling in air , in the moving annealing atmosphere or in a water bath.
  • protective gas such as argon or hydrogen
  • the components or layers on components produced from the powder using the various processes can optionally be subjected to solution annealing in the temperature range from 700 to 1250 ° C for 0.1 minutes to 70 hours, if necessary under protective gas, such as. B. argon or hydrogen, followed by cooling in air, in the moving annealing atmosphere or in a water bath.
  • protective gas such as. B. argon or hydrogen
  • the surface can then be cleaned or processed by pickling, blasting, grinding, turning, peeling, milling. Such processing can optionally take place partially or completely before annealing.
  • the components or layers on components made from the powder After annealing, the components or layers on components made from the powder have an average grain size of 2 pm to 2000 pm. The preferred range is between 20 and 600 pm.
  • the components or layers on components produced from the powder according to the invention should preferably be used in areas in which highly corrosive conditions, such as carburizing or sulfiding or chlorinating environments or carburizing and chlorinating environments or carburizing and chlorinating environments or carburizing and sulfiding and chlorinating environments , especially atmospheres, prevail.
  • These environments come e.g. B. for components in waste incineration plants, in pyrolysis plants, in refinery furnaces, in the chemical industry, etc
  • samples measuring 20 x 8 x 4 mm 3 were cut from the semi-finished product of the respective alloys, then drilled with a diameter of 3 mm and then wet-ground with SiC paper up to 1200 grit (grain size ⁇ 15 pm).
  • the samples were degreased and cleaned with isopropanol in an ultrasonic bath.
  • Each sample was suspended in the reaction vessel using this hole over a ceramic crucible so that any flaking corrosion products were collected and the mass of the flaking can be determined by weighing the crucible containing the corrosion products.
  • the sum of the mass of the spalls and the mass change of the samples is the gross mass change of the sample.
  • the specific mass change is the mass change related to the surface of the samples. These are referred to below as rriNetto for the specific net mass change, mGrutto for the specific gross mass change, m S paii for the specific mass change of the spalled oxides.
  • This mixture has a carburizing (60% CO), sulfiding (1% H2S) and chlorinating (0.05% HCl) effect.
  • Tests were carried out at 500°C. The duration of the experiment was 1056 hours each, divided into 11 cycles of 96 hours each. There were two samples per alloy in each test. The values given are the averages of these two samples.
  • the assessment of weldability is based on the extent of the formation of hot cracks during welding. The greater the risk of hot cracks forming, the worse the weldability of a material.
  • the various alloys were tested using the MVT (Modified Varestraint Transvarestraint) test at the BAM (Federal Institute for Materials Research and Testing).
  • MVT Modified Varestraint Transvarestraint
  • BAM Breast Institute for Materials Research and Testing
  • a sample measuring 100 mm x 40 mm x 10 mm is made from the alloy.
  • WIG Tungsten Inert Gas
  • a defined bending strain is applied to the sample.
  • the samples were bent lengthwise to the welding direction (varestraint mode).
  • hot cracks form in a localized test zone on the MVT sample.
  • the tests were carried out with 4% bending elongation, a die speed of 2 mm/s, with a line energy of 7.5 kJ/cm, each under pure argon 4.8.
  • the lengths of all solidification cracks and remelting cracks that are visible on the sample in a light microscope at 25x magnification are determined and added up. Based on these results, the material can then be divided into the category “hot crack-proof” (area 1), “increasing tendency to hot crack” (area 2) and “at risk of hot cracking” (area 3) as shown in Table 2.
  • alloys that are in range 1 “hot crack resistant” and in range 2 “increasing hot cracking tendency” in the MVT test are considered to be easily weldable, since the weldable alloy according to the state of the art AC66 is in range 2. Alloys that are at risk of hot cracking (range 3) are generally difficult to weld. In particular, welding with a welding filler material of the same type (comparable in composition to the material to be welded) is difficult or impossible.
  • the assessment of the high-temperature strength was determined by hot tensile tests. This is determined in a tensile test according to DIN EN ISO 6892-2 at the desired temperature.
  • the yield strength R P o,2, the tensile strength Rm and the elongation A until fracture are determined. The tests were carried out on round samples with a diameter of 6 mm in the measuring range and an initial measuring length Lo of 30 mm.
  • the yield strength R P o.2 or the tensile strength Rm at 500 ° C should at least reach the minimum values for the alloy AC66 according to the state of the art:
  • the grain size is determined using a line cutting method. Manufacturing
  • alloys melted in a vacuum furnace are used on a laboratory scale.
  • Tables 3a and 3b show the analyzes of the laboratory-scale smelted batches along with some state-of-the-art large-scale smelted batches of AC66 (1.4877) and 45TM (2.4889) used for comparison.
  • the batches according to the prior art are marked with a T, those according to the invention with an E.
  • the batches melted on a laboratory scale are marked with an L, the batches melted on an industrial scale with a G.
  • All alloy variants typically had a grain size of 50 to 190 pm.
  • Table 4 shows the results of the corrosion test in the form of gross mass change and spalling at 500°C after 1056 hours in an atmosphere of 60% CO, 30% H2 , 4% CO2 , 1% H2S, 0.05% HCl and 3 .95% H2O. All alloys tested have a chromium content of around 27 to 28%.
  • the state-of-the-art alloy AC66 with only 0.2% silicon shows by far the largest gross mass change of 10.92 mg/cm 2
  • the state-of-the-art alloy 45TM with 2.6% silicon and all tested were melted on a laboratory scale Batches with a silicon content greater than 1.0% show a gross mass change of less than or equal to 2.0 mg/cm 2 (2209, 250098, 250101, 250105, 250102 and 250107). If the aluminum content is also greater than 0.40%, a batch with a silicon content of less than or equal to 1.0% can also have a gross mass change of less than or equal to 2.0 mg/cm 2 if at the same time the formula (1a) Fc ⁇ 2.5 is satisfied.
  • Batches 250084, 250106, 250105, 250108 and 250107 are according to the invention, batch 2209 with a silicon content of greater than 1.50% and batch 250098 with a nickel content of 44.0% are not.
  • the upper limit for nickel is therefore set at a maximum of 40%.
  • alloys 250084 and 250106 according to the invention still show flaking. If the formula (1c) Fc ⁇ 1.0 is also fulfilled, these alloys no longer show any spalling (250107) and, surprisingly, with moderate silicon contents, they also have a very low gross mass change of well below 1.0 mg/cm 2 in the order of magnitude of 45TM with 2.6% silicon and 0.16% aluminum.
  • Table 4 shows the classification of the weldability of the alloys using the MVT test.
  • the weldable alloy according to the state of the art AC66 is in area 2.
  • the alloy 45TM is classified in area 3 (at risk of hot cracking) and therefore has a strong tendency to crack, which makes welding difficult and welding with a specific welding filler material difficult or impossible.
  • Batches not according to the invention with a silicon content greater than or equal to 1.50% greater than 1.50% are all in range 3.
  • the batches with a silicon content are around 1.4% Area 2 (batches 2093, 2101), those with a higher aluminum content already in area 3 (batches 2103, 2096, 2097, 2098).
  • the batches with a silicon content of less than 1.3% are all in range 1 or 2 (AC66, batches 2095, 2102, 250084 to 250108). All laboratory batches according to the invention are in range 1 (batches 250084, 250106, 250105, 250108 and 250107) or Area 2 (Lot 250102).
  • a relatively low nickel content (with a higher iron content (residual)) promotes low corrosion in highly corrosive environments such as carburizing and sulfiding and chlorinating atmospheres. Therefore, a content of 40% is the upper limit of nickel.
  • a nickel content that is too low (at the same time iron content (residue) that is too high) promotes the formation of sigma phases, especially when there is a high chromium content and silicon content. Therefore, a nickel content of 35% is the lower limit.
  • Chromium improves corrosion resistance in a highly corrosive environment such as carburizing and sulfiding and chlorinating atmospheres. Chromium contents that are too low mean that the chromium concentration drops very quickly when the alloy is used in a highly corrosive environment the critical limit drops so that a closed chromium oxide layer can no longer form. Therefore, 26% chromium is the lower limit for chromium when used in highly corrosive environments such as carburizing and sulfiding and chlorinating atmospheres. Too high a chromium content promotes the sigma phase formation of the alloy, especially at high chromium contents. Therefore, 30% chromium is to be regarded as the upper limit.
  • Silicon improves corrosion resistance in a highly corrosive environment such as a carburizing and sulfiding and chlorinating atmosphere. A minimum content of 0.40% is therefore necessary. Contents that are too high, in turn, impair weldability and promote sigma phase formation, especially with high chromium contents. The silicon content is therefore limited to 1.50%.
  • a certain content of aluminum improves corrosion resistance in a highly corrosive environment such as a carburizing and sulfiding and chlorinating atmosphere.
  • a minimum content of 0.40% is therefore necessary. Contents that are too high, in turn, impair weldability, especially with high chromium and silicon contents.
  • the aluminum content is therefore limited to 1.30%.
  • Manganese is useful for improving workability. Manganese is limited to 1.0% because this element reduces high-temperature corrosion resistance.
  • magnesium and/or calcium contents improve processing by binding sulfur, which prevents the occurrence of low-melting NiS eutectics.
  • a minimum content of 0.0001% is therefore required for magnesium and/or calcium. If the content is too high, intermetallic Ni-Mg phases or Ni-Ca phases can occur, which significantly worsen the processability.
  • the magnesium content and/or calcium content is therefore limited to a maximum of 0.05%.
  • a minimum carbon content of 0.015% is necessary for good creep resistance. Carbon is limited to a maximum of 0.12%, as above this level this element reduces processability due to the excessive formation of primary carbides.
  • a minimum nitrogen content of 0.001% is required, which improves the workability and high-temperature strength of the material. Nitrogen is limited to a maximum of 0.150% because this element reduces processability through the formation of coarse carbonitrides.
  • the phosphorus content should be less than or equal to 0.030%, as this surface-active element impairs high-temperature corrosion resistance. Too low a phosphorus content increases costs. The phosphorus content is therefore > 0.001%.
  • the oxygen content must be less than or equal to 0.100% to ensure the alloy can be manufactured. Too low oxygen levels increase costs. The oxygen content is therefore > 0.0001%.
  • Sulfur contents should be kept as low as possible since this surface-active element impairs high-temperature corrosion resistance. A maximum of 0.010% sulfur is therefore specified.
  • Molybdenum is limited to less than 1.0% because this element reduces high-temperature corrosion resistance.
  • Tungsten is limited to less than 1.0% because this element also reduces high-temperature corrosion resistance.
  • Cobalt can be contained in this alloy in less than 1.0%. Higher contents reduce high-temperature corrosion resistance. Copper is limited to less than 0.5% because this element reduces high-temperature corrosion resistance.
  • Fc - 1.2 + 0.29*Ni - 4.6*Si - 4.4*AI ⁇ 2.5 (1a), where Ni, Si and Al and Si are the concentration of the relevant elements in mass % .
  • the limit for Fc has been explained in detail in the previous text.
  • the high-temperature corrosion resistance can be further improved with the addition of oxygen-affinous elements. They do this by being incorporated into the oxide layer and blocking the diffusion paths of oxygen on the grain boundaries.
  • a minimum content of one or more of the elements cerium, lanthanum, cerium mixed metal, yttrium, zirconium and hafnium of 0.001% each is necessary in order to maintain the effect of increasing high-temperature corrosion resistance.
  • the upper limit for each element is set at 0.20% for cost reasons. The following formula must be fulfilled:
  • FRE 0.714*Ce + 0.720*La + 1 .124*Y + 1 .096*Zr + 0.560*Hf ⁇ 0.10 (2a) where Ce, La, Y, Zr, and Hf are the concentration of the relevant elements in mass -% are. This formula limits the total content of elements such as cerium, lanthanum, yttrium, zirconium and hafnium. Contents with FRE > 1.0 can increase corrosion rates again and impair processability.
  • titanium can be added. Titanium increases high temperature strength. From 0.50% the high-temperature corrosion behavior can deteriorate, which is why 0.50% is the maximum value. If necessary, niobium can be added, as niobium also increases high-temperature strength. Higher salaries increase costs significantly. The upper limit is therefore set at 0.20%.
  • the alloy can also contain tantalum, since tantalum also increases high-temperature strength. Higher salaries increase costs significantly.
  • the upper limit is therefore set at 0.20%. A minimum level of 0.001% is required to have an effect.
  • boron can be added to the alloy because boron improves creep resistance. Therefore there should be a content of at least 0.0001%. At the same time, this surface-active element deteriorates the high-temperature corrosion resistance. A maximum of 0.008% boron is therefore specified.
  • vanadium is limited to a maximum of 0.50%, as this element reduces high-temperature corrosion resistance.
  • lead is limited to a maximum of 0.002%, as this element reduces high-temperature corrosion resistance.
  • lead is limited to a maximum of 0.002%, as this element reduces high-temperature corrosion resistance.
  • zinc and tin are the same applies to zinc and tin.
  • Table 2 Classification of weldability according to the total length of solidification and remelting cracks in mm (of the MVT Modified Varestraint-Transvarestraint) - hot crack tests by BAM (Federal Institute for Materials Research and Testing).
  • Table 3a Composition of the laboratory batches and the large-scale comparison batches, part 1. All information in mass% (T: alloy according to the state of the art, E: alloy according to the invention, L: melted on a laboratory scale, G: melted on an industrial scale).
  • Table 3b Composition of the laboratory batches and the large-scale comparison batches, part 2. All information in mass% (applies to all alloys: W: ⁇ 0.01 ; Y ⁇ 0.01; Pb: max. 0.002%, Zn: max. 0.002%, Sn: max. 0.002%) (meaning of T, E, G, L, see table 3a).
  • Figure 1 Depth of corrosion attack on various alloys after aging for 2100 hours in a Prenflo pilot plant in a gas containing FhS as a function of temperature.

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Abstract

L'invention concerne l'utilisation d'un alliage nickel-fer-chrome ayant une excellente résistance à la corrosion à haute température en tant que poudre, la poudre étant constituée de particules sphériques d'une taille de 5 à 250 pm, et ledit alliage comprenant (en % en poids) : 35,0 à 38 % de nickel, 26,0 à 30,0 % de chrome, > 0,7 à 1,50 % de silicium, 0,40 à 1,30 % d'aluminium, 0,00 à 1,0 % de manganèse, 0,0001 à 0,05 % de magnésium et/ou de calcium, 0,015 à 0,12 % de carbone, 0,001 à 0,150 % d'azote, 0,001 à 0,030 % de phosphore, 0,0001 à 0,020 % d'oxygène, un maximum de 0,010 % de soufre, moins de 1,0 % de molybdène, moins de 1,0 % de cobalt, moins de 0,5 % de cuivre, moins de 1,0 % de tungstène, le reste étant du fer et les impuretés habituelles liées au procédé, il est nécessaire de satisfaire l'équation suivante : Fc = - 1.2 + 0.29*Ni - 4.6*Si - 4.4*AI < 2.5 (1 a), où Ni, Si et AI sont la concentration des éléments en question en % en poids.
EP23724164.1A 2022-04-28 2023-04-20 Utilisation d'un alliage nickel-fer-chrome ayant une résistance élevée dans des environnements hautement corrosifs et simultanément une bonne aptitude au traitement et une bonne résistance Pending EP4515011A1 (fr)

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DE102022110384.6A DE102022110384A1 (de) 2022-04-28 2022-04-28 Verwendung einer Nickel-Eisen-Chrom-Legierung mit hoher Beständigkeit in hoch korrosiven Umgebungen und gleichzeitig guter Verarbeitbarkeit und Festigkeit
PCT/DE2023/100283 WO2023208278A1 (fr) 2022-04-28 2023-04-20 Utilisation d'un alliage nickel-fer-chrome ayant une résistance élevée dans des environnements hautement corrosifs et simultanément une bonne aptitude au traitement et une bonne résistance

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CN119710371B (zh) * 2025-02-28 2025-08-08 铸创智能科技(烟台)有限责任公司 一种铁铬镍铝高温合金材料及其应用方法

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