[go: up one dir, main page]

EP1935996A1 - Legierungen mit hoher Temperaturbeständigkeit - Google Patents

Legierungen mit hoher Temperaturbeständigkeit Download PDF

Info

Publication number
EP1935996A1
EP1935996A1 EP08153580A EP08153580A EP1935996A1 EP 1935996 A1 EP1935996 A1 EP 1935996A1 EP 08153580 A EP08153580 A EP 08153580A EP 08153580 A EP08153580 A EP 08153580A EP 1935996 A1 EP1935996 A1 EP 1935996A1
Authority
EP
European Patent Office
Prior art keywords
max
hafnium
chromium
alloy
nickel
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.)
Withdrawn
Application number
EP08153580A
Other languages
English (en)
French (fr)
Inventor
Dominique Flahaut
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Paralloy Ltd
Original Assignee
Paralloy Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from GB0225648A external-priority patent/GB2394959A/en
Priority claimed from GB0324859A external-priority patent/GB0324859D0/en
Application filed by Paralloy Ltd filed Critical Paralloy Ltd
Publication of EP1935996A1 publication Critical patent/EP1935996A1/de
Withdrawn legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0026—Matrix based on Ni, Co, Cr or alloys thereof
    • 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
    • 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
    • C22C19/053—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 30% but less than 40%
    • 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
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • 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
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
    • C22C33/0228—Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • C22C38/02—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
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Definitions

  • This invention relates to high temperature alloys, and more particularly to oxide dispersion strengthened alloys having improved creep resistance and carburisation resistance at high temperatures.
  • high temperature alloys used for example, in the manufacture of alloy tubes for steam methane reforming, suffer from insufficient creep resistance.
  • high temperature alloys for example, alloy tubes used in ethylene pyrolysis, the alloys suffer from insufficient carburisation resistance and, in consequence, insufficient creep resistance.
  • INCOLOY® alloy 803 (UNS S 35045), which is an iron-nickel-chromium alloy specifically designed for use in petrochemical, chemical and thermal processing applications.
  • the composition of INCOLOY 803, by weight, is 25%Cr, 35%Ni, 1%Mn, 0.6%Ti, 0.5%Al, 0.7%Si, 0.07%C and balance Fe. Relatively unsuccessful efforts have been made to improve the properties of this alloy by the addition of further alloying components and also by cladding.
  • alloy creep resistance can be considerably improved by adding a fine dispersion of oxide particles into a metallic matrix, yielding a so-called oxide dispersion strengthened (ODS) alloy.
  • ODS oxide dispersion strengthened
  • Such alloys exhibit a creep threshold, that is to say, below a certain stress their creep rate is very low. This behaviour is commonly explained by interfacial pinning of the moving dislocations at the oxide particle; Bartsch, M., A. Wasilkowska, A. Czyrska-Filemonowicz and U. Messerschmidt Materials Science & Engineering A 272, 152-162 (1999 ). It has recently been proposed to provide oxide dispersion strengthened clad tubes based on INCOLOY 803, but to date no entirely successful commercial product is available
  • the nickel-chromium-iron alloys in the ethylene pyrolysis market which have been produced to have good corrosion resistance and acceptable creep resistance mainly develop an oxide coating layer based on chromium oxide (with in some cases admixed silica).
  • This layer under excessively carburising service conditions high temperature, high carbon activity, low oxygen pressure
  • Alumina is known to be a very stable oxide and ideally it would be desirable to create an alumina layer on the surface of the nickel-chromium-iron alloy, for example, by adding aluminium to the melt.
  • aluminium has two highly detrimental effects on the mechanical properties of such alloys and especially on the creep resistance. Firstly, addition of aluminium to the melt can produce a dispersion of alumina in the alloy that can drastically reduce the creep resistance properties. Secondly, aluminium can form brittle Ni-Al phases in the alloy.
  • the invention provides an improved creep resistant nickel-chromium-iron alloy comprising up to about 5% by weight of hafnium-containing particles.
  • the invention provides an improved oxide dispersion strengthened nickel-chromium-iron alloy which comprises up to about 5% by weight of hafnium, with at least part of the hafnium being present as finely divided oxidised particles.
  • the invention provides a corrosion resistant nickel-chromium-iron-aluminium alloy comprising up to about 15%, preferably up to about 10%, by weight of aluminium and up to about 5% by weight of hafnium-containing particles.
  • the alloys of the invention are castable and can be formed into tubes and coils.
  • the present invention provides an oxide dispersion strengthened castable alloy comprising, by weight: Carbon 0.01 - 0.7% Silicon 0.1 - 3.0% Manganese 0 - 3.0% Nickel 15 - 90% Chromium 5 - 40% Molybdenum 0 - 3.0% Niobium 0 - 2.0% Tantalum 0 - 2.0% Titanium 0 - 2.0% Zirconium 0 - 2.0% Cobalt 0 - 2.0% Tungsten 0 - 4.0% Hafnium 0.01 - 4.5% Aluminium 0 - 15% Nitrogen 0.001 - 0.5% Oxygen 0.001 - 0.7% balance iron and incidental impurities, with the proviso, that at least one carbide forming element whose carbide is more stable than chromium carbide selected from niobium, titanium, tungsten, tantalum and zirconium is present and that at least part of the hafnium is present as finely divided oxide particles.
  • a preferred embodiment of an oxide dispersion strengthened nickel-chromium-iron castable alloy according to the invention comprises, by weight: Carbon 0.01 - 0.5% Silicon 0.01 - 2.5% Manganese 0 - 2.5% Nickel 15 - 50% Chromium 20 - 40% Molybdenum 0 - 1.0% Niobium 0 - 1.7% Titanium 0 - 0.5% Zirconium 0 - 0.5% Cobalt 0 - 2.0% Tungsten 0 - 1.0% Hafnium 0.01 - 4.5% Aluminium 0 - 15% balance iron and incidental impurities, with the proviso, that at least one of niobium, titanium and zirconium is present and that at least part of the hafnium is present as finely divided oxide particles.
  • Preferred alloy compositions according to the invention include the following: Carbon 0.3 to 0.7% Silicon 0.1 to 2.5% Manganese 2.5% max. Nickel 30 to 40% Chromium 20 to 30% Molybdenum 3.0% max. Niobium 2.0% max. Hafnium 0.01 to 4.5% Titanium 0.5% max. Zirconium 0.5% max. Cobalt 2.0% max. Tungsten 1.0% max. Nitrogen 0.001 - 0.5% Oxygen 0.001 - 0.7% Balance iron and incidental impurities. Carbon 0.03 to 0.2% Silicon 0.1 to 0.25% Manganese 2.5% max. Nickel 30 to 40% Chromium 20 to 30% Molybdenum 3.0% max. Niobium 1.7% max. Hafnium 0.01 to 4.5% Titanium 0.5% max. Zirconium 0.5% max.
  • nickel-chromium-iron castable alloys include the following compositions, where all percentages are given by weight: Carbon Silicon Manganese Nickel Chromium Molybdenum A 0.3-0.5 0.1-2.5 2.5max 30-40 20-30 1.0max B 0.03 - 0.2 0.1 - 2.5 2.5 max 30 - 40 20 - 30 1.0 max C 0.3 - 0.6 0.1-2.5 2.5 max 40 - 60 30 - 40 1.0 max D 0.03 - 0.2 0.1 - 2.5 2.5 max 40 - 60 30 - 40 1.0 max E 0.30 - 0.5 0.1 - 2.5 2.5 max 19 - 22 24 - 27 1.0 max F 0.03 - 0.2 0.1 - 2.5 2.5 max 30 - 45 19 - 22 1.0 max Niobium Hafnium Optional Aluminium Titanium Zirconium Cobalt Tungsten A 2 max 0.025 - 4.5 6.0 max 0.5 max 0.5 max 2.0 max 1.0 max B 2 max 0.025 - 4.5 6.0 max 0.5 max 0.5 max 2.0 max 1.0 max B 2
  • the amount of hafnium in the alloy, by weight, is preferably from 0.05 to 3.0%, more preferably from 0.1% to 1.0% and most preferably from 0.2 to 0.5% for the high carbon alloy (0.3 - 0.6% carbon), and more than 1% for the low carbon alloy (0.03 - 0.2% carbon), preferably from 1% to 4.5%.
  • the hafnium is present in the alloy in the form of finely divided oxidised particles having an average particle size of from 50 microns to 0.25 microns, or less, more preferably from 5 microns to 0.25 microns or less.
  • Examples of particularly preferred alloy compositions according to the invention consist essentially of the following components, by weight: Carbon 0.45% Silicon 1.3% Manganese 0.9% Nickel 33.8% Chromium 25.7% Molybdenum 0.03% Niobium 0.85% Hafnium 0.25% Titanium 0.1% Zirconium 0.01% Cobalt 0.04% Tungsten 0.01% Nitrogen 0.1% Iron balance. Carbon 0.07% Silicon 1.0% Manganese 0.98% Nickel 32.5% Chromium 25.8% Molybdenum 0.20% Niobium 0.04% Hafnium 1.1% Titanium 0.12% Zirconium 0.01% Cobalt 0.04% Tungsten 0.08% Nitrogen 0.1% Iron balance.
  • Incidental impurities in the alloys of the invention can comprise, for example, phosphorus, sulphur, vanadium, zinc, arsenic, tin, lead, copper and cerium, up to a total amount of about 1.0%.
  • the invention provides a method of manufacturing an oxide dispersion strengthened castable nickel-chromium-iron alloy which comprises adding finely divided hafnium particles to a melt of the alloy before pouring, under conditions such that at least part of the hafnium is converted to oxide in the melt.
  • the alloys of the invention it is important to provide conditions in the melt which permit oxidation of the hafnium particles without allowing detrimental reactions which would result in the hafnium (with or without aluminium) being taken up in the slag.
  • the correct oxidising conditions can be achieved by appropriate adjustment or additions of the components, example, silicon and/or manganese, and by ensuring that unwanted contaminants are absent or kept to a minimum. If the slag is able to react with the oxidised hafnium particles this of course removes them detrimentally from the melt.
  • the level of oxygen in the melt can be varied by additions of, for example, one or more of silicon, niobium, titanium, zirconium, chromium, manganese, calcium and the optimum free oxygen level necessary to react with the hafnium particles can readily be found by routine experimentation.
  • any such micro-additions are made after the addition of hafnium.
  • alloying amounts of titanium and/or zirconium may be added, up to the specified limits of 0.5% by weight in each case.
  • the substantial removal of available free oxygen from the melt helps to ensure that any such titanium and/or zirconium additions do not form oxides, which could react detrimentally with the hafnium particles and reduce the yields of titanium, zirconium and hafnium present in the alloy.
  • hafnium is added to the melt as finely divided particles and that it is oxidised in situ.
  • hafnium added to nickel/chromium alloys in non-particulate form does not disperse, or reacts only with the carbon/nitrogen present resulting in a decrease of the alloy properties.
  • Attempts to add large pieces of hafnium to nickel/chromium micro-alloys have revealed that the hafnium does not disperse, but settles to the bottom of the alloy melt, and so is not present in the final casting.
  • hafnia hafnium oxide particles directly to the melt does not provide the desired dispersion strengthening either. Hafnia added in this way simply goes into the slag. According to the invention it has been found that it is necessary to carry out the oxidation of the hafnium particles in the melt in order to obtain the desired improvements.
  • the charge make up can be a virgin charge (pure metals), a mixture of virgin charge and reverts, a mixture of virgin charge and ingots, or a mixture of virgin charge and reverts and ingots.
  • the ingots can be made from argon/oxygen decarburisation (AOD) revert alloy treatment or from in-house reverts treated, for example, by argon purging. In each case the chemical composition of the melt should be carefully monitored to avoid contaminants and the formation of unwanted slag.
  • the melt temperature is preferably in the range of from 1500°C to 1700 °C, preferably from 1610 °C to 1670 °C for nickel-chromium-Iiron, and 1630°C to 1690C for nickel-chromium-iron-aluminium.
  • Hafnium particles are preferably added to the melt just before pouring the molten alloy into the mould. If a ladle is used, the hafnium is preferably added in the ladle. To improve the hafnium dispersion, the molten alloy is preferably stirred before pouring.
  • hafnium particles are preferably reduced in size as much as possible, for example, by grinding to a fine powder in a suitable mill.
  • the hafnium particles preferably have a particle size of less than 5 mm, preferably less than 4 mm, with an average particle size of from 1 to 2 mm. When dispersed in the melt, the hafnium particles are further reduced in size.
  • the high carbon alloys of the invention (0.3 - 0.6% carbon) have a primary carbide network similar to the corresponding alloys without the oxide dispersion.
  • the primary carbides are mainly composed of chromium and/or iron carbo-nitrides, optionally with niobium, titanium and/or zirconium carbo-nitrides also present.
  • the invention also provides the possibility of obtaining a dispersion of secondary carbides after the alloy has been brought to a high temperature.
  • These secondary carbides are mainly chromium (or other elements such as iron) carbo-nitrides and optionally niobium, titanium (and/or zirconium) carbo-nitrides.
  • the low carbon alloys of the invention (0.03 - 0.2% carbon) can contain a dispersion of carbides, carbonitrides, or nitrides, for example, titanium nitrides, titanium carbo-nitrides, niobium carbides, niobium carbonitrides, niobium nitrides, zirconium nitrides, zirconium carbo-nitrides, zirconium carbides, tantalum carbides, tantalum carbo-nitrides, tantalum nitrides, tungsten carbides, tungsten nitrides, and/or tungsten carbonitrides.
  • titanium nitrides titanium carbo-nitrides, niobium carbides, niobium carbonitrides, niobium nitrides, zirconium nitrides, zirconium carbo-nitrides, zirconium carbides, tantalum carbides, tantalum carb
  • the invention provides for the formation of a hafnia / hafnium oxide dispersion (the hafnium can be oxidised to form HfO 2 , but it can be expected that there will also be formed an oxide HfO x with x as a variable).
  • alloys containing more than a trace of niobium and titanium for example, high carbon nickel-chromium-iron alloys, hafnium/niobium/titanium carbo-nitrides and (rarely) oxides mixtures (wherein the quantities of niobium and titanium are variable as well as the quantities of nitrogen and oxygen) can be expected to be present.
  • more numerous titanium nitride (and/or carbide) dispersions may be observed in the alloy, some of which may also contain hafnia particles. It is also possible that some hafnium carbo-nitrides may be formed.
  • an oxide dispersion strengthened nickel-chromium-iron alloy which comprises up to about 5% by weight of hafnium, with at least part of the hafnium being present as finely dispersed oxidised particles, the alloy having a carbon content of from 0.3% to 0.5% by weight and having improved high temperature creep resistance, leading to an improved service life expectancy.
  • the creep resistance of such high carbon alloys in the substantial absence of aluminium, derives from the ability of the particle dispersion to delay the motion of the dislocations in the alloy lattice.
  • the invention provides an oxide dispersion strengthened nickel-chromium-iron alloy, which comprises up to about 5% of hafnium, with at least part of the hafnium being present as finely dispersed oxidised particles, the alloy having a carbon content of from 0.03% - 0.2%, preferably 0.03% - 0.1%, more preferably 0.03% - 0.08%, for example, about 0.05% - 0.07%, and a significantly increased service temperature, preferably greater than 1150°C.
  • the improved high temperature performance of the new low carbon alloys of this further aspect of the invention is due to the replacement of the strengthening carbide dispersion by a hafnia dispersion which is more stable than the carbide at high temperature.
  • An example of a low carbon oxide dispersion strengthened alloy is alloy B in Table 1 (wherein aluminium is absent).
  • the nickel-chromium-iron alloy of the invention also comprises aluminium
  • the aluminium is preferably present in an amount of from 0.1% to 10% by weight, more preferably from 0.5% to 6% by weight and most preferably from 1.0 to 5% by weight.
  • a method of manufacturing a carburisation resistant nickel-chromium-iron alloy which comprises adding sequentially finely divided hafnium particles and aluminium to a melt of the alloy before pouring.
  • the aluminium is added to the melt immediately before pouring the molten alloy into the mould.
  • hafnium limits the amount of available oxygen in the alloy able to react with the aluminium and minimises or eliminates the formation of a detrimental dispersion of alumina particles.
  • the alloys of the invention can be formed into tubes, for example, by rotational moulding, and such rotationally moulded tubes are a further aspect of the invention.
  • the rotational moulding process can provide a non-uniform particle distribution in the tube wall, with the greater concentration of particles being towards the outer surface of the tube wall, and this can be beneficial in some cases.
  • the internal bore of the tube is machined, removing 4-5 mm of material; this gradient of concentration ensures that the hafnium/hafnia reinforcement is kept in the useful part of the tube.
  • Other components that can be manufactured from the new alloys include fittings, fully fabricated ethylene furnace assemblies, reformer tubes and manifolds.
  • hafnium addition For high chromium content (more than 10%) alloys, a further advantage of the hafnium addition is that it can tend to improve the oxide layer adherence at the surface of an alloy tube.
  • nickel-chromium-iron alloys are used in ethylene furnaces, they are able to develop an oxide layer on the surface that protects the alloy against corrosion by carburisation.
  • This protective oxide layer is formed ideally of chromium/manganese/silicon oxides, but can also include iron and nickel oxides.
  • the oxide layer has a tendency to spall during the tube service life (because of differences of coefficients of expansion with the alloy, compressive stresses in the oxide, etc). Spalling leaves the alloy unprotected against corrosion from the gaseous and particulate reactants of the ethylene cracking process. It has surprisingly been found that the addition of hafnium as described herein can tend to delay the spalling of the protective oxide layer.
  • the following melt composition is produced in a clean furnace: Nickel 35% Chromium 25% Carbon 0.4% Niobium 0.8 - 0.9% Silicon 1.6 - 1.8% Manganese 1.1 - 1.3% Iron balance.
  • the temperature of the melt is raised to a tap temperature of from 1640°C to 1650°C and the silicon content checked to obtain the correct oxidising conditions.
  • the furnace is then de-slaged, removing as much slag as possible.
  • 100kg of alloy are then tapped into a ladle and 0.35% hafnium particles of particle size maximum 5 mm, average 1 to 2 mm, are added to the tap stream. After the hafnium addition, 0.18% titanium, in the form of FeTi is added to the ladle.
  • the alloy in the ladle is stirred and immediately poured into a tube mould.
  • the creep resistance properties of the alloy thus produced were compared with the properties of an otherwise identical commercial alloy without hafnium.
  • Example 1 The procedure of Example 1 is repeated using the same melt composition except that the titanium addition is omitted.
  • the creep resistance properties of the alloy thus produced were compared with the properties of an otherwise identical commercial alloy from which the hafnium addition was omitted.
  • the results of a Larson-Miller plot of the stress-rupture properties of the commercial alloy derived from the regression analysis of numerous creep tests gave a typical figure of 16.2 MPa at a temperature of 1100°C.
  • the commercial alloy is expected to fail after a minimum of 100 hours, with a mean value failure of 202 hours.
  • the alloy according to the invention had a minimum failure time of rupture of 396 hours, a mean value failure of 430 hours and a maximum failure time of rupture of 629 hours.
  • This example describes the production of a low carbon oxide dispersion strengthened alloy according to the invention.
  • the following melt composition is produced in a clean furnace: Nickel 33% - 35% Chromium 24% - 26% Carbon 0.04% - 0.08% Silicon 1.0% - 1.2% Manganese 1.0% - 1.2% Molybdenum 0.14% - 0.3% Iron balance.
  • the temperature of the melt is raised to a tap temperature of from 1640°C to 1650°C and the silicon content checked.
  • the furnace is then de-slaged, removing as much slag as possible.
  • 100kg of alloy are then tapped into a ladle and 0.75% hafnium particles of particle size maximum 5 mm, average 1 - 2 mm, are added to the tap stream.
  • 0.25% titanium, in the form of FeTi is added to the ladle.
  • FIG. 5 A photomicrograph of the alloy is shown in Figure 5 .
  • the dispersed oxidised particles can clearly be seen.
  • Example 3 The procedure of Example 3 is repeated using the same melt composition except that the hafnium addition is 0.5%.
  • a photomicrograph of the alloy is shown in Figure 6 .
  • the dispersed oxidised particles can clearly be seen.
  • Examples 3 and 4 show a higher solidus than the high carbon alloys of Examples 1 and 2, indeed their solidus is 1344°C instead of 1260°C for the high carbon alloys.
  • This Example describes the production of an oxide dispersion strengthened nickel-chromium-iron alloy according to the invention comprising both hafnium and aluminium.
  • a nickel-chromium-iron alloy melt having the following constituents by weight is formed in a clean furnace and brought to tapping temperature.
  • Example 5 has been tested to confirm that aluminium can improve the carburisation resistance of a hafnium-containing alloy according to the invention.
  • a very severe pack-carburisation test was performed, the results of which are shown in Figure 9 .
  • the creep resistance of the alloy was found to be substantially maintained compared to an identical alloy without hafnia and aluminium additions. Indeed only a decrease of maximum 20% in creep resistance was observed compared to an identical alloy without hafnium and aluminium additions.
  • an identical alloy with an aluminium addition, but without hafnium showed a decrease in creep resistance of 80%.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Ceramic Products (AREA)
EP08153580A 2002-11-04 2003-10-30 Legierungen mit hoher Temperaturbeständigkeit Withdrawn EP1935996A1 (de)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
GB0225648A GB2394959A (en) 2002-11-04 2002-11-04 Hafnium particle dispersion hardened nickel-chromium-iron alloys
GBGB0228576.5A GB0228576D0 (en) 2002-11-04 2002-12-09 High temperature alloys
GB0324859A GB0324859D0 (en) 2002-11-04 2003-10-24 High temperature alloys
EP03775499A EP1558776B8 (de) 2002-11-04 2003-10-30 Hochtemperaturbeständige legierungen

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
EP03775499A Division EP1558776B8 (de) 2002-11-04 2003-10-30 Hochtemperaturbeständige legierungen

Publications (1)

Publication Number Publication Date
EP1935996A1 true EP1935996A1 (de) 2008-06-25

Family

ID=29740472

Family Applications (2)

Application Number Title Priority Date Filing Date
EP08153580A Withdrawn EP1935996A1 (de) 2002-11-04 2003-10-30 Legierungen mit hoher Temperaturbeständigkeit
EP03775499A Expired - Lifetime EP1558776B8 (de) 2002-11-04 2003-10-30 Hochtemperaturbeständige legierungen

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP03775499A Expired - Lifetime EP1558776B8 (de) 2002-11-04 2003-10-30 Hochtemperaturbeständige legierungen

Country Status (6)

Country Link
US (1) US20070144622A1 (de)
EP (2) EP1935996A1 (de)
JP (1) JP2006505694A (de)
AU (1) AU2003283525A1 (de)
GB (1) GB2394960B (de)
WO (1) WO2004042100A2 (de)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2448194C1 (ru) * 2011-04-14 2012-04-20 Открытое акционерное общество Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" (ОАО НПО "ЦНИИТМАШ") Жаропрочный сплав
WO2021254028A1 (zh) * 2020-06-17 2021-12-23 大连理工大学 一种b2纳米粒子共格析出强化的超高强度马氏体时效不锈钢及制备方法

Families Citing this family (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB0407531D0 (en) * 2004-04-02 2004-05-05 Univ Loughborough An alloy
FR2922636B1 (fr) * 2007-10-19 2012-06-08 Manoir Ind Tube a surface interne augmentee utilise dans des fours, procede de fabrication et applications
US8430075B2 (en) * 2008-12-16 2013-04-30 L.E. Jones Company Superaustenitic stainless steel and method of making and use thereof
US8479700B2 (en) * 2010-01-05 2013-07-09 L. E. Jones Company Iron-chromium alloy with improved compressive yield strength and method of making and use thereof
US9689615B2 (en) * 2012-08-21 2017-06-27 Uop Llc Steady state high temperature reactor
US9656229B2 (en) * 2012-08-21 2017-05-23 Uop Llc Methane conversion apparatus and process using a supersonic flow reactor
US10029957B2 (en) * 2012-08-21 2018-07-24 Uop Llc Methane conversion apparatus and process using a supersonic flow reactor
US10160697B2 (en) * 2012-08-21 2018-12-25 Uop Llc Methane conversion apparatus and process using a supersonic flow reactor
US9707530B2 (en) * 2012-08-21 2017-07-18 Uop Llc Methane conversion apparatus and process using a supersonic flow reactor
CN103361642B (zh) * 2013-07-23 2015-08-12 中国矿业大学 一种等离子熔覆梯度耐磨层及制备工艺
DE102014001329B4 (de) * 2014-02-04 2016-04-28 VDM Metals GmbH Verwendung einer aushärtenden Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit
CN104087786B (zh) * 2014-06-25 2016-06-15 盐城市鑫洋电热材料有限公司 一种镍铬电热复合材料及其制备方法
CN104233040A (zh) * 2014-09-18 2014-12-24 丹阳惠达模具材料科技有限公司 一种用于模具表面激光熔覆的镍基金属陶瓷合金粉末
EP3202932B1 (de) * 2014-09-29 2019-03-20 Nippon Steel & Sumitomo Metal Corporation Rohr aus einer legierung auf nickelbasis
RU2716966C2 (ru) * 2015-02-17 2020-03-17 Хеганес Аб (Пабл) Сплав на основе никеля с высоким интервалом плавления, пригодный для высокотемпературной пайки супераустенитной стали
US10415121B2 (en) * 2016-08-05 2019-09-17 Onesubsea Ip Uk Limited Nickel alloy compositions for aggressive environments
GB201713066D0 (en) 2017-08-15 2017-09-27 Paralloy Ltd Oxidation resistant alloy
JP7131318B2 (ja) * 2018-11-14 2022-09-06 日本製鉄株式会社 オーステナイト系ステンレス鋼
CN115722184B (zh) * 2021-08-31 2024-04-02 中国石油化工股份有限公司 一种吸附脱硫剂及其制备方法和应用
CN115679209B (zh) * 2022-10-14 2024-02-09 成都先进金属材料产业技术研究院股份有限公司 一种低合金含钨超高强钢及其生产方法
WO2024232408A1 (ja) * 2023-05-10 2024-11-14 株式会社クボタ 耐窒化性にすぐれる耐熱合金
JP7587078B1 (ja) 2023-05-10 2024-11-19 株式会社クボタ 耐窒化性にすぐれる耐熱合金
CN119410957A (zh) * 2025-01-07 2025-02-11 北京赛亿科技有限公司 一种掺杂稀土的耐高温耐化学性合金材料及其制备方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5284135A (en) * 1976-11-08 1977-07-13 Mitsubishi Heavy Ind Ltd Carburizinggresisting alloys
EP0050408A1 (de) * 1980-09-05 1982-04-28 Firth Brown Limited Austenitischer Stahl und Stäbe, Knüppel, Drähte, Brammen, Grobbleche, Feinbleche, Röhren oder Schmiedestücke
EP0391381A1 (de) * 1989-04-05 1990-10-10 Kubota Corporation Hitzebeständige Legierung
JPH051355A (ja) * 1991-06-21 1993-01-08 Kubota Corp クリープ破断強度の改良された耐熱鋳鋼
US5851318A (en) * 1995-06-09 1998-12-22 Krupp Vdm Gmbh High temperature forgeable alloy
EP1065290A1 (de) * 1999-06-30 2001-01-03 Sumitomo Metal Industries, Ltd. Hitzebeständige Nickelbasislegierung
US20010001399A1 (en) * 1996-07-25 2001-05-24 Willi Kleemann Austenitic nickel-chromium steel alloys

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB959442A (en) * 1960-06-13 1964-06-03 Du Pont Improvements in or relating to metalliferous compositions
US3556744A (en) * 1965-08-16 1971-01-19 United Aircraft Corp Composite metal article having nickel alloy having coats containing chromium and aluminum
US3479180A (en) * 1967-05-24 1969-11-18 Fansteel Metallurgical Corp Process for making chromium alloys of dispersion-modified iron-group metals,and product
BE794142A (fr) * 1972-01-17 1973-07-17 Int Nickel Ltd Alliages pour hautes temperatures
US3864093A (en) * 1972-11-17 1975-02-04 Union Carbide Corp High-temperature, wear-resistant coating
EP0065812B1 (de) * 1981-04-08 1986-07-30 Johnson Matthey Public Limited Company Nickellegierung mit hohem Chromgehalt
DE3606804A1 (de) * 1986-03-01 1987-09-10 Thyssen Huette Ag Metallisches halbzeug und verfahren zu seiner herstellung sowie verwendung
EP0246092A3 (de) * 1986-05-15 1989-05-03 Exxon Research And Engineering Company Durch Spannungskorrosion gegen Rissbildung beständige Legierungen
JPS63259051A (ja) * 1987-04-14 1988-10-26 Nippon Steel Corp 耐サワ−性の優れた高靭性電縫鋼管用鋼
CH674019A5 (de) * 1988-01-18 1990-04-30 Asea Brown Boveri
AT391435B (de) * 1988-04-14 1990-10-10 Plansee Metallwerk Verfahren zur herstellung einer odssinterlegierung
US4877435A (en) * 1989-02-08 1989-10-31 Inco Alloys International, Inc. Mechanically alloyed nickel-cobalt-chromium-iron composition of matter and glass fiber method and apparatus for using same
SU1763511A1 (ru) * 1990-11-05 1992-09-23 Орский Механический Завод Сталь
US5712050A (en) * 1991-09-09 1998-01-27 General Electric Company Superalloy component with dispersion-containing protective coating
JPH0674481B2 (ja) * 1992-03-13 1994-09-21 松下電工株式会社 Ｆｅ−Ｃｒ−Ｎｉ−Ａｌ系フェライト合金
US5328499A (en) * 1993-04-28 1994-07-12 Inco Alloys International, Inc. Mechanically alloyed nickel-base composition having improved hot formability characteristics
GB2394959A (en) * 2002-11-04 2004-05-12 Doncasters Ltd Hafnium particle dispersion hardened nickel-chromium-iron alloys

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5284135A (en) * 1976-11-08 1977-07-13 Mitsubishi Heavy Ind Ltd Carburizinggresisting alloys
EP0050408A1 (de) * 1980-09-05 1982-04-28 Firth Brown Limited Austenitischer Stahl und Stäbe, Knüppel, Drähte, Brammen, Grobbleche, Feinbleche, Röhren oder Schmiedestücke
EP0391381A1 (de) * 1989-04-05 1990-10-10 Kubota Corporation Hitzebeständige Legierung
JPH051355A (ja) * 1991-06-21 1993-01-08 Kubota Corp クリープ破断強度の改良された耐熱鋳鋼
US5851318A (en) * 1995-06-09 1998-12-22 Krupp Vdm Gmbh High temperature forgeable alloy
US20010001399A1 (en) * 1996-07-25 2001-05-24 Willi Kleemann Austenitic nickel-chromium steel alloys
EP1065290A1 (de) * 1999-06-30 2001-01-03 Sumitomo Metal Industries, Ltd. Hitzebeständige Nickelbasislegierung

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
BARTSCH, M.; A. WASILKOWSKA, A. CZYRSKA-FILEMONOWICZ AND U. MESSERSCHMIDT MATERIALS SCIENCE & ENGINEERING A, vol. 272, 1999, pages 152 - 162

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2448194C1 (ru) * 2011-04-14 2012-04-20 Открытое акционерное общество Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" (ОАО НПО "ЦНИИТМАШ") Жаропрочный сплав
WO2021254028A1 (zh) * 2020-06-17 2021-12-23 大连理工大学 一种b2纳米粒子共格析出强化的超高强度马氏体时效不锈钢及制备方法

Also Published As

Publication number Publication date
GB0325297D0 (en) 2003-12-03
EP1558776A2 (de) 2005-08-03
GB2394960B (en) 2007-04-25
AU2003283525A8 (en) 2004-06-07
US20070144622A1 (en) 2007-06-28
GB2394960A (en) 2004-05-12
WO2004042100A3 (en) 2004-08-19
JP2006505694A (ja) 2006-02-16
AU2003283525A1 (en) 2004-06-07
WO2004042100A2 (en) 2004-05-21
EP1558776B8 (de) 2009-04-29
EP1558776B1 (de) 2008-08-13

Similar Documents

Publication Publication Date Title
EP1558776B1 (de) Hochtemperaturbeständige legierungen
US20100175508A1 (en) High temperature alloys
EP2725112B1 (de) Aufkohlungsresistentes metallmaterial und anwendungen des aufkohlungsresistenten metallmaterials
EP1867740B1 (de) Nickel-Superlegierung mit geringer Wärmeausdehnung
EP1975267B1 (de) Metallmaterial mit hervorragender metal-dusting-beständigkeit
EP2430204B1 (de) Legierung auf nickelbasis für ventilsitzeinsätze
KR101698075B1 (ko) 우수한 가공성, 내크리프성 및 내부식성을 갖는 니켈-크롬 합금
RU2599324C2 (ru) Хромоникелевоалюминиевый сплав с хорошими показателями обрабатываемости, предела ползучести и коррозионной стойкости
KR101403553B1 (ko) 고온 저열팽창 Ni-Mo-Cr 합금
EP1945826B1 (de) Hochfeste und korrosionsresistente legierung für anwendungen in ölfeldern
RU2518812C2 (ru) Сплав на основе никеля, способный образовывать оксид алюминия
FI3775308T3 (fi) Nikkeli-kromi-rauta-alumiini-metalliseoksen käyttö
US7922969B2 (en) Corrosion-resistant nickel-base alloy
EP3616828B1 (de) Ni-cr-basiertes legierungslötmaterial mit spuren von v
EP1947207B1 (de) Hitzeresistente legierung mit fähigkeit zur abscheidung von feinem ti-nb-cr-carbid oder ti-nb-zr-cr-carbid
EP3650560B1 (de) Oxidationsbeständige hitzebeständige legierung und herstellungsverfahren
JP2819906B2 (ja) 室温および高温強度に優れた工具用Ｎｉ基合金
JP4846373B2 (ja) 耐熱鋳鋼
JP3901801B2 (ja) 耐熱鋳鋼および耐熱鋳鋼部品
CN112030041B (zh) 一种在含氧氢氟酸中具有耐腐蚀性的MonelK500A合金
JPS6173853A (ja) 耐熱合金
KR20240160625A (ko) 침탄 및 황화 및 염소화 환경에서 높은 저항성 및 동시에 우수한 가공성 및 강도를 갖는 니켈-철-크롬 합금의 용도
WO2024235867A1 (en) A nickel-base alloy, an object made thereof and the use thereof
CN117070857A (zh) 一种马氏体耐热钢及其生产方法

Legal Events

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

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20080328

AC Divisional application: reference to earlier application

Ref document number: 1558776

Country of ref document: EP

Kind code of ref document: P

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

RIN1 Information on inventor provided before grant (corrected)

Inventor name: FLAHAUT, DOMINIQUE

17Q First examination report despatched

Effective date: 20090202

AKX Designation fees paid

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

RBV Designated contracting states (corrected)

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GR HU IE IT LI LU MC NL PT RO SE SI SK TR

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

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20120501