GB2394959A - Hafnium particle dispersion hardened nickel-chromium-iron alloys - Google Patents

Hafnium particle dispersion hardened nickel-chromium-iron alloys Download PDF

Info

Publication number
GB2394959A
GB2394959A GB0225648A GB0225648A GB2394959A GB 2394959 A GB2394959 A GB 2394959A GB 0225648 A GB0225648 A GB 0225648A GB 0225648 A GB0225648 A GB 0225648A GB 2394959 A GB2394959 A GB 2394959A
Authority
GB
United Kingdom
Prior art keywords
max
alloy
hafnium
chromium
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Withdrawn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
GB0225648A
Other versions
GB0225648D0 (en
Inventor
Dominique Marianne Luc 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.)
Doncasters PLC
Original Assignee
Doncasters PLC
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
Application filed by Doncasters PLC filed Critical Doncasters PLC
Priority to GB0225648A priority Critical patent/GB2394959A/en
Priority to GBGB0228576.5A priority patent/GB0228576D0/en
Publication of GB0225648D0 publication Critical patent/GB0225648D0/en
Priority to GB0324859A priority patent/GB0324859D0/en
Priority to JP2004549307A priority patent/JP2006505694A/en
Priority to US10/533,034 priority patent/US20070144622A1/en
Priority to EP03775499A priority patent/EP1558776B8/en
Priority to EP08153580A priority patent/EP1935996A1/en
Priority to ES03775499T priority patent/ES2312831T3/en
Priority to AU2003283525A priority patent/AU2003283525A1/en
Priority to PCT/GB2003/004665 priority patent/WO2004042100A2/en
Priority to AT03775499T priority patent/ATE404706T1/en
Priority to DE60322935T priority patent/DE60322935D1/en
Priority to GB0325297A priority patent/GB2394960B/en
Priority to EP03810516A priority patent/EP1560940A2/en
Priority to CA002504937A priority patent/CA2504937A1/en
Priority to AU2003301837A priority patent/AU2003301837A1/en
Priority to JP2004549337A priority patent/JP2006517255A/en
Priority to PCT/GB2003/004754 priority patent/WO2004042101A2/en
Publication of GB2394959A publication Critical patent/GB2394959A/en
Priority to US10/533,850 priority patent/US20060096673A1/en
Priority to US12/561,057 priority patent/US20100175508A1/en
Withdrawn legal-status Critical Current

Links

Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/002Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C32/00Non-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
    • C22C32/001Non-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
    • C22C32/0015Non-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
    • C22C32/0026Matrix based on Ni, Co, Cr or alloys thereof
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C33/00Making ferrous alloys
    • C22C33/02Making ferrous alloys by powder metallurgy
    • C22C33/0207Using a mixture of prealloyed powders or a master alloy
    • C22C33/0228Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C33/00Making ferrous alloys
    • C22C33/02Making ferrous alloys by powder metallurgy
    • C22C33/0257Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278Making 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%
    • C22C33/0285Making 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%
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Powder Metallurgy (AREA)
  • Ceramic Products (AREA)
  • Glass Compositions (AREA)
  • Manufacture And Refinement Of Metals (AREA)

Abstract

An oxide dispersion strengthened nickel-chromium-iron alloy comprising (in % by weight): Ni 15-50%, Cr 20-40%, Hf 0.01-4.5 %, C 0.01-0.5 %, Si 0.01-2.5 %, Mn0-2.5 %, Mo 0-1.0 %, Nb 0-1.7 %, Ti 0-0.5 %, Zr 0-0.5 %, Co 0-2.0 %, W 0-1.0 %, with the balance being Fe and impurities. At least one of niobium, titanium and zirconium are present and at least part of the hafnium exists as oxide particles. Embodiments are also specified where the chromium range is 19-22 % by weight and the cobalt maximum is 2.05 weight %. The alloy may be used for making into tubes by rotational moulding. The alloy is made by adding hafnium particles to a melt held in a ladle before pouring under conditions such that at least part of the hafnium is oxidised in the melt.

Description

GB 2394959 A continuation (52) cont C7D DJB D805 D807 D810D811 D812 D814
D815 D816
D818 D819 D822 D823 D824 D825 D827 D828D829
D831 D834 D835 D836 D838 D839
(56) Docu meets Cited: EP 0384608 A1 EP 0246092 A2
EP 0065812 A1 JP 630259051 A
SU 001763511 A1 US 5328499 A
(58) Field of Search:
INT CL7 C22C
Other: Online: PAJ, WPI
Bigh Temperature Alloys This invention relates to high temperature alloys, and more particularly to an oxide dispersion strengthened 5 nickelchromium-iron alloy having improved creep resistance and oxidation resistance at high temperatures.
Frequently alloy materials for use at high temperatures, for example, alloy tubes used in ethylene pyrolysis and 10 in steam methane reforming, suffer from insufficient creep resistance. The industry continues to look for improved materials and other technologies to enable more efficient ethylene production under increasingly severe pyrolysis/cracking conditions (higher temperatures, 15 shorter residence times, and lower partial pressures of product), leading to increased ethylene yields. Current alloys have specific issues related to their creep performance which causes failure at increasingly high design process temperatures. This is the case currently 20 for both castable alloy tubes and wrought alloy tubes.
An example of a known alloy material is INCOLOY alloy 803 (UNS S 35045), which is an iron-nickel-chromium alloy 25 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 30 properties of this alloy by the addition of further alloying components and also by cladding.
It has been known for about thirty years that alloy creep resistance can be considerably improved by adding a fine 35 dispersion of oxide particles into a metallic matrix,
À Àee.e..e e e e ÀÀ À À
ÀÀÀ À À
À À....
Àee ee. Àe Àe À.
yielding a so-called oxide dispersion strengthened (ODS) alloy. Such alloys show a creep threshold, that is to say, below a certain stress their creep rate is very low.
This behaviour is commonly explained by interracial 5 pinning of the moving dislocations at the oxide particle; Bartsch, M., A. Wasilkowska, A. Czyrska-Filemonowicz and U. Messerschmidt Ma serial s Science Engineering A 272, 152-162 (1999). It has recently been proposed to provide oxide dispersion strengthened clad tubes based on INCOLOY 10 803, but to date no entirely successful commercial product is available (www. oit.doe.gov/imf/factsheets/mtu tubes).
According to the present invention, an improved creep 15 resistant nickelchromium-iron alloy comprises up to about 5% of hafnium-containing particles. The alloy is particularly useful in the production of creep resistant tubes. 20 Also according to the invention, an improved oxide dispersion strengthened nickel-chromium-iron alloy is provided, which comprises up to about 5% of hafnium, with at least part of the hafnium being present as finely dispersed oxidised particles.
In a first aspect, the present invention provides an oxide dispersion strengthened nickel-chromium-iron alloy comprising, by weight: 30 Carbon 0.01 - 0.5% Silicon 0.1 - 2.5% Manganese 0 - 2.5% Nickel 15 - 50% Chromium 20 - 40% 35 Molybdenum 0 - 1.0%
: t;'.t'\:...,:i _t'_i:.'?.;':: ,i. 1,'j'.'.'\..:i'.:.:;' A::.:._.::.:_:. :::: I.':\ A.:'.': At..!:.,';_.:'._::'.':.',._,,'.::.: 9 '..,'J'_:'1'.:'.. !. 'S. I:.:.:.::,:,i À e ee.ÀeHe ÀÀ À À À
À À
ÀÀÀa Àe C. ae..e.e Niobium 0 - 1.7% Titanium 0 - 0.5% Zirconium 0 - 0.5% Cobalt 0 - 2.0% 5 Tungsten 0 - 1.0% Hafnium 0.01 - 4.5% balance iron and incidental impurities, 10 with the proviso that at least one of niobium, titanium and zirconium is present and that at least part of the hainium is present as finely divided oxide particles.
In a second aspect, the present invention provides a 15 method of manufacturing an oxide dispersion strengthened 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.
Preferred alloys according to the invention 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 2.5 max 30 40 20 - 30 1.0 max B 0.03 - 0.2 0.1 - 2.5 2.5 max 30 - 40 20 - 30 1.0 max C 0.3 - 0.5 0.1 - 2.5 2.5 max 40 - 50 30 - 40 1.0 max D 0.03 - 0.2 0.1 2.5 2.5 max 40 - 50 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
:.'.'&.';.'w'\'i'.-:..::i.-l:.-:.';:-.;;...:.. i:.:.:;:.:-'..,,..'::.'Y:.. ;.'.-.'::..'-.::'..;;'..i.;:..L,:_;;.;::,.;.,:.,;.,;:.i; '-;::.:...'._.;. ::..._.::.:.,:;.:i._, À À Àe.eC À @ .ÀÀ À ÀÀ À À
À ÀÀ À. -
ÀeÀ...ee. Àe Niobium Hafnium Titanium zirconium Cobalt Tungsten A 1.7 max 0.025 - 4.5 0.5 max 0.5 max 2.0 max 1.0 max s 1.7 max 0.025 - 4.5 0.5 max 0.5 max 2.0 max 1.0 max C 1.7 max 0.025 - 4.5 0.5 max 0.5 max 2.0 max 1.0 max D 1.7 max 0.025 - 4.5 0.5 max 0.5 max 2.0 max 1.0 max E 1.7 max 0.025 - 4.5 2.0 max 1.0 max F 1.7 max 0.025 - 4.5 0.5 max 0.5 max 2.0 max 1.0 max balance iron and incidental impurities.
The amount of hafnium in the alloy, by weight, is 5 preferably from 0.05 to 3.0%, more preferably from 0.1% to 1.0% and most preferably from 0.2 to 0.5%. Preferably 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 10 preferably from 5 microns to 0.25 microns or less.
A particularly preferred alloy composition according to the invention consists essentially of the following components, by weight: Carbon 0.45% Silicon 1.3% Manganese 0.9% Nickel 33.8% 20 Chromium 25.7% Molybdenum 0. 03% Niobium 0.85% Hafnium 0.25% Titanium 0.1% 25 Zirconium 0.01% Cobalt 0. 04% Tungsten 0.01% Iron balance.
i. in 5;j i ti hi " A 9 we'd I;:,;: i: I,..::.:3i;:.::Lv-.i; ^'.;:i.: \':. :.' '.'. in'.
eeÀÀ e ÀcÀ À À À À À ÀÀÀÀ À e Àe À À e À À À e À. Àe eve Àe ece À Àe Incidental impurities in the alloys of the invention can comprise, for example, aluminium, phosphorus, sulphur, vanadium, zinc, arsenic, nitrogen, tin, lead, copper and 5 cerium, up to a total amount of about 1. 0%.
In the method of the invention, it is important to provide conditions in the melt which permit oxidation of the hafnium particles without allowing detrimental 10 reactions which would result in the hafnium being taken up in the slag. The correct oxidising conditions can be achieved by appropriate adjustment or additions of the components, especially silicon, and by ensuring that unwanted contaminants such as aluminium are absent or 15 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 micro-additions of, for example, one or more of silicon, niobium, titanium and zirconium, 20 and the optimum free oxygen level necessary to react with the hafnium particles can readily be found by routine experimentation. After the reaction of the hafnium particles with free 25 oxygen, alloying amounts of titanium and/or zirconium may be added, up to the specified limits of 0.5% by weight.
The substantial removal of available free oxygen from the melt helps to ensure that any such titanium and zirconium additions do not form oxides, which could react 30 detrimentally with the hafnium particles and reduce the yields of titanium, zirconium and hafnium present in the alloy. It is important that the hafnium is added to the melt as 35 finely divided particles and that it is oxidised in situ.
3."' 'i:;;::.'.'i "I:'.:.i': '..;;:.';... ':::.":.:'.::: ?. '::.:.:-_::.:; qS.: ';:.; 3:.:.' i_.;.;;_. '.;:::.::'::;::_.:.::.::.:; i':::\;::: ÀÀÀÀ À
e. À. , À À À À
À À À
À Àe e Attempts to \ add large pieces of hafnium to nickel/chromium \micro-alloys have revealed that the hafnium does not perse, but settles to the bottom of the alloy melt, or Reacts with carbon resulting in a 5 decrease of the alloy properties. Surprisingly, we have also found that the addition of hafnia (hafoium 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 10 invention it has been found that it is necessary to carry out the oxidation of the hainium particles in the melt in order to obtain the desired improvement.
The charge make up can be a virgin charge (pure metals), 15 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 inhouse reverts treated by argon purging. In 20 each case the chemical composition of the melt should be carefully monitored to avoid contaminants and the formation of unwanted slag. Special care should be taken to deslag the bath, and the maximum amount of slag is preferably removed from the surface of the bath. It is 25 possible to improve slag removal by the use of a neutral deslag powder. If desired the melt can be maintained in an argon atmosphere, but this is not essential.
The melt temperature is preferably in the range of from 30 1580 C to 1700 C, preferably from 1610 C to 1670 C.
Hafnium particles are preferably added to the melt just before pouring the molten alloy into the mould. If a ladle is used, the hafoium is preferably added in the
:..!: G:.:..:'..':';..:!.:.':..:''.i...::'..'.':'.. {.'.':::2'::.::.'..::...::!.......;'::.:.'.'..'. A:::'::::...:..:..'..'......:...^:._. -.:....
:.::.'::..'_'.;,.'.:i:....':...::....'.':.:, À :::::: Àe a tee ee. e ce. ate ladle. To improve the hafnium dispersion, the molten alloy is preferably stirred before pouring...DTD: Any type of hafnium can be used, but electrolytic hafnium 5 is preferred. The 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 of 10 from 1 to 2 mm. When dispersed in the melt, the hafnium particles are further reduced in size.
The alloys of the invention have a primary carbide network similar to the corresponding alloys without the 15 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 20 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. In additions to these precipitates, the invention provides for the formation of a hafoia / hafnium oxide dispersion (the hafnium can be oxidised to form HfO2, but it can be expected that there will also be formed an 30 oxide HfOX with x as a variable), and hafnium/niobium/titanium carbo-nitrides and (rarely) oxides mixtures (the quantity of niobium and titanium is variable as well as the nitrogen and the oxygen). It is also possible that some hafnium carbo-nitrides may be 35 formed. More numerous titanium nitride (or carbide)
:..1 ';.:.... '; 'lo.';.. ".':'t'::i'.;;t'.'.'.':...::...1 _ i:::.:.' ' '::. a! i:. a_:'.:.:':.1.':.'::'.;.i'. i::'..i:\'. &:: À À À À e À À
À TIC BC..e dispersions may be observed in the alloy, some of which may also contain hafnia particles.
The alloys of the invention have improved high 5 temperature creep resistance, leading to an improved service life expectancy. Without wishing to be confined to any particular theory, it is believed that the creep resistance of the new alloys derives from the ability of the particle dispersion to delay the motion of the 10 dislocations in the alloy lattice. The micro-alloy, without the oxide dispersion, can delay the motion of dislocations by the presence of carbide (and/or nitride) precipitates, but the presence of the oxide dispersion provides a substantial unexpected extra improvement.
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 20 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. For example, in certain applications the internal bore of the tube is machined, removing 4-5 mm of 25 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 30 manifolds.
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. The alloy is able to develop an 35 oxide layer on its surface that protects it against
:.i '..i._i L.;;.;',!i.;;ti',i: i.i:..'i\ i it.. \'L I. _;.'.i' i. is.;:.. :i.'.. i:i & ÀÀ e Àeeece.e À c À À ac À Àe À Àe- a.- I. e.. e 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 spell during the tube service 5 life (because of differences of coefficients of expansion with the alloy, compressive stresses in the oxide, eta).
Spalling leaves the alloy unprotected against corrosion from the gaseous and particulate reactants of the ethylene cracking process. It has surprisingly been 10 found that the hafnium addition can tend to delay the spelling of the protective oxide layer.
Embodiments of alloys according to the invention are illustrated in the accompanying Drawings, by way of 15 example only, in which: Figure 1 is a photomicrograph of a first alloy according to the invention with its composition, Figure 2 is a photomicrograph of a second alloy according 20 to the invention with its composition; Figure 3 is a photomicrograph of a third alloy according to the invention with its composition; and Figure 4 is a photomicrograph of a fourth alloy acording to the invention with its composition.
The invention is further illustrated by the following Examples, in which all percentages are by weight: Example 1
The following melt composition is produced in a clean furnace: Nickel 25% 35 Chromium 35%
At; I'.,:;: it's I;.\..it i.i.;.i '..;. i.;.\ A,._..;; i:;\.) i: HA 'i. '; À e.e.ee ee À e C e e Àeeeseee..e e.e Carbon 0.4% Niobium 0.8 - 0.9% Silicon 1.6 - 1.8% Manganese 1.1 - 1.3% 5 Iron balance.
The temperature of the melt is raised to a tap temperature of 1640 C to 1650 C and the silicon content checked. The furnace is then de-slaged, removing as much 10 slag as possible. lOOkg of alloy are then tapped into a ladle and 0.35% hafnium particles of particle size maximum 5 mm, average 1 -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 20 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 25 properties of the commercial alloy derived from the regression analysis of numerous creep tests gave a typical figure of 16.7 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 275 hours.
30 The alloy according to the invention had a minimum failure time of rupture of 370 hours and a mean value failure of 430 hours.
Example 2
'..'\,.';;.j'#.;'\:,'j.i.'..i''.. -'i''-.';..'.S..'.''. C\i;','i.',i.\'.'.'.'.i.:'.';:;'..;..;i.'.i.''''.'.'..'".'.'...i.'.;-.-..-' \..'..'.'.i;.
À e À e c À À À À À C
À À À e À À see ce. ee. Àe À see The procedure of Example 1 is repeated using the same melt composition except that the titanium addition is omitted. 5 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.
10 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 15 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.
The results of Examples 1 and 2 show the dramatic improvement in creep properties that can be obtained using the alloys and method of the invention.
25 The reader's attention is directed to all papers and documents which are filed concurrently with or previous to this specification in connection with this application
and which are open to public inspection with this specification, and the contents of all such papers and
30 documents are incorporated herein by reference.
All of the features disclosed in this specification
(including any accompanying claims, abstract and drawings), and/or all of the- steps of any method or 35 process so disclosed, may be combined in any combination,
;I'',\.;..'i:',t'iiiY''.\',' 'I. '.4'; ''. hi'.'.'.\:'.:4'..'47. \'l' 'a::;.;:; hi".'.'.;:..'..i'.';::i,;,.i'.':,';..
ee e e e.eccecc e e e #ece e e e e e c c cce c e seeeeeeceec e e ce.
except combinations where at least some of such features and/or steps are mutually exclusive.
Each feature disclosed in this specification (including
5 any accompanying claims, abstract and drawings), may be replaced by alternative features serving the same, equivalent or similar purpose, unless expressly stated otherwise. Thus, unless expressly stated otherwise, each feature disclosed is one example only of a generic series 10 of equivalent or similar features.
The invention is not restricted to the details of any foregoing embodiments. The invention extends to any novel one, or any novel combination, of the features 15 disclosed in this specification (including any
accompanying claims, abstract and drawings), or to any novel one, or any novel combination, of the steps of any method or process so disclosed.

Claims (1)

  1. :'.C.; a: '.'.:.'.'^b.'N'.:.'i'':::.::::::":':i:.' I:::' \:;.': ',: i.',
    i.:1'.'. ':.::.'. \.:,::.'.::.:.::.::.: -.:.ii.:: ' ',:..;' 'l.' '. ::::::.::.!: ' ': ÀÀÀÀ À
    ÀeÀc.eÀe e aÀCc À À ÀÀÀC À À
    eÀ À À Àee À. À- ece e Àe CLAIMS
    1. An oxide dispersion strengthened nickel-chromium 5 iron alloy comprising, by weight: Carbon 0.01 to 0. 5% Silicon 0.01 to 2. 5% Manganese O to 2. 5% 10 Nickel 15 to 50% Chromium 20 to 40% Molybdenum O to 1. 0% Niobium O to 1. 7% Titanium O to 0.5% 15 zirconium. O to 0. 5% Cobalt O to 2. 0% Tungsten O to 1. 0% Hafnium 0.01 to 4. 5%, 20 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 hafoium is present as finally divided oxide particles.
    2. An alloy according to claim 1 having the following composition, by weight: Carbon 0.3 to 0.5% 30 Silicon 0.1 to 2.5% Manganese 2.5% max.
    Nickel 30 to 40% Chromium 20 to 30% Molybdenum 1. 0% max.
    35 Niobium 1.7% max.
    i it;,,,, j.,I,,,;;t,,, jut\.,Y,, i,, A;, jeer i to L.; I,, I],, cup,,,, i,,,j ej -in ion -:::r.:: ÀÀ À À
    e. À.
    ee ee Àeee À e Àe.eceeBe,,,.e Hafnium 0.01 to 4.5% Titanium 0.5% max.
    Zirconium 0.5% max.
    Cobalt 2.0% max.
    5 Tungsten 1.0% max., Balance iron and incidental impurities.
    3. An alloy according to claim 1 having the following composition, by weight: Carbon 0.03 to 0.2% Silicon 0.1 to 0.25% Manganese 2.5% max.
    Nickel 30 to 40% 15 Chromium 20 to 30% Molybdenum 1.0% max.
    Niobium 1.7% max.
    Hafnium 0.01 to 4.5% Titanium 0.5% max.
    20 Zirconium 0.5% max.
    Cobalt 2.05% max.
    Tungsten 1.0% max., balance iron and incidental impurities.
    4. An alloy according to claim 1 having the following composition, by weight: Carbon 0.3 to 0.5% 30 Silicon 0.1 to 2.5% Manganese 2.5% max.
    Nickel 40 to 50% Chromium 30 to 40% Molybdenum 1.0% max.
    35 Niobium 1.7% max.
    :.:;;:;.:.::.:.' _. a.:. i:;.':.;.':.;:::.'=.:':_i.:.'.;.'.:!':.'.;.-.:. ::;::!' ';:.i:'.::..'.. ti: ';;i' '..\.i.:i _..'.u..
    CC C ce.ehehe c À ÀÀe À -
    À ace can see ee. eve Hafnium 0.01 to 4.5% Titanium 0.5% max.
    Zirconium 0.5% max.
    Cobalt 2.0% max.
    5 Tungsten 1.0% max., balance iron and incidental impurities.
    5. An alloy according to claim 1 having the following 10 composition, by weight: Carbon 0.03 to 0.2% Silicon 0.1 to 2.5% Manganese 2.5% max.
    15 Nickel 40 to 50% Chromium 30 to 40% Molybdenum 1.0% max.
    Niobium 1.7% max.
    Hafnium 0.01 to 4.5% 20 Titanium 0.5% max.
    Zirconium 0.5% max.
    Cobalt 2.0% max.
    Tungsten 1.0% max., 25 balance iron and incidental impurities.
    6. An alloy according to claim 1 having the following composition, by weight: 30 Carbon 0.3 to 0.5% Silicon 0.1 to 2.5% Manganese 2.5% max.
    Nickel 19 to 22% Chromium 24 to 27% 35 Molybdenum 1.0% max.
    :4',:.'t.',.'bi't;." 'A;X';'.i';;.';i&i i'.; i..'\i.;;';ii;'-' 'it 'ii 'I t C 8
    se 84 88 À À 8 À À 8 8
    88 e À À eÀ; À 8 me 868 I À. 8 '..
    Niobium 1.7% max Hafoium 0.01 to 4.5% Cobalt 2.0% max.
    Tungsten 1.0% max., balance iron and incidental impurities.
    7. An alloy according to claim 1 having the following composition, by weight: Carbon 0.03 to 0.2% Silicon 0.1 to 2.5% Manganese 2.5% max Nickel 30 to 45% 15 Chromium 19 to 22% Molybdenum 1.0% max.
    Niobium 1.7% max.
    Hafnium 0.01 to 4.5% Titanium 0.5% max.
    20 Zirconium 0.5% max.
    Cobalt 2.0% max.
    Tungsten 1.0% max., balance iron and incidental impurities.
    8. An alloy according to any of the preceding claims, in which the amount of hafnium in the alloy, by weight, is from 0.01 to 3.0%.
    30 9. An alloy according to any of the preceding claims, in which the amount of hafnium in the alloy, by weight, is from 0.1% to 1.0%.
    10. An alloy according to any of the preceding claims, 35 in which the amount of hafnium in the alloy, by weight,
    \;.; 'i'.iec;.;;i"ldi ' i ':: It'd:.'::. 3::'.'; ':.',':.'.;.'.i.'.':.i.'. ':;.:.'.b k' 'i.&'. ':'.';.'i '' 'y' -i,: '.':.i\.:tu.:.:i;.,:.;. i. i; ::: eee e e e'Heeee8 e e e e I e e e e e e e e e e e e I e e I 8 e Use ese see ele ese.
    is from 0.2 to 0.5%.
    11. An alloy according to any of the preceding claims, in which the hafnium is present in the alloy in the form 5 of finally divided oxidised particles having an average particle size of from 50 microns to 0.25 microns, or less. 12. An alloy according to any of the preceding claims, 10 in which the hafnium is present in the alloy in the form of finally divided oxidised particles having an average particle size of from 5 microns to 0.25 microns, or less.
    13. An alloy having the following composition, by 15 weight: Carbon 0.45% Silicon 1.3% Manganese 0.9% 20 Nickel 33.8% Chromium 25.7% Molybdenum 0. 03% Niobium 0.85% Hafnium 0.25% 25 Titanium 0.1% Zirconium 0.01% Cobalt 0. 4% Tungsten 0.01%, 30 balance iron and incidental impurities.
    14. An alloy according to any of the preceding claims substantially as described in the Examples.
    35 15. A nickel-chromium iron alloy comprising up to about
    ,; ID,,; a_. bin','_:i'ii '.' ',?,,,ji,,t,':,::,,:';,.-,::,'t i.:;:,';: i, :,'.,,, ?.-.,; '.:':..;i MA.;. ?. ?;._; ÀeÀe À e Àee.eeee À e e e eeee e e e Àeee e e e eeee e e e seeaceeeesee e see 5% of hafnium-containing particles.
    16. A method of manufacturing an oxide dispersion strengthened nickelchromium-iron alloy which comprises 5 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.
    17. A method according to claim 16, in which the alloy 10 is an alloy as claimed in any of claims 1 to 15.
    18. A method according to claim 16 or 17, wherein the hafnium particles have a particle size of less than 5mm.
    15 19. A method according to any of claims 16 to 18, in which the amount of hafnium added to the melt is from 0.01 to 3.0% by weight.
    20. A method according to any of claims 16 to 19, 20 wherein the hafnium particles are added to the melt shortly before pouring the molten alloy into the mould.
    21. A method according to claim 20, in which the hafnium particles are added to the molten alloy in a ladle.
    22. A method according to any of claims 16 to 21, in which the hafnium is electrolytic hafnium.
    23. A method according to any of claims 16 to 22, in 30 which the alloy melt is substantially aluminium free.
    24. A method according to any of claims 16 to 23, wherein the level of oxygen in the melt is varied by additions of one or more of niobium, titanium and 35 zirconium.
    :i.::.:: At:::.:: ÀÀeÀ cee.ÀeÀe À e ÀÀÀÀ À e ÀÀÀÀ À
    ÀÀÀÀ À
    Àe ee. À. Àe À À..
    25. A method according to claim 24, in which the titanium is added in the form of TiFe after the hafnium addition. 26. A method according to any of claims 16 to 24, in which the maximum amount of slag is removed from the surface of the alloy.
    10 27. A method according to any of claims 16 to 26, in which the melt temperature is in the range of from 1580 C to 1700 C.
    28. A method according to any of claims 16 to 27, in 15 which the alloy is formed into a tube by rotational moulding. 29. A method according to any of claims 16 to 28 substantially as described in the Examples.
    30. A method of manufacturing a nickel-chromium-iron alloy, which comprises adding finely divided hafnium particles to the melt before pouring.
    25 31. A creep resistant alloy tube formed from a nickel-
    chromium-iron alloy comprising up to about 5% of hafnium-
    containing particles.
    32. A tube according to claim 31, which comprises an 30 oxide dispersion strengthened nickel-chromium-iron alloy comprising up to about 5% of hafnium 33. A nickel-chromium-iron alloy tube comprising up to about 5% of hafnium-containing particles substantially as 35 hereinbefore described.
    V'I'',;_'\itI. '.:.; i Ike YLg:;;t:;;: id;;; it; \;eq;\{:,n,; j,_l,j, ÀeeÀ Àee.ÀeÀe À Àeee e À Àeee e e Àeee e À ce.Àe.seeÀee À eee 34. A tube formed from an alloy according to any of claims 1 to 15 by rotational moulding.
    5 35. A nickel-chromium-iron alloy having a structure and composition substantially as described and illustrated in Figures 1 to 4 of the accompanying Drawings, wherein the tables represent percentages by weight of the alloy constituents.
GB0225648A 2002-11-04 2002-11-04 Hafnium particle dispersion hardened nickel-chromium-iron alloys Withdrawn GB2394959A (en)

Priority Applications (20)

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
US10/533,034 US20070144622A1 (en) 2002-11-04 2003-10-30 High temperature resistant alloys
AT03775499T ATE404706T1 (en) 2002-11-04 2003-10-30 HIGH TEMPERATURE RESISTANT ALLOYS
GB0325297A GB2394960B (en) 2002-11-04 2003-10-30 High temperature alloys
EP03775499A EP1558776B8 (en) 2002-11-04 2003-10-30 High temperature resistant alloys
EP08153580A EP1935996A1 (en) 2002-11-04 2003-10-30 High temperature resistant alloys
ES03775499T ES2312831T3 (en) 2002-11-04 2003-10-30 HIGH TEMPERATURE RESISTANT ALLOYS.
AU2003283525A AU2003283525A1 (en) 2002-11-04 2003-10-30 High temperature resistant alloys
PCT/GB2003/004665 WO2004042100A2 (en) 2002-11-04 2003-10-30 High temperature resistant alloys
JP2004549307A JP2006505694A (en) 2002-11-04 2003-10-30 High temperature alloy
DE60322935T DE60322935D1 (en) 2002-11-04 2003-10-30 HIGH TEMPERATURE RESISTANT ALLOYS
EP03810516A EP1560940A2 (en) 2002-11-04 2003-11-04 High temperature alloys
PCT/GB2003/004754 WO2004042101A2 (en) 2002-11-04 2003-11-04 High temperature alloys
CA002504937A CA2504937A1 (en) 2002-11-04 2003-11-04 Tube made from high temperature alloys
AU2003301837A AU2003301837A1 (en) 2002-11-04 2003-11-04 High temperature alloys
JP2004549337A JP2006517255A (en) 2002-11-04 2003-11-04 High temperature alloy
US10/533,850 US20060096673A1 (en) 2002-11-04 2004-11-04 High temperature alloys
US12/561,057 US20100175508A1 (en) 2002-11-04 2009-09-16 High temperature alloys

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
GB0225648A GB2394959A (en) 2002-11-04 2002-11-04 Hafnium particle dispersion hardened nickel-chromium-iron alloys

Publications (2)

Publication Number Publication Date
GB0225648D0 GB0225648D0 (en) 2002-12-11
GB2394959A true GB2394959A (en) 2004-05-12

Family

ID=9947143

Family Applications (2)

Application Number Title Priority Date Filing Date
GB0225648A Withdrawn GB2394959A (en) 2002-11-04 2002-11-04 Hafnium particle dispersion hardened nickel-chromium-iron alloys
GBGB0228576.5A Ceased GB0228576D0 (en) 2002-11-04 2002-12-09 High temperature alloys

Family Applications After (1)

Application Number Title Priority Date Filing Date
GBGB0228576.5A Ceased GB0228576D0 (en) 2002-11-04 2002-12-09 High temperature alloys

Country Status (10)

Country Link
US (2) US20060096673A1 (en)
EP (1) EP1560940A2 (en)
JP (1) JP2006517255A (en)
AT (1) ATE404706T1 (en)
AU (1) AU2003301837A1 (en)
CA (1) CA2504937A1 (en)
DE (1) DE60322935D1 (en)
ES (1) ES2312831T3 (en)
GB (2) GB2394959A (en)
WO (1) WO2004042101A2 (en)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8318083B2 (en) * 2005-12-07 2012-11-27 Ut-Battelle, Llc Cast heat-resistant austenitic steel with improved temperature creep properties and balanced alloying element additions and methodology for development of the same
CN109112327A (en) * 2018-11-08 2019-01-01 北京钢研高纳科技股份有限公司 A kind of anti-oxidant heat-resisting alloy and preparation method

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2394959A (en) * 2002-11-04 2004-05-12 Doncasters Ltd Hafnium particle dispersion hardened nickel-chromium-iron alloys
JP2006505694A (en) * 2002-11-04 2006-02-16 ドンカスターズ リミテッド High temperature alloy
US7824606B2 (en) * 2006-09-21 2010-11-02 Honeywell International Inc. Nickel-based alloys and articles made therefrom
FR2939808B1 (en) * 2008-12-16 2011-01-07 Air Liquide HIGH-TEMPERATURE STABLE-NICKEL-CHROME ALLOY ALLOYS
CN103087739A (en) * 2013-02-04 2013-05-08 安徽省建辉可再生能源科技有限公司 Biomass material thermal cracking furnace and material thereof, and method for preparing natural gas by using biomass material thermal cracking furnace
CN105463288B (en) * 2016-01-27 2017-10-17 大连理工大学 Casting alloy of high-strength high-plastic anti-chlorine ion corrosion and preparation method thereof
FR3082209B1 (en) * 2018-06-07 2020-08-07 Manoir Pitres AUSTENITIC ALLOY WITH HIGH ALUMINUM CONTENT AND ASSOCIATED DESIGN PROCESS
JP7131318B2 (en) * 2018-11-14 2022-09-06 日本製鉄株式会社 austenitic stainless steel
CN113005333B (en) * 2021-02-23 2022-04-01 江苏兄弟合金有限公司 Ultra-high temperature nickel-based alloy and preparation method thereof

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0065812A2 (en) * 1981-04-08 1982-12-01 Johnson Matthey Public Limited Company Nickel alloys containing large amounts of chromium
EP0246092A2 (en) * 1986-05-15 1987-11-19 Exxon Research And Engineering Company Alloys resistant to stress corrosion cracking
JPS63259051A (en) * 1987-04-14 1988-10-26 Nippon Steel Corp High toughness steel for electric resistance welded steel tube having excellent sour resistance
EP0384608A1 (en) * 1989-02-08 1990-08-29 Inco Alloys International, Inc. Mechanically alloyed nickel-cobalt-chromium-iron composition of matter
SU1763511A1 (en) * 1990-11-05 1992-09-23 Орский Механический Завод Steel
US5328499A (en) * 1993-04-28 1994-07-12 Inco Alloys International, Inc. Mechanically alloyed nickel-base composition having improved hot formability characteristics

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5040099B1 (en) * 1971-03-09 1975-12-22
BE794142A (en) * 1972-01-17 1973-07-17 Int Nickel Ltd HIGH TEMPERATURE ALLOYS
US3993454A (en) * 1975-06-23 1976-11-23 United Technologies Corporation Alumina forming coatings containing hafnium for high temperature applications
JPS5284135A (en) * 1976-11-08 1977-07-13 Mitsubishi Heavy Ind Ltd Carburizinggresisting alloys
US4615864A (en) * 1980-05-01 1986-10-07 Howmet Turbine Components Corporation Superalloy coating composition with oxidation and/or sulfidation resistance
GB2083499A (en) * 1980-09-05 1982-03-24 Firth Brown Ltd Austenitic steel
US4585481A (en) * 1981-08-05 1986-04-29 United Technologies Corporation Overlays coating for superalloys
US4743514A (en) * 1983-06-29 1988-05-10 Allied-Signal Inc. Oxidation resistant protective coating system for gas turbine components, and process for preparation of coated components
DE3606804A1 (en) * 1986-03-01 1987-09-10 Thyssen Huette Ag METALLIC SEMI-FINISHED PRODUCT AND METHOD FOR THE PRODUCTION AND USE THEREOF
CH674019A5 (en) * 1988-01-18 1990-04-30 Asea Brown Boveri
AT391435B (en) * 1988-04-14 1990-10-10 Plansee Metallwerk METHOD FOR PRODUCING AN ODSS ALLOY
JPH072981B2 (en) * 1989-04-05 1995-01-18 株式会社クボタ Heat resistant alloy
JPH051355A (en) * 1991-06-21 1993-01-08 Kubota Corp Heat resistant cast steel improved in creep fracture strength
US5712050A (en) * 1991-09-09 1998-01-27 General Electric Company Superalloy component with dispersion-containing protective coating
US5851318A (en) * 1995-06-09 1998-12-22 Krupp Vdm Gmbh High temperature forgeable alloy
DE19629977C2 (en) * 1996-07-25 2002-09-19 Schmidt & Clemens Gmbh & Co Ed Austenitic nickel-chrome steel alloy workpiece
KR100372482B1 (en) * 1999-06-30 2003-02-17 스미토모 긴조쿠 고교 가부시키가이샤 Heat resistant Ni base alloy
GB2394959A (en) * 2002-11-04 2004-05-12 Doncasters Ltd Hafnium particle dispersion hardened nickel-chromium-iron alloys

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0065812A2 (en) * 1981-04-08 1982-12-01 Johnson Matthey Public Limited Company Nickel alloys containing large amounts of chromium
EP0246092A2 (en) * 1986-05-15 1987-11-19 Exxon Research And Engineering Company Alloys resistant to stress corrosion cracking
JPS63259051A (en) * 1987-04-14 1988-10-26 Nippon Steel Corp High toughness steel for electric resistance welded steel tube having excellent sour resistance
EP0384608A1 (en) * 1989-02-08 1990-08-29 Inco Alloys International, Inc. Mechanically alloyed nickel-cobalt-chromium-iron composition of matter
SU1763511A1 (en) * 1990-11-05 1992-09-23 Орский Механический Завод Steel
US5328499A (en) * 1993-04-28 1994-07-12 Inco Alloys International, Inc. Mechanically alloyed nickel-base composition having improved hot formability characteristics

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8318083B2 (en) * 2005-12-07 2012-11-27 Ut-Battelle, Llc Cast heat-resistant austenitic steel with improved temperature creep properties and balanced alloying element additions and methodology for development of the same
CN109112327A (en) * 2018-11-08 2019-01-01 北京钢研高纳科技股份有限公司 A kind of anti-oxidant heat-resisting alloy and preparation method
CN109112327B (en) * 2018-11-08 2019-09-03 青岛新力通工业有限责任公司 A kind of anti-oxidant heat-resisting alloy and preparation method

Also Published As

Publication number Publication date
GB0225648D0 (en) 2002-12-11
ES2312831T3 (en) 2009-03-01
ATE404706T1 (en) 2008-08-15
WO2004042101A2 (en) 2004-05-21
WO2004042101B1 (en) 2004-09-30
EP1560940A2 (en) 2005-08-10
JP2006517255A (en) 2006-07-20
US20100175508A1 (en) 2010-07-15
CA2504937A1 (en) 2004-05-21
WO2004042101A3 (en) 2004-08-12
GB0228576D0 (en) 2003-01-15
AU2003301837A1 (en) 2004-06-07
US20060096673A1 (en) 2006-05-11
DE60322935D1 (en) 2008-09-25

Similar Documents

Publication Publication Date Title
EP1558776B1 (en) High temperature resistant alloys
US20100175508A1 (en) High temperature alloys
Huang et al. Effect of Ti content on microstructure and properties of Ti x ZrVNb refractory high-entropy alloys
CA3115366C (en) Anti-oxidation heat-resistant alloy and preparation method
AU2005205736B2 (en) Ni-Cr-Co alloy for advanced gas turbine engines
RU2599324C2 (en) Chrome nickel aluminium alloy with good machinability, creep limit properties and corrosion resistance parameters
KR101403553B1 (en) HIGH TEMPERATURE LOW THERMAL EXPANSION Ni-Mo-Cr ALLOY
US20210355564A1 (en) Nickel-based superalloys
US20070227630A1 (en) Nickel-based alloy
US5873950A (en) Strengthenable ethylene pyrolysis alloy
CN110952028B (en) Cr-Ni series austenite heat-resistant steel with enhanced phase precipitated in interior and preparation method thereof
KR20220118435A (en) Ni-based alloy, heat/corrosion-resistant parts, heat treatment furnace parts
CN109906129B (en) Alloy for build-up welding, powder for welding, and reaction tube
WO2009108892A1 (en) Method of making a high strength, high toughness, fatigue resistant, precipitation hardenable stainless steel
US4861547A (en) Iron-chromium-nickel heat resistant alloys
US11612967B2 (en) Alloy for overlay welding and reaction tube
US4718940A (en) Method of manufacturing alloy for use in fabricating metal parts
EA017210B1 (en) Refractory alloy, fibre-forming plate and method for producing mineral wool
JP2002173721A (en) Ni BASED ALLOY FOR MACHINE STRUCTURAL USE
JPS6173853A (en) Heat resisting alloy
JP3901801B2 (en) Heat-resistant cast steel and heat-resistant cast steel parts
CN112941393A (en) Quinary master alloy material and preparation method and application thereof
EP0477363A1 (en) Heat resistant alloys
JP2007197774A (en) Heat-resistant cast steel
Loria Development of ductile Nb-Ti-Al alloys: perspective and selected successes

Legal Events

Date Code Title Description
WAP Application withdrawn, taken to be withdrawn or refused ** after publication under section 16(1)