WO2017198831A1 - An object comprising a pre-oxidized nickel-based alloy - Google Patents
An object comprising a pre-oxidized nickel-based alloy Download PDFInfo
- Publication number
- WO2017198831A1 WO2017198831A1 PCT/EP2017/062136 EP2017062136W WO2017198831A1 WO 2017198831 A1 WO2017198831 A1 WO 2017198831A1 EP 2017062136 W EP2017062136 W EP 2017062136W WO 2017198831 A1 WO2017198831 A1 WO 2017198831A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- alloy
- based alloy
- max
- oxidized nickel
- nickel
- Prior art date
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 113
- 239000000956 alloy Substances 0.000 title claims abstract description 113
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 85
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 41
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 30
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 19
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 15
- 239000001301 oxygen Substances 0.000 claims abstract description 15
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 13
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 13
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 13
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 16
- 229910052804 chromium Inorganic materials 0.000 claims description 11
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 abstract description 7
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 28
- 239000011651 chromium Substances 0.000 description 18
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 230000015572 biosynthetic process Effects 0.000 description 12
- 239000004411 aluminium Substances 0.000 description 11
- 239000010936 titanium Substances 0.000 description 11
- 229910052761 rare earth metal Inorganic materials 0.000 description 10
- 150000002910 rare earth metals Chemical class 0.000 description 10
- 150000004767 nitrides Chemical class 0.000 description 9
- 230000003647 oxidation Effects 0.000 description 9
- 238000007254 oxidation reaction Methods 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 8
- 230000000694 effects Effects 0.000 description 8
- 238000007792 addition Methods 0.000 description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 230000001681 protective effect Effects 0.000 description 7
- -1 aluminium nitrides Chemical class 0.000 description 6
- 239000011572 manganese Substances 0.000 description 6
- 239000010955 niobium Substances 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 238000005275 alloying Methods 0.000 description 5
- 239000006185 dispersion Substances 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- 229910052727 yttrium Inorganic materials 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 238000000889 atomisation Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 238000003384 imaging method Methods 0.000 description 2
- 229910052747 lanthanoid Inorganic materials 0.000 description 2
- 150000002602 lanthanoids Chemical class 0.000 description 2
- 229910052746 lanthanum Inorganic materials 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 238000005121 nitriding Methods 0.000 description 2
- 230000000737 periodic effect Effects 0.000 description 2
- 230000005855 radiation Effects 0.000 description 2
- 229910052706 scandium Inorganic materials 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000943 NiAl Inorganic materials 0.000 description 1
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- BIJOYKCOMBZXAE-UHFFFAOYSA-N chromium iron nickel Chemical compound [Cr].[Fe].[Ni] BIJOYKCOMBZXAE-UHFFFAOYSA-N 0.000 description 1
- 229910000423 chromium oxide Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 238000000386 microscopy Methods 0.000 description 1
- 238000009862 microstructural analysis Methods 0.000 description 1
- 229910000907 nickel aluminide Inorganic materials 0.000 description 1
- 229910021334 nickel silicide Inorganic materials 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- 230000001052 transient effect Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- 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
- 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
Definitions
- the present disclosure relates to an object comprising a pre-oxidized nickel-based alloy and to the use thereof in environments where the temperature is high and the atmosphere surrounding the object comprises a high concentration of nitrogen and a low oxygen partial pressure.
- These environments exist in e.g. sintering furnaces and muffle furnaces.
- Nickel-based alloys comprise aluminium are used in a variety of high temperature applications, such as in heat treatment furnaces, since they will form a stable and protective aluminium oxide on the surface of objects made thereof.
- the formed aluminium oxide has a very good adhesion and does not tend to spall or fall off the surface. Furthermore, the aluminium oxide will have a low growth rate even at high temperatures.
- nickel-based alloys comprising aluminium will form aluminium nitrides on the surface instead of the protective aluminium oxide.
- the formation of aluminium nitrides will penetrate into the metal alloy rapidly and will also have a negative effect on the ability of the alloy to form a protective surface oxide.
- the mechanical properties, such as ductility and creep strength will due to this be reduced.
- the present disclosure therefore relates to an object comprising a pre-oxidized nickel- based alloy comprising by weight (wt-%)
- one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b 0.25-2.2;
- REM rare earth metals
- the present disclosure also relates to the use of the object as defined hereinabove or hereinafter in environments having a high nitrogen concentration and a low oxygen partial pressure and high temperature. Examples of where such environments exist are in sintering furnaces and muffle furnaces. Examples of objects, but not limited to, are mesh-belts, rollers (such as furnace rollers), tubes (such as radiation tubes and thermocouple protection tubes), fixtures and heating elements.
- the alloy and the objects made thereof may be manufactured from a powder.
- Figure 1 a and b discloses mass gain curves of the different nickel-based alloys at different temperatures.
- Figure 2a to c discloses the surface of objects formed by the nickel-based alloy as defined hereinabove or hereinafter and another alloy, which objects have been exposed to the conditions of high nitrogen concentration and a low oxygen partial pressure and high temperature.
- one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b 0.25-2.2 ;
- REM rare earth metals
- nickel-based alloy is described in EP 2617858 Al and it is known to be used in applications where there is a need for high oxidation resistance and good creep resistance.
- this pre- oxidized nickel-based alloy is very resistant against nitridation in environments having a high concentration of nitrogen and high temperature as it is alloyed with aluminium.
- aluminium nitrides would be formed on the surface instead of the protective aluminium oxide and also just below the surface but for this pre-oxidised alloy as defined hereinabove or hereinafter, a protective aluminium oxide is formed on the surface.
- the alloy is pre-oxidated before being made into an object, thus the object comprises a pre-oxidated nickel based alloy.
- the object may also be peroxided after being made into an object.
- the pre-oxidation is performed by exposing the material to a high temperature (above 900 °C) and to atmosphere comprising oxygen (e.g. air).
- Examples of objects are manufacturing parts which are exposed to environment having a high concentration of nitrogen and a low concentration of oxygen at high temperature (more than about 900 °C).
- Other examples are mesh-belts, furnace rollers, radiation tubes, fixtures, heating elements, and thermocouple protection tubes
- high temperature is intended to mean temperatures above or equal to 900 °C, However, the highest possible temperature is 1300 °C, such as about 1250 °C.
- the phrase "high nitrogen content” is intended to mean that the nitrogen concentration of more than or equal to 25 vol% N 2 , such as more than or equal to 50 vol% N 2 , such as more than or equal to 75 vol% N 2 , such as more than or equal to 95 vol% N 2 , such as more than or equal to 98 vol% N 2 .
- the phrase “low oxygen pressure” is intended to mean an oxygen content of less than or equal to lOOO ppm.
- the elementary composition of the nickel-based alloy is generally as defined hereinabove or hereinafter and the function of each alloying element is further described below.
- Carbon in free form will take interstitial locations in the crystal structure and thereby lock the mobility of dislocations at temperatures up to approximately 400-500°C. Carbon also forms carbides with other elements in the alloy such as Ta, Ti, Hf, Zr and Nb. In a micro structure with finely dispersed carbides, these carbides provide obstacles for the dislocation movement and have effect even at higher temperatures. Carbon is an essential element to improve the alloy's creep strength since the dislocation mobility is the mechanism that generates creep elongation. Too high contents of C will however lead to the alloy becoming difficult to cold work due to deteriorated ductility at lower temperatures, such as below 300°C. The alloy therefore comprises 0.05-0.2 % C.
- Silicon can be present in the alloy in contents up to 1.5 %. Silicon in too high contents can in nickel based alloys lead to increased risk for precipitations of nickel silicides, which have an embritteling effect on this type of alloy. Results from creep testing of similar alloys have shown that the creep life time, i.e. the time to creep fracture, is reduced with Si contents close to 1.5 %. The reason for this is however not known.
- the Si content should preferably be maximally 1 %.
- the alloy as defined hereinabove or hereinafter only comprises impurity content of Si, i.e. up to 0.3 %.
- Manganese is present in the alloy as an impurity. It is likely that up to 0.5 % can be allowed without negatively influencing the properties of the alloy whereby the alloy comprises maximally 0.5 % Mn. According to a one embodiment, the alloy as defined hereinabove or hereinafter only comprises impurity content of Mn, i.e. up to 0.2 %.
- Chromium is an element which for a long period of time has been the leading element when it comes to creating a dense and protective oxide scale. Less than 15 % Cr in an austenitic structure tends to render an oxide which is not entirely covering the surface and which is not dense and consequently render an insufficient oxidation resistance to the alloy. There is also a risk that the material closest to the oxide is depleted of Cr such that possible damages to the oxide cannot heal since there is not sufficient Cr to form new oxide.
- a nickel based alloy comprising 4 % Al should however not comprise more than about 20 % Cr as higher contents increase the risk of formation of ⁇ ' and ⁇ phases.
- the alloy as defined hereinabove or hereinafter comprises max 20 % Cr.
- the alloy as defined hereinabove or hereinafter comprises 15-20 % Cr, such as 17-20 % Cr, such as 17-19 % Cr. Aluminium
- Aluminium is an element that generates a much denser and more protective oxide scale compared to Cr. Aluminium can however not replace Cr since the formation of the aluminium oxide is slower than the chromium oxide at lower temperatures.
- the alloy comprises at least 4 % Al, such as more than 4 % Al, which will ensure a sufficient oxidation resistance at high temperatures and that the oxide covers the surface entirely.
- the relatively high content of Al provides excellent oxidation resistance even at temperatures of about 1100 °C.
- the alloy should therefore comprise 4-6 % Al, such as >4-5.5 %, such as >4 - 5.2 % A1.
- the alloy comprises at least 15 % Fe. High contents of iron may however lead to formation of unwanted phases. Therefore, the alloy shall not comprise more than 25 % Fe. Moreover, at Fe contents over approximately 21-22 %, the risk of formation of a ⁇ -phase ( iAl), which in some cases can be embritteling, increases.
- the alloy should therefore comprise 16-21.5 % Fe. According to a preferred embodiment, the alloy comprises 17-21 % Fe.
- the alloy according to the invention is a nickel based alloy.
- Nickel is an element which stabilises an austenitic structure in alloys and thereby counteracts formation of some brittle intermetallic phases, such as ⁇ -phase.
- the austenitic structure of the alloy is beneficial for example when it comes to welding.
- the austenitic structure also contributes to the good creep strength of the alloy at high temperatures. This could be a result of that the diffusion rate is lower in an austenitic structure than for example in a ferritic.
- the alloy comprises 52-62 % Ni, such as 52-60% Ni.
- Ni is substituted with Co in order to increase the mechanical strength of the alloy which may also be done in the alloy according to the invention.
- a part of the Ni of the alloy can be replaced with an equal amount of Co.
- This Co addition must however be balanced against the oxidation properties since the presence of NiAl will reduce the activity of Al and thereby deteriorate the ability to form aluminium oxide.
- nickel is partly substituted with Co. The Co content shall, however, not exceed 5%. Nitrogen
- free N takes interstitial locations in the crystal structure and thereby locks the dislocation mobility at temperatures up to approximately 400-500°C.
- Nitrogen also forms nitrides and/or carbon nitrides with other elements in the alloy such as Ta, Ti, Hf, Zr and Nb. In a microstructure where these particles are finely dispersed they confer obstacles for the dislocation mobility, especially at higher temperatures.
- the alloy comprises 0.03-0.15 % N, such as 0.05-0.15 % N, such as 0.05-0.10 % N.
- Oxygen may be present in the present alloy either in the form of an impurity, or as an active addition up to 0.5 %. Oxygen may contribute to increasing the creep strength of the alloy by forming small oxide dispersions together with Zr, Hf, Ta and Ti, which, when they are finely distributed in the alloy, improves its creep strength. These oxide dispersions have higher dissolution temperature than corresponding carbides and nitrides, whereby oxygen is a preferred addition for use at high temperatures. Oxygen may also form dispersions with Al, the elements in group 3 of the periodic table, Sc, Y and La as well as the fourteen lanthanides, and in the same manner as with the above identified elements thereby contribute to higher creep strength of the alloy. According to a preferred embodiment, the alloy comprises 200-2000 ppm O, such as 400-1000 ppm O.
- the elements in the group consisting of Ta, Hf and Zr forms very small and stable particles with carbon and nitrogen. It is these particles which, if they are finely dispersed in the structure, help to lock dislocation movement and thereby increase the creep strength, i.e. provides the dispersion strengthening. It is also possible to accomplish this effect with addition of Ti. Additions of Ti can, however, sometimes lead to problems, especially during powder metallurgical production of the alloy, since it forms carbides and nitrides already in the melt before atomisation, which in turn may clog the orifice during the atomisation.
- Niobium also forms stable dispersions with C and or N and can therefore suitably be added to the alloy according to the invention.
- the alloy comprises one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b in an amount of 0.25-2.2 %, such as 0.3-1.5 %, such as 0.6-1.5 %.
- the alloy may also comprise such an amount of the elements Ta, Zr, Hf, Ti and Nb that essentially all C and N is bound to these elements. This ensures that for example the risk of formation of chromium carbides during high temperature use of the alloy is significantly reduced.
- the alloy as defined hereinabove or hereinafter comprises 0.1 -0.5% Hf.
- the alloy comprises 0.05-0.35 % Zr.
- the alloy comprises 0.05-0.5 % Ta.
- the alloy comprises 0.05-0.4 % Ti. According to yet another embodiment, the alloy comprises 0.1-0.8 % Nb.
- Rare earth metals (REM) Rare earth metals
- Rare earth metals relates in this context to the elements of group three of the periodic table, Sc, Y, and La as well as the fourteen lanthanides.
- REM affects the oxidation properties by doping of the formed oxide. Excess alloying of these elements often gives an oxide which tends to spall of the surface and a too low addition of these elements tends to give an oxide with weaker adhesion to the metal surface.
- the alloy may comprise one or more elements from the group consisting of REM in a content of up to 0.5 % in total, such as 0.05-0.25 %. According to a one embodiment, yttrium is added to the alloy as defined hereinabove or hereinafter in an amount of 0.05-0.25 %.
- the nickel based alloy as defined hereinabove or hereinafter may also comprise normally occurring impurities as a result of the raw material used or the selected manufacturing process.
- impurities are Ca, S and P.
- other alloying elements, which will not affect the properties of the alloy may optionally be added in amounts up to 1 %.
- max the skilled person knows that the lower limit of the range is 0 wt% unless another number is specifically stated.
- the prenickel-based alloy as defined hereinabove or hereinafter may be manufactured according to conventional methods, i.e. casting followed by hot working and/or cold working and optional additional heat treatment.
- the nickel-based alloy as defined hereinabove or hereinafter may also be used produced as a powder product by for example hot isostatic pressure process (HIP).
- HIP hot isostatic pressure process
- Alloy 1 is an alloy according to the present disclosure
- Alloy 2 is an austenitic nickel-chromium-iron alloy of the standard U S N06600.
- the alloys were exposed in an atmosphere containing 5% 3 ⁇ 4 and 95% N 2 , with a dew point below -40°C, reminiscent of the environment in a sintering furnace. Two exposure temperatures were used; 900°C and 1150°C. The effect of pre-oxidation was investigated.
- Sample coupons with the dimensions 10 x 15 x 2 mm with one corner cut off were machined and ground with successively finer grinding paper, ending at 600 grit. After grinding, the dimensions of the samples were measured and identification numbers were punched into the edges of the samples. Prior to exposure, the samples were cleaned and degreased in ethanol and acetone and the mass of each sample was recorded using a Sartorius microbalance with microgram resolution. The samples were mounted in cylindrical crucibles and exposed in horizontal tube furnaces. Half of the samples were pre-oxidized at 1150°C for 20 minutes prior to the exposure to the nitriding atmosphere. The parameters for the pre-oxidation were selected to resemble the final hot step of the production of tubes. Table 1 - The compositions of the tested alloys (wt%)
- Exposures were performed at 900°C and 1150°C.
- the atmosphere consisted of 95% nitrogen and 5% hydrogen.
- the dew point was kept below -40°C and continuously monitored using hygrometers.
- the exposure times were 200, 500 and 1500 hours at both temperatures.
- the exposures were isothermal, with each sample being exposed once only. Analysis
- the micro structural analysis was done using two different microscopes. One was a Zeiss EVO 50 variable pressure scanning electron microscope (VP-SEM), and the other was a Zeiss Sigma VP-SEM. An acceleration voltage of 20 kV was used for imaging and chemical analysis by energy dispersive spectroscopy (EDS). Back scattered (BSE) were used for imaging.
- Figure 2 discloses examples of the microscope studie.
- the alloy according to the disclosure shows a nitridation resistance in 5% H 2 - 95% N 2 .
- the alloy according to the disclosure shows a nitridation resistance in 5% H 2 - 95% N 2 .
- At 1150°C there is no sign of nitridation on and at 900°C, only modest nitridation is seen on samples of the present nickel based alloy that have not been pre-oxidized. Without being bound to any theory, it is believed that it is possible this may be due to formation of transient alumina.
- nitrides are formed on the surface of alloy 2, which makes it unsuitable for the conditions defined herein.
- an alloy of the present disclosure can be used in nitriding environments, especially at higher temperatures as the alloy will almost form no nitrides which keep the aluminum oxide layer undamaged and thereby preventing corrosion.
Abstract
The present application relates to an object comprising a pre-oxidized nickel based alloy comprising in percent by weight (wt-%) C 0.05-0.2; Si max 1.5; Mn max 0.5; Cr 15-20; Al 4-6; Fe 15-25; Co max 5; N 0.03-0.15; O max 0.5; one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and Nb 0.25-2.2; one or more elements selected from the group consisting of REM max 0.5; balance Ni and normally occurring impurities an also to the use of said object wherein the use is in an environment comprised of high concentration of nitrogen, low partial pressure of oxygen and high temperature.
Description
An object comprising a pre-oxidized nickel-based alloy Technical field
The present disclosure relates to an object comprising a pre-oxidized nickel-based alloy and to the use thereof in environments where the temperature is high and the atmosphere surrounding the object comprises a high concentration of nitrogen and a low oxygen partial pressure. These environments exist in e.g. sintering furnaces and muffle furnaces. Background
Nickel-based alloys comprise aluminium are used in a variety of high temperature applications, such as in heat treatment furnaces, since they will form a stable and protective aluminium oxide on the surface of objects made thereof. The formed aluminium oxide has a very good adhesion and does not tend to spall or fall off the surface. Furthermore, the aluminium oxide will have a low growth rate even at high temperatures.
However, it has been found that in applications wherein the gas atmosphere comprises high nitrogen content and low oxygen content nickel-based alloys comprising aluminium will form aluminium nitrides on the surface instead of the protective aluminium oxide. The formation of aluminium nitrides will penetrate into the metal alloy rapidly and will also have a negative effect on the ability of the alloy to form a protective surface oxide. Furthermore, the mechanical properties, such as ductility and creep strength will due to this be reduced.
The aspect of the present disclosure is to overcome the above-mentioned problems. Summary of the disclosure
The present disclosure therefore relates to an object comprising a pre-oxidized nickel- based alloy comprising by weight (wt-%)
C 0.05-0.2;
Si max 1.5;
Mn max 0.5;
Cr 15-20;
Al 4-6;
Fe 15-25;
Co max 5;
N 0.03-0.15;
0 max 0.5;
one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b 0.25-2.2;
one or more elements selected from the group consisting of the rare earth metals (REM) max 0.5;
balance Ni and normally occurring impurities. The present disclosure also relates to the use of the object as defined hereinabove or hereinafter in environments having a high nitrogen concentration and a low oxygen partial pressure and high temperature. Examples of where such environments exist are in sintering furnaces and muffle furnaces. Examples of objects, but not limited to, are mesh-belts, rollers (such as furnace rollers), tubes (such as radiation tubes and thermocouple protection tubes), fixtures and heating elements.
The alloy and the objects made thereof may be manufactured from a powder.
Brief description of the drawings
Figure 1 a and b discloses mass gain curves of the different nickel-based alloys at different temperatures.
Figure 2a to c discloses the surface of objects formed by the nickel-based alloy as defined hereinabove or hereinafter and another alloy, which objects
have been exposed to the conditions of high nitrogen concentration and a low oxygen partial pressure and high temperature.
Detailed description
It has surprisingly been shown that an object comprising a pre-oxidized nickel-based alloy with the following composition in weight% (wt%):
c 0.05-0.2;
Si max 1.5;
Mn max 0.5;
Cr 15-20;
Al 4-6;
Fe 15-25;
Co max 5;
N 0.03-0.15;
0 max 0.5;
one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b 0.25-2.2 ;
one or more elements selected from the group consisting of the rare earth metals (REM) max 0.5;
balance Ni and normally occurring impurities
will have very good nitridation resistance in environments having a high concentration of nitrogen and high temperature. The nickel-based alloy is described in EP 2617858 Al and it is known to be used in applications where there is a need for high oxidation resistance and good creep resistance. However, as stated above, it is very surprising that this pre- oxidized nickel-based alloy is very resistant against nitridation in environments having a high concentration of nitrogen and high temperature as it is alloyed with aluminium. Thus, normally aluminium nitrides would be formed on the surface instead of the protective aluminium oxide and also just below the surface but for this pre-oxidised alloy as defined hereinabove or hereinafter, a protective aluminium oxide is formed on the surface.
The alloy is pre-oxidated before being made into an object, thus the object comprises a pre-oxidated nickel based alloy. The object may also be peroxided after being made into an object. The pre-oxidation is performed by exposing the material to a high temperature (above 900 °C) and to atmosphere comprising oxygen (e.g. air).
Examples of objects are manufacturing parts which are exposed to environment having a high concentration of nitrogen and a low concentration of oxygen at high temperature (more than about 900 °C). Other examples are mesh-belts, furnace rollers, radiation tubes, fixtures, heating elements, and thermocouple protection tubes
The term "high temperature" is intended to mean temperatures above or equal to 900 °C, However, the highest possible temperature is 1300 °C, such as about 1250 °C.
According to the present disclosure, the phrase "high nitrogen content" is intended to mean that the nitrogen concentration of more than or equal to 25 vol% N2, such as more than or equal to 50 vol% N2, such as more than or equal to 75 vol% N2, such as more than or equal to 95 vol% N2, such as more than or equal to 98 vol% N2. Additionally, the phrase "low oxygen pressure" is intended to mean an oxygen content of less than or equal to lOOO ppm.
The elementary composition of the nickel-based alloy is generally as defined hereinabove or hereinafter and the function of each alloying element is further described below.
However, the listing of functions and effects of the respective alloying elements is not to be seen as complete, but there may be further functions and effects of said alloying elements. The terms weight%, wt% and % are used interchangeably.
Carbon
Carbon in free form will take interstitial locations in the crystal structure and thereby lock the mobility of dislocations at temperatures up to approximately 400-500°C. Carbon also forms carbides with other elements in the alloy such as Ta, Ti, Hf, Zr and Nb. In a micro structure with finely dispersed carbides, these carbides provide obstacles for the
dislocation movement and have effect even at higher temperatures. Carbon is an essential element to improve the alloy's creep strength since the dislocation mobility is the mechanism that generates creep elongation. Too high contents of C will however lead to the alloy becoming difficult to cold work due to deteriorated ductility at lower temperatures, such as below 300°C. The alloy therefore comprises 0.05-0.2 % C.
Silicon
Silicon can be present in the alloy in contents up to 1.5 %. Silicon in too high contents can in nickel based alloys lead to increased risk for precipitations of nickel silicides, which have an embritteling effect on this type of alloy. Results from creep testing of similar alloys have shown that the creep life time, i.e. the time to creep fracture, is reduced with Si contents close to 1.5 %. The reason for this is however not known.
Because of this, the Si content should preferably be maximally 1 %. According to one embodiment, the alloy as defined hereinabove or hereinafter only comprises impurity content of Si, i.e. up to 0.3 %.
Manganese
Manganese is present in the alloy as an impurity. It is likely that up to 0.5 % can be allowed without negatively influencing the properties of the alloy whereby the alloy comprises maximally 0.5 % Mn. According to a one embodiment, the alloy as defined hereinabove or hereinafter only comprises impurity content of Mn, i.e. up to 0.2 %.
Chromium
Chromium is an element which for a long period of time has been the leading element when it comes to creating a dense and protective oxide scale. Less than 15 % Cr in an austenitic structure tends to render an oxide which is not entirely covering the surface and which is not dense and consequently render an insufficient oxidation resistance to the alloy. There is also a risk that the material closest to the oxide is depleted of Cr such that possible damages to the oxide cannot heal since there is not sufficient Cr to form new oxide.
A nickel based alloy comprising 4 % Al should however not comprise more than about 20 % Cr as higher contents increase the risk of formation of γ' and β phases. Therefore, in order to minimise the presence of the γ' and β phases, the alloy as defined hereinabove or hereinafter comprises max 20 % Cr. There may also be a risk of formation of other unwanted phases, such as σ-phase and chromium rich ferrite, at too high Cr contents. Moreover, Cr may also at high contents stabilise nickel aluminides. Thus, the alloy as defined hereinabove or hereinafter comprises 15-20 % Cr, such as 17-20 % Cr, such as 17-19 % Cr. Aluminium
Aluminium is an element that generates a much denser and more protective oxide scale compared to Cr. Aluminium can however not replace Cr since the formation of the aluminium oxide is slower than the chromium oxide at lower temperatures. The alloy comprises at least 4 % Al, such as more than 4 % Al, which will ensure a sufficient oxidation resistance at high temperatures and that the oxide covers the surface entirely. The relatively high content of Al provides excellent oxidation resistance even at temperatures of about 1100 °C. At Al contents above 6 %, there is a risk of formation of such an amount of intermetallic phases in a nickel based matrix that the ductility of the material is considerably deteriorated (this will also be discussed below with reference to Figure 3). The alloy should therefore comprise 4-6 % Al, such as >4-5.5 %, such as >4 - 5.2 % A1.
Iron
It has been shown in accordance with the present invention that relatively high contents of Fe in an aluminium oxide forming nickel based alloy can have positive effects.
Additions of Fe generate a metallic structure which is energetically unfavourable for the formation of embritteling γ', which in turn leads to the risk of the alloy becoming hard and brittle reducing considerably. Consequently, the workability is improved. Therefore, the alloy comprises at least 15 % Fe. High contents of iron may however lead to formation of unwanted phases. Therefore, the alloy shall not comprise more than 25 % Fe.
Moreover, at Fe contents over approximately 21-22 %, the risk of formation of a β-phase ( iAl), which in some cases can be embritteling, increases. The alloy should therefore comprise 16-21.5 % Fe. According to a preferred embodiment, the alloy comprises 17-21 % Fe.
Nickel
The alloy according to the invention is a nickel based alloy. Nickel is an element which stabilises an austenitic structure in alloys and thereby counteracts formation of some brittle intermetallic phases, such as σ-phase. The austenitic structure of the alloy is beneficial for example when it comes to welding. The austenitic structure also contributes to the good creep strength of the alloy at high temperatures. This could be a result of that the diffusion rate is lower in an austenitic structure than for example in a ferritic.
According to one embodiment, the alloy comprises 52-62 % Ni, such as 52-60% Ni.
Cobalt
In some commercial alloys, a part of the Ni is substituted with Co in order to increase the mechanical strength of the alloy which may also be done in the alloy according to the invention. A part of the Ni of the alloy can be replaced with an equal amount of Co. This Co addition must however be balanced against the oxidation properties since the presence of NiAl will reduce the activity of Al and thereby deteriorate the ability to form aluminium oxide. According to one embodiment of the present invention, nickel is partly substituted with Co. The Co content shall, however, not exceed 5%. Nitrogen
In the same way as C, free N takes interstitial locations in the crystal structure and thereby locks the dislocation mobility at temperatures up to approximately 400-500°C. Nitrogen also forms nitrides and/or carbon nitrides with other elements in the alloy such as Ta, Ti, Hf, Zr and Nb. In a microstructure where these particles are finely dispersed they confer obstacles for the dislocation mobility, especially at higher temperatures.
Therefore, N is added in order to improve the creep strength of the alloy. However, when
adding N to aluminium alloyed alloys the risk is high for formation of secondary aluminium nitrides and the present nickel based alloy therefore has a very limited N content. The alloy comprises 0.03-0.15 % N, such as 0.05-0.15 % N, such as 0.05-0.10 % N.
Oxygen
Oxygen may be present in the present alloy either in the form of an impurity, or as an active addition up to 0.5 %. Oxygen may contribute to increasing the creep strength of the alloy by forming small oxide dispersions together with Zr, Hf, Ta and Ti, which, when they are finely distributed in the alloy, improves its creep strength. These oxide dispersions have higher dissolution temperature than corresponding carbides and nitrides, whereby oxygen is a preferred addition for use at high temperatures. Oxygen may also form dispersions with Al, the elements in group 3 of the periodic table, Sc, Y and La as well as the fourteen lanthanides, and in the same manner as with the above identified elements thereby contribute to higher creep strength of the alloy. According to a preferred embodiment, the alloy comprises 200-2000 ppm O, such as 400-1000 ppm O.
Tantalum, Hafnium, Zirconium, Titanium and Niobium
The elements in the group consisting of Ta, Hf and Zr forms very small and stable particles with carbon and nitrogen. It is these particles which, if they are finely dispersed in the structure, help to lock dislocation movement and thereby increase the creep strength, i.e. provides the dispersion strengthening. It is also possible to accomplish this effect with addition of Ti. Additions of Ti can, however, sometimes lead to problems, especially during powder metallurgical production of the alloy, since it forms carbides and nitrides already in the melt before atomisation, which in turn may clog the orifice during the atomisation.
Niobium also forms stable dispersions with C and or N and can therefore suitably be added to the alloy according to the invention.
The alloy comprises one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b in an amount of 0.25-2.2 %, such as 0.3-1.5 %, such as 0.6-1.5 %.
The alloy may also comprise such an amount of the elements Ta, Zr, Hf, Ti and Nb that essentially all C and N is bound to these elements. This ensures that for example the risk of formation of chromium carbides during high temperature use of the alloy is significantly reduced.
According to a preferred embodiment, the alloy as defined hereinabove or hereinafter comprises 0.1 -0.5% Hf. According to another embodiment, the alloy comprises 0.05-0.35 % Zr. According to yet another embodiment, the alloy comprises 0.05-0.5 % Ta.
According to yet another embodiment, the alloy comprises 0.05-0.4 % Ti. According to yet another embodiment, the alloy comprises 0.1-0.8 % Nb. Rare earth metals (REM)
Rare earth metals (REM) relates in this context to the elements of group three of the periodic table, Sc, Y, and La as well as the fourteen lanthanides. REM affects the oxidation properties by doping of the formed oxide. Excess alloying of these elements often gives an oxide which tends to spall of the surface and a too low addition of these elements tends to give an oxide with weaker adhesion to the metal surface. The alloy may comprise one or more elements from the group consisting of REM in a content of up to 0.5 % in total, such as 0.05-0.25 %. According to a one embodiment, yttrium is added to the alloy as defined hereinabove or hereinafter in an amount of 0.05-0.25 %. The nickel based alloy as defined hereinabove or hereinafter may also comprise normally occurring impurities as a result of the raw material used or the selected manufacturing process. Examples of impurities are Ca, S and P. Furthermore, other alloying elements, which will not affect the properties of the alloy may optionally be added in amounts up to 1 %.
When the term "max" is used, the skilled person knows that the lower limit of the range is 0 wt% unless another number is specifically stated.
The prenickel-based alloy as defined hereinabove or hereinafter may be manufactured according to conventional methods, i.e. casting followed by hot working and/or cold working and optional additional heat treatment. The nickel-based alloy as defined hereinabove or hereinafter may also be used produced as a powder product by for example hot isostatic pressure process (HIP).
The present disclosure is further illustrated by the following non-limiting examples. Examples
Two alloys were used in these examples. The compositions of the alloys are shown in table 1. Alloy 1 is an alloy according to the present disclosure, and Alloy 2 is an austenitic nickel-chromium-iron alloy of the standard U S N06600.
The alloys were exposed in an atmosphere containing 5% ¾ and 95% N2, with a dew point below -40°C, reminiscent of the environment in a sintering furnace. Two exposure temperatures were used; 900°C and 1150°C. The effect of pre-oxidation was investigated.
Sample coupons with the dimensions 10 x 15 x 2 mm with one corner cut off were machined and ground with successively finer grinding paper, ending at 600 grit. After grinding, the dimensions of the samples were measured and identification numbers were punched into the edges of the samples. Prior to exposure, the samples were cleaned and degreased in ethanol and acetone and the mass of each sample was recorded using a Sartorius microbalance with microgram resolution. The samples were mounted in cylindrical crucibles and exposed in horizontal tube furnaces. Half of the samples were pre-oxidized at 1150°C for 20 minutes prior to the exposure to the nitriding atmosphere. The parameters for the pre-oxidation were selected to resemble the final hot step of the production of tubes.
Table 1 - The compositions of the tested alloys (wt%)
Exposures were performed at 900°C and 1150°C. The atmosphere consisted of 95% nitrogen and 5% hydrogen. The dew point was kept below -40°C and continuously monitored using hygrometers. The exposure times were 200, 500 and 1500 hours at both temperatures. The exposures were isothermal, with each sample being exposed once only. Analysis
After exposure, the mass changes of the samples were recorded (see figure la and b) and selected samples were cut in half parallel to the longest axis and mounted in polyfast conductive plastic, and polished with a Ιμηι diamond suspension to produce flat cross sections for microscopy.
The micro structural analysis was done using two different microscopes. One was a Zeiss EVO 50 variable pressure scanning electron microscope (VP-SEM), and the other was a Zeiss Sigma VP-SEM. An acceleration voltage of 20 kV was used for imaging and chemical analysis by energy dispersive spectroscopy (EDS). Back scattered (BSE) were used for imaging. Figure 2— discloses examples of the microscope studie.
Result
The mass changes at 900°C for all materials are shown in figure la). As can be seen for Figure 1 , the alloy of the disclosure both the pre-oxidized and the non-oxidized had the lowest mass change. The lowest mass change was exhibited by the pre-oxidized alloy of the present disclosure samples, while the corresponding samples that were not pre-
oxidized had the second lowest mass changes. The mass changes of sample of alloy 2 were higher.
In figure lb), the mass changes at 1150°C are shown. As can be seen from figure, the mass gains all of the samples are low. Thus, these results indicate that the samples of the alloy of the present invention will not gain mass by forming nitrides. Even though alloy 2 had the lowest mass change, figure 2c shows that nitrides are formed, to be compared with figure 2b (the present alloy) wherein no nitrides are formed. Thus alloy 2 is not suitable to be used in the conditions defined herein even though it had the lowest mass gain.
Hence, the result as shown in Figure 1 a and Figure lb shows that the samples of the alloy of the present disclosure has very little mass gain thus indicating that almost no nitrides are formed.
As can be seen from Figures 2a and b, the alloy according to the disclosure shows a nitridation resistance in 5% H2 - 95% N2. At 1150°C, there is no sign of nitridation on and at 900°C, only modest nitridation is seen on samples of the present nickel based alloy that have not been pre-oxidized. Without being bound to any theory, it is believed that it is possible this may be due to formation of transient alumina.
Further, as can be seen from the figure 2c, nitrides are formed on the surface of alloy 2, which makes it unsuitable for the conditions defined herein. Hence, both figure la and figure lb and the photos, an alloy of the present disclosure can be used in nitriding environments, especially at higher temperatures as the alloy will almost form no nitrides which keep the aluminum oxide layer undamaged and thereby preventing corrosion.
Claims
Claims
An object comprising a pre-oxidized nickel based alloy comprising percent by weight (wt-%)
C 0.05-0.2;
Si max 1.5;
Mn max 0.5;
Cr 15-20;
Al 4-6;
Fe 15-25;
Co max 5;
N 0.03-0.15;
0 max 0.5;
one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b 0.25-2.2;
one or more elements selected from the group consisting of REM max 0.5;
balance Ni and normally occurring impurities.
The object according to claim 1, wherein the pre-oxidized nickel-based alloy comprises 16-21.5 wt-% Fe.
The object according to claim 1 or 2, wherein the pre-oxidized nickel-based alloy comprises 17-20 wt-% Cr.
The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy comprises max 0.3 wt-% Si.
5. The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy comprises max 1 wt% Co
6. The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy one or more elements selected from the group consisting of REM in a total content of 0.05-0.25 wt-%.
The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy comprises one or more elements selected from the group consisting of Ta, Zr, Hf, Ti and b in a total content of 0.3-1.5 %.
The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy comprises >4-5.5 wt-% Al.
9. The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy comprises 200-2000 ppm O.
The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy comprises 52-62 wt-% Ni.
The object according to any preceding claims, wherein the pre-oxidized nickel-based alloy according to any preceding claims is oxidized before
12. Manufacture of an object comprising the pre-oxidized nickel-based alloy as defined in any preceding claims wherein said manufacture comprises a step of preoxidation.
13. Use of an object comprising the pre-oxidized nickel-based alloy according to any one of claims 1 to 11, wherein said use is in an atmosphere comprising a high concentration of nitrogen and a low oxygen partial pressure.
14. The use according to claim 13, wherein said use also comprises a high
temperature.
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP17723722.9A EP3458620A1 (en) | 2016-05-20 | 2017-05-19 | An object comprising a pre-oxidized nickel-based alloy |
CN201780031213.2A CN109154038A (en) | 2016-05-20 | 2017-05-19 | The alloy body of nickel-base alloy comprising pre-oxidation |
US16/302,788 US20190292631A1 (en) | 2016-05-20 | 2017-05-19 | An object comprising a pre-oxidized nickel-based alloy |
JP2018560765A JP2019519677A (en) | 2016-05-20 | 2017-05-19 | Object containing preoxidized nickel base alloy |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP16170756.7 | 2016-05-20 | ||
EP16170756 | 2016-05-20 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2017198831A1 true WO2017198831A1 (en) | 2017-11-23 |
Family
ID=56068752
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/EP2017/062136 WO2017198831A1 (en) | 2016-05-20 | 2017-05-19 | An object comprising a pre-oxidized nickel-based alloy |
Country Status (5)
Country | Link |
---|---|
US (1) | US20190292631A1 (en) |
EP (1) | EP3458620A1 (en) |
JP (1) | JP2019519677A (en) |
CN (1) | CN109154038A (en) |
WO (1) | WO2017198831A1 (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020126053A1 (en) * | 2018-12-21 | 2020-06-25 | Sandvik Intellectual Property Ab | New use of a nickel-based alloy |
CN111910148A (en) * | 2020-08-28 | 2020-11-10 | 浙江华达新型材料股份有限公司 | Method for forming compact oxide film on surface of Fe-Mn-Al alloy |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111088447B (en) * | 2020-03-12 | 2021-06-29 | 王军伟 | Pre-oxidized Ni-Fe-Al series alloy used in molten chloride and pre-oxidation process |
CN114230154B (en) * | 2021-12-22 | 2022-11-22 | 东海县太阳光新能源有限公司 | Quartz crucible with long service life and low deformation rate and preparation method thereof |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2000034541A1 (en) * | 1998-12-09 | 2000-06-15 | Inco Alloys International, Inc. | High strength alloy tailored for high temperature mixed-oxidant environments |
WO2009045136A1 (en) * | 2007-10-05 | 2009-04-09 | Sandvik Intellectual Property Ab | The use and method of producing a dispersion strengthened steel as material in a roller for a roller hearth furnace |
EP2367963A1 (en) * | 2008-11-19 | 2011-09-28 | Sandvik Intellectual Property Ab | Aluminium oxide forming nickel based alloy |
EP2617858A1 (en) | 2012-01-18 | 2013-07-24 | Sandvik Intellectual Property AB | Austenitic alloy |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS58207352A (en) * | 1982-05-28 | 1983-12-02 | Mitsubishi Metal Corp | Cast ni alloy for guide shoe |
DE102012015828B4 (en) * | 2012-08-10 | 2014-09-18 | VDM Metals GmbH | Use of a nickel-chromium-iron-aluminum alloy with good processability |
JP6247977B2 (en) * | 2014-03-28 | 2017-12-13 | 株式会社クボタ | Cast products having an alumina barrier layer |
-
2017
- 2017-05-19 JP JP2018560765A patent/JP2019519677A/en active Pending
- 2017-05-19 EP EP17723722.9A patent/EP3458620A1/en not_active Withdrawn
- 2017-05-19 WO PCT/EP2017/062136 patent/WO2017198831A1/en unknown
- 2017-05-19 CN CN201780031213.2A patent/CN109154038A/en active Pending
- 2017-05-19 US US16/302,788 patent/US20190292631A1/en not_active Abandoned
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2000034541A1 (en) * | 1998-12-09 | 2000-06-15 | Inco Alloys International, Inc. | High strength alloy tailored for high temperature mixed-oxidant environments |
WO2009045136A1 (en) * | 2007-10-05 | 2009-04-09 | Sandvik Intellectual Property Ab | The use and method of producing a dispersion strengthened steel as material in a roller for a roller hearth furnace |
EP2367963A1 (en) * | 2008-11-19 | 2011-09-28 | Sandvik Intellectual Property Ab | Aluminium oxide forming nickel based alloy |
EP2617858A1 (en) | 2012-01-18 | 2013-07-24 | Sandvik Intellectual Property AB | Austenitic alloy |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020126053A1 (en) * | 2018-12-21 | 2020-06-25 | Sandvik Intellectual Property Ab | New use of a nickel-based alloy |
CN111910148A (en) * | 2020-08-28 | 2020-11-10 | 浙江华达新型材料股份有限公司 | Method for forming compact oxide film on surface of Fe-Mn-Al alloy |
Also Published As
Publication number | Publication date |
---|---|
JP2019519677A (en) | 2019-07-11 |
US20190292631A1 (en) | 2019-09-26 |
CN109154038A (en) | 2019-01-04 |
EP3458620A1 (en) | 2019-03-27 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
Brady et al. | The development of alumina-forming austenitic stainless steels for high-temperature structural use | |
EP1842934B1 (en) | Heat-resistant superalloy | |
JP5596697B2 (en) | Aluminum oxide forming nickel base alloy | |
WO2015159554A1 (en) | Austenitic stainless steel and method for producing same | |
JPH04272154A (en) | Oxidation resisting low expanding super-alloy | |
WO2017198831A1 (en) | An object comprising a pre-oxidized nickel-based alloy | |
EP3230481B1 (en) | A ferritic alloy | |
WO2008086141A1 (en) | Oxidation resistant high creep strength austenitic stainless steel | |
KR102486432B1 (en) | Uses of Nickel-Chromium-Iron-Aluminum Alloys | |
KR20190065352A (en) | NiCrFe alloy | |
JP5047456B2 (en) | Precipitation strengthened nickel-iron-chromium alloy and method of processing the same | |
EP3169820A1 (en) | Corrosion resistant article and methods of making | |
JP5554180B2 (en) | Austenitic stainless steel | |
US20100021338A1 (en) | High-temperature alloy | |
Fahrmann et al. | HAYNES NS-163 Alloy: A Novel Nitride Dispersion-Strengthened Co-Base Alloy | |
WO2023086006A1 (en) | A ferritic iron-chromium-aluminum powder and a seamless tube made thereof | |
WO2023086007A1 (en) | A fecral powder and an object made thereof | |
Kratochvil et al. | Creep behaviour of the intermetallic Fe-28Al-3Cr alloy | |
CN115707788A (en) | Heat-resistant alloy material and elastic member obtained by processing and forming the same | |
Yoshihra et al. | The oxidation behavior of engineering gamma TiAl alloys | |
Fu et al. | STRAIN RATE DEPENDENCE ON THE HIGH TEMPERATURE MECHANICAL BEHAVIOR OF THE NI-18 SI-3.0 NB-1.0 CR-0.2 B INTERMETALLIC ALLOY | |
JPH08159691A (en) | Radiant tube |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2018560765 Country of ref document: JP Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 17723722 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2017723722 Country of ref document: EP Effective date: 20181220 |