CA2186842A1 - Highly heat-resistant nickel-based alloy and its use - Google Patents
Highly heat-resistant nickel-based alloy and its useInfo
- Publication number
- CA2186842A1 CA2186842A1 CA002186842A CA2186842A CA2186842A1 CA 2186842 A1 CA2186842 A1 CA 2186842A1 CA 002186842 A CA002186842 A CA 002186842A CA 2186842 A CA2186842 A CA 2186842A CA 2186842 A1 CA2186842 A1 CA 2186842A1
- Authority
- CA
- Canada
- Prior art keywords
- nickel
- max
- nitrogen
- based alloy
- alloy
- 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.)
- Abandoned
Links
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
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F27—FURNACES; KILNS; OVENS; RETORTS
- F27D—DETAILS OR ACCESSORIES OF FURNACES, KILNS, OVENS, OR RETORTS, IN SO FAR AS THEY ARE OF KINDS OCCURRING IN MORE THAN ONE KIND OF FURNACE
- F27D3/00—Charging; Discharging; Manipulation of charge
- F27D3/02—Skids or tracks for heavy objects
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Conductive Materials (AREA)
- Furnace Charging Or Discharging (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
A highly heat and oxidation-resistant hot- and cold-formable nickel-based alloy with a massive nitrogen content, for the production of objects which must be resistant against oxidation and carbonisation at temperatures in the range of 750 to 1,200°C, even under cyclic exposures, consisting (in mass %) of 0.001 to 0.15% carbon, 0.10 to 3.0% silicon, max. 0.5% manganese, max. 0.015% phosphorus, max. 0.005% sulphur, 28 to 33% chromium, max. 2.0% iron, max. 0.3% aluminium, 0.25 to 1.2% nitrogen, 0.001 to 0.01%; boron, 0.01 to 0.5% yttrium, cerium, lanthanum, zirconium, hafnium and tantalum alone or in combination, the remainder being constituted of nickel and the usual admixtures from the smelting process, with the nickel content being a least 64.0%. The invention also concerns the use of this alloy as a material for objects such as gas turbines, furnace components and heat conductors.
Description
ecT/EPg5/oo762 2186~42 Krupp VDM GmbH
Highly heat-resistant nickel-based alloy and its use.
The invention relates to highly heat-resistant nickel-based alloys. For objects which must be resistant against carbonisation and oxidation in the temperature range of 750 to 1,200C, in particular under cyclic exposures, the nickel alloy with the material number 2 . q658 is used. This alloy, with the letter symbol NiCr7030, consists according to the steel key 1992 of (data in mass %): max 0.10 carbon, 0 . 50 to 2 . 00 silicon, max . 1. 0 manganese, max . 0 . 020 phosphorus, max . 0 . 015 sulphur, 29 . 0 to 32 . 0 chromium, min.
60.0 nickel, max. 0.3 aluminium, :~ax. 5.0 iron and max.
0 . 50 copper . A relatively inexpensive heat-resistant nickel-based alloy comprising 0 . 05 to 0 .15 % C, 2 . 5 to 3 9~
Si, 0.2 to 0.5 96 Mn, 25 to 30 % Cr, 0.05 to 0.15 5; A1 and lo~ contents of P and S is known from DE-PS ql 30 139, which contains next to 20 to 27 P~ Fe and 0 . 05 to 0 . 2 % ~1 also 0 . 05 to 0 .15 % rare eart~ls and 0 . 001 to 0 . 005 % Ca, and w~ich fully meets the requirements of numerous applications. This known alloy is characterized by resistance to carbonisation, sulphidizing and oxidation at operating temperatures of 500 to 1, 000C as well as by hot formability. I~owev,er, the thermal endurance and creep strenth depending on time are relatively ~ow for a temperature range of 750 to 1, 200C . The gervice life can be influenced in an unfavourable way in pi-actice, e.g. in the construction of furnaces and instal lations .
The high iror~ content of the aforen~entioned nickel-based alloy leads to the coJlsideration of heat-resistant iron-based alloys with high nickel contents, as in ~he case of t~le molybdenum--alloyed basic irorl material as krlown from US-PS 5 077 006, ` with 12 to 32 % Cr and 8 to 62 % Ni as well as additional alloys of W, Cb, Ti, Zr and rare earths and optionally also additions with 0 . 05 % B.
Furthermore, from EP-OS 0 3.91 381 a carbon-rich heat-resistant iron-based alloy with 23 to 30 % Cr and 40 to 55 % ~i, which is partly replaceable by Co, is known which contains up to 0 2 % N and less than 1 % Nb, Ti, Zr and can additionally comprise small quantities of Al, Ca, B and Y.
As a result of the cooperation of titanium and nitrogen a high creep strength has been reached at the expense of the hot and cold formability.
The general demand for resistance at high operating temperatures can regularly be fulfilled better with nickel-based alloys, so that the type of the invention is based thereon .
It is the object of the invention to provide a nickel-based alloy which can be used without any limitations under oxidizing and carbonising conditions, in particular under cyclic exposures in the temperature range of 750 to 1, 200C
with sufficient thermal endurance and creep strength depending on time and which takes into account the forming requirements by hot and cold formability in the production of wrought prQducts such as in the production of apparatuses and devices. A further object is representing the applications for the alloy.
This obj ect is achieved by a highly heat and oxidation-resistant hot- and cold-formable nickel-based alloy with a massive nitrogen content, consisting (in mass %) of 0. 001 to 0_I5 % ~ carbon 0 .10 to ~. 0 % silicon max . 0 . 5 % manganese max . 0 . 015 % phosphorus max . 0 . 005 % sulphur 28 to 33 % chromium max . 2 . 0 % iron max . 0 . 3 % aluminium 0 . 25 to 1. 2 % nitrogen 0 . 001 to 0 . 01 ~ boron 0 . 01 to 0 . 5 % yttrium, cerium, lanthanum, zirconium, hafnium and tantalum alone or in combination, the remainder being constituted of nickel and the usual admixtures from the smelting process, with the nickel content being at least 64 . 0 % .
Preferable are nitrogen contents of 0 . 35 to 0 . 8 % .
T~e nickel-based alloy in accordance with the invention is highly suitable as material for producing objects which must be resistant to oxidation and carbonisation at temperatures in the range of 750 to 1, 200C, even under cyclic exposures. It is therefore provided as material for gas turbines and is also il~tended for the aircraft industry, and it is a material for the production of furnace components such as supporting frames for burning kilrls, conveyor rails and conveyor belts and heat treatment ir~stallations, and is also suitable as material for heat conductors .
T~le use of the nickel-based alloy as material for cast parts which become hot and naturally have to be cast under pressure is also considered.
T~e nic}.el-based alloys with 0 . 25 to 1. 20 weight % of nitrogen can be produced by the addition of nitrogen carriers such as c~lromium nitride and/or silicon nitride in t~le liquid condition or under a llitrogen gas atmosphere with t~le help of pressure metallurgy.
2186844~
For t~le production of steels ~llth massive nitrogen content, i.e. of steels with nitrogen contents above the solubility threshold at 1, 600C and 1 bar nitrogen pressure, the process of pressure electroslag refining is k.nown and particularly suitable (see patent specification DE 29 24 415 C2). In this process the alloy to be nitrided is sub~ected to high pressures during the entire remelting process, from the liquid condition to the complete solidification .
It has proved to be advantageous to use this n~ethod also for producing the nickel-based alloy with massive nitrogen content in accordance with the invention.
All metallurgical methods in which smelting and casting occur under pressure are suitable for the production of the alloy in accordance with the invention.
1~1hen using suitable casting methods, cast components or elements can be produced from the nickel-based alloy in accordance with the invention.
The nickel-based alloy in accordar~ce ~ith the invention will be described below and explained in closer detail by reference to examples. The claimed alloy ranges are explained as follo~s:
Ca rboll ( C ):
Through a mixed crystal hardening and the discarding of carbides, carbon leads to an increase of the thermal endurance and creep strength depending on ~ime of the material. The lo~.ler lirr,it of t~le analytical span is predetermined by the d~creasing effect of the carbon on the improvement of the therrnal endurance and creep strength depending on time, whereas the upper limit of 0.15 weight %
is given by the increasingly limited cold formability.
- ~ 2186842 Silicon ~Si):
Silicon is used in the present material not only as deoxidant, but can be used in addition as nitrogen carrier in the massive nitride hardening of the alloy and as additive to improve the oxidation resistance. The cyclic oxidation resistance in particular can be improved considerably by silicon contents of up to 3 weight %.
Higher contents will have an adverse effect on the hot formability behaviour, whereas contents of less than 0.10 ~eight t have proved to be ineffective.
Chromium (Cr):
The addition of chromium improves the oxidation resistance of the alloy considerably. At the same time, chromium increases the solubility of nickel for nitrogen. In connection with sufficient high contents of nitrogen there is a discarding of chromium nitrides which permanently improves the creep strength dependirlg on time of the alloy.
Chromium contents of over 33 weight % lead to an impaired hot formability, whereas contents under 28 weight % do not cause a sufficiently large quantity of discarded chromium nitrides, so that contents between 28 and 33 weight ~ have proved to be optimal.
Nitrogen (N):
T~e addition of nitrogen to the alloy causes both a rise in the thermal endurance by mixed crystal hardening as well as in the creep strength depending on time by the discarding of chromium nitrides.
If the nitrogen content is below 0.25 weight ~, however, no 2ppreciable irlfluence on the increase in hardness of the alloy can be expected. Contents over 1. 20 weight % of nitrogen are metallurgically possible, but they require an increased effort~s to achieve precise adjustment, so that itrogen contents between 0.25 and 1.20 welght ~ have 21~684~
proved to be desirable within t~le scope of the ~lorks for this invention.
Boron ~ B ):
The creep strength deper]ding on time is increased by the additioll of up to 0 . 010 weight g6 of boron to the alloy.
~igher contents will lead to reduced hot formability by the formation of low-meLting phases on the grain boundaries Contents of lower than 0 . 001 weight 9~ have proved to be inef fective .
Nickel ~Ni ):
The addition of nickel not only favo~lrably influences the oxidation resistance of the alloy, in particular with a simultaneous presence of chromium by the nickel-chromium spinel formation, but also the cal~bonisation resistance.
Nickel contents of at least 6~ '~ are not mandatorily required for this reason, but because only from these nickel contents onwards a sufficient quantity of chromium nitrides will be discarded which are absolutely required for the creep strength depending on time.
Yttrium (Y), cerium ~Ce), lanthanum (La), zirconiunl (2r), hafnium (~f) and tanta~um (Ta):
All these elements are effective in the improvement of the t formability of the alloy.
Eor this reason it is necessary thc~t at least one of the aforementiolled alloy elements must be present when the alloy is subjected to extrer~e }lOt forming operations. On the other hand, contents of over 0 . 50 weight ~ of one or several of t~lese alloy elen ents have proved to be more detrimental to the hot formability.
It ~as furt~ler seen that yttrium, cerium, lant~lanum, zirconium, hafrlium and tantalum, alone or in combination, lead to a considerable improvement of the cycli.c oxidation resistance of the alloy.
The nickel-based alloys 1 to 6 are explaineà below in closer detail in comparison with the known standard alloys 8 to 11.
The actual analyses of the alloys 1 to 11 are shown in table 1.
Fig. 1 sho~s the creep strength depending on time of the alloys ] to 6 il~ accordance with the invention in comparison with the standard alloys 8 to 11 at a permanent temperature of 1, 000C which is typical for a later use .
The stress is shown herein on the ordinate in form of the tension in N/rt~rr,2 to which the sample is subjected over the logarithmized endurance time in hours on the abscisse.
The two spread bands for the alloys 1 to 6 and 8 to 11 contain the breaking pOillts of the individual alloys. The considerably better creep strength depending on time of the alloys 1 to 6 in accordance with t~le invention over the standard alloys 8 to 11 can be recognized by the shift of the spread band curve for the alloys 1 to 6 towards higher tensions. It can be seen that with the alloys 1 to 6 in accordance with the invention it is possible to achieve approx. 2 . 5 times higher creep strengths depending on time as compared ~lith standard alloys 8 to 11.
Fig 2 descr}bes the thermal endurance of the alloys 1 to 6 in comparison with the alloys 8 to 11.
T~le tensile strength is applied here in N/mm2 on the ordinate against the testing temperature i~l ~C on the abscisse .
8 21~86g42 The alloys 1 to 6 in accordance with the invention are provided in the spread band application over the entire temperature range of room temperature up to 1, 200C with the considerably higher thermal endurances as compared ~lith the standard alloys a to 11.
The results of the oxidation examinations show that by the alloying of nitrogen no deterioration of the o%idation resistance occurs as compared with nitrogen-free standard alloys. On the contrary, the standard alloys and the alloys in accordance with the invention are within the spread band for measured value fluctuations for 750C, 1,000C and 1, 200C .
ig. 3 describes in this respect the cyclic oxidation resistance of the alloys 1 to 6 i,n accordance with the invention in comparison Wit}l the standard alloys a to 11 for the testing temperatures of 750, l,000C and 1,200C.
T~le fi gure shows the change in mass in g/m2h standardized for the examination time and the surface of the sample. The examination occurred in the air, with a cycle period of 24 hours at a dwell time at testing temperature of 16 hours with 2 hours heating time and 6 hours cooling time.
2186~2 _ 9 _ _ O
~o ~ r- o _ o 3 r o I ~ I I I I I o o ,~
o ~
,~ o o ~
~ ~ o ~
~ .
, o , , , ~ t o o o o o o o o o o o o o o o o o o , , I
o C~ o o o o , o ô o C~
o - o o o o . o cO O ~ O O r~ _ --I
oo o o o o o o o o o o o o o o o o o o o o o o o o o -L_, o o o o o o , o o o o o o o o o o _ ~
o o o o o o o o o U'~ o o o o o o o o o O O o~
o o o o o o o o o o . . . _ ~_U~ o o _ ~ o o O ~ r.
o o o o o o o o o ~
~,o o o o o o o o o o < ~ C ~ C <
Highly heat-resistant nickel-based alloy and its use.
The invention relates to highly heat-resistant nickel-based alloys. For objects which must be resistant against carbonisation and oxidation in the temperature range of 750 to 1,200C, in particular under cyclic exposures, the nickel alloy with the material number 2 . q658 is used. This alloy, with the letter symbol NiCr7030, consists according to the steel key 1992 of (data in mass %): max 0.10 carbon, 0 . 50 to 2 . 00 silicon, max . 1. 0 manganese, max . 0 . 020 phosphorus, max . 0 . 015 sulphur, 29 . 0 to 32 . 0 chromium, min.
60.0 nickel, max. 0.3 aluminium, :~ax. 5.0 iron and max.
0 . 50 copper . A relatively inexpensive heat-resistant nickel-based alloy comprising 0 . 05 to 0 .15 % C, 2 . 5 to 3 9~
Si, 0.2 to 0.5 96 Mn, 25 to 30 % Cr, 0.05 to 0.15 5; A1 and lo~ contents of P and S is known from DE-PS ql 30 139, which contains next to 20 to 27 P~ Fe and 0 . 05 to 0 . 2 % ~1 also 0 . 05 to 0 .15 % rare eart~ls and 0 . 001 to 0 . 005 % Ca, and w~ich fully meets the requirements of numerous applications. This known alloy is characterized by resistance to carbonisation, sulphidizing and oxidation at operating temperatures of 500 to 1, 000C as well as by hot formability. I~owev,er, the thermal endurance and creep strenth depending on time are relatively ~ow for a temperature range of 750 to 1, 200C . The gervice life can be influenced in an unfavourable way in pi-actice, e.g. in the construction of furnaces and instal lations .
The high iror~ content of the aforen~entioned nickel-based alloy leads to the coJlsideration of heat-resistant iron-based alloys with high nickel contents, as in ~he case of t~le molybdenum--alloyed basic irorl material as krlown from US-PS 5 077 006, ` with 12 to 32 % Cr and 8 to 62 % Ni as well as additional alloys of W, Cb, Ti, Zr and rare earths and optionally also additions with 0 . 05 % B.
Furthermore, from EP-OS 0 3.91 381 a carbon-rich heat-resistant iron-based alloy with 23 to 30 % Cr and 40 to 55 % ~i, which is partly replaceable by Co, is known which contains up to 0 2 % N and less than 1 % Nb, Ti, Zr and can additionally comprise small quantities of Al, Ca, B and Y.
As a result of the cooperation of titanium and nitrogen a high creep strength has been reached at the expense of the hot and cold formability.
The general demand for resistance at high operating temperatures can regularly be fulfilled better with nickel-based alloys, so that the type of the invention is based thereon .
It is the object of the invention to provide a nickel-based alloy which can be used without any limitations under oxidizing and carbonising conditions, in particular under cyclic exposures in the temperature range of 750 to 1, 200C
with sufficient thermal endurance and creep strength depending on time and which takes into account the forming requirements by hot and cold formability in the production of wrought prQducts such as in the production of apparatuses and devices. A further object is representing the applications for the alloy.
This obj ect is achieved by a highly heat and oxidation-resistant hot- and cold-formable nickel-based alloy with a massive nitrogen content, consisting (in mass %) of 0. 001 to 0_I5 % ~ carbon 0 .10 to ~. 0 % silicon max . 0 . 5 % manganese max . 0 . 015 % phosphorus max . 0 . 005 % sulphur 28 to 33 % chromium max . 2 . 0 % iron max . 0 . 3 % aluminium 0 . 25 to 1. 2 % nitrogen 0 . 001 to 0 . 01 ~ boron 0 . 01 to 0 . 5 % yttrium, cerium, lanthanum, zirconium, hafnium and tantalum alone or in combination, the remainder being constituted of nickel and the usual admixtures from the smelting process, with the nickel content being at least 64 . 0 % .
Preferable are nitrogen contents of 0 . 35 to 0 . 8 % .
T~e nickel-based alloy in accordance with the invention is highly suitable as material for producing objects which must be resistant to oxidation and carbonisation at temperatures in the range of 750 to 1, 200C, even under cyclic exposures. It is therefore provided as material for gas turbines and is also il~tended for the aircraft industry, and it is a material for the production of furnace components such as supporting frames for burning kilrls, conveyor rails and conveyor belts and heat treatment ir~stallations, and is also suitable as material for heat conductors .
T~le use of the nickel-based alloy as material for cast parts which become hot and naturally have to be cast under pressure is also considered.
T~e nic}.el-based alloys with 0 . 25 to 1. 20 weight % of nitrogen can be produced by the addition of nitrogen carriers such as c~lromium nitride and/or silicon nitride in t~le liquid condition or under a llitrogen gas atmosphere with t~le help of pressure metallurgy.
2186844~
For t~le production of steels ~llth massive nitrogen content, i.e. of steels with nitrogen contents above the solubility threshold at 1, 600C and 1 bar nitrogen pressure, the process of pressure electroslag refining is k.nown and particularly suitable (see patent specification DE 29 24 415 C2). In this process the alloy to be nitrided is sub~ected to high pressures during the entire remelting process, from the liquid condition to the complete solidification .
It has proved to be advantageous to use this n~ethod also for producing the nickel-based alloy with massive nitrogen content in accordance with the invention.
All metallurgical methods in which smelting and casting occur under pressure are suitable for the production of the alloy in accordance with the invention.
1~1hen using suitable casting methods, cast components or elements can be produced from the nickel-based alloy in accordance with the invention.
The nickel-based alloy in accordar~ce ~ith the invention will be described below and explained in closer detail by reference to examples. The claimed alloy ranges are explained as follo~s:
Ca rboll ( C ):
Through a mixed crystal hardening and the discarding of carbides, carbon leads to an increase of the thermal endurance and creep strength depending on ~ime of the material. The lo~.ler lirr,it of t~le analytical span is predetermined by the d~creasing effect of the carbon on the improvement of the therrnal endurance and creep strength depending on time, whereas the upper limit of 0.15 weight %
is given by the increasingly limited cold formability.
- ~ 2186842 Silicon ~Si):
Silicon is used in the present material not only as deoxidant, but can be used in addition as nitrogen carrier in the massive nitride hardening of the alloy and as additive to improve the oxidation resistance. The cyclic oxidation resistance in particular can be improved considerably by silicon contents of up to 3 weight %.
Higher contents will have an adverse effect on the hot formability behaviour, whereas contents of less than 0.10 ~eight t have proved to be ineffective.
Chromium (Cr):
The addition of chromium improves the oxidation resistance of the alloy considerably. At the same time, chromium increases the solubility of nickel for nitrogen. In connection with sufficient high contents of nitrogen there is a discarding of chromium nitrides which permanently improves the creep strength dependirlg on time of the alloy.
Chromium contents of over 33 weight % lead to an impaired hot formability, whereas contents under 28 weight % do not cause a sufficiently large quantity of discarded chromium nitrides, so that contents between 28 and 33 weight ~ have proved to be optimal.
Nitrogen (N):
T~e addition of nitrogen to the alloy causes both a rise in the thermal endurance by mixed crystal hardening as well as in the creep strength depending on time by the discarding of chromium nitrides.
If the nitrogen content is below 0.25 weight ~, however, no 2ppreciable irlfluence on the increase in hardness of the alloy can be expected. Contents over 1. 20 weight % of nitrogen are metallurgically possible, but they require an increased effort~s to achieve precise adjustment, so that itrogen contents between 0.25 and 1.20 welght ~ have 21~684~
proved to be desirable within t~le scope of the ~lorks for this invention.
Boron ~ B ):
The creep strength deper]ding on time is increased by the additioll of up to 0 . 010 weight g6 of boron to the alloy.
~igher contents will lead to reduced hot formability by the formation of low-meLting phases on the grain boundaries Contents of lower than 0 . 001 weight 9~ have proved to be inef fective .
Nickel ~Ni ):
The addition of nickel not only favo~lrably influences the oxidation resistance of the alloy, in particular with a simultaneous presence of chromium by the nickel-chromium spinel formation, but also the cal~bonisation resistance.
Nickel contents of at least 6~ '~ are not mandatorily required for this reason, but because only from these nickel contents onwards a sufficient quantity of chromium nitrides will be discarded which are absolutely required for the creep strength depending on time.
Yttrium (Y), cerium ~Ce), lanthanum (La), zirconiunl (2r), hafnium (~f) and tanta~um (Ta):
All these elements are effective in the improvement of the t formability of the alloy.
Eor this reason it is necessary thc~t at least one of the aforementiolled alloy elements must be present when the alloy is subjected to extrer~e }lOt forming operations. On the other hand, contents of over 0 . 50 weight ~ of one or several of t~lese alloy elen ents have proved to be more detrimental to the hot formability.
It ~as furt~ler seen that yttrium, cerium, lant~lanum, zirconium, hafrlium and tantalum, alone or in combination, lead to a considerable improvement of the cycli.c oxidation resistance of the alloy.
The nickel-based alloys 1 to 6 are explaineà below in closer detail in comparison with the known standard alloys 8 to 11.
The actual analyses of the alloys 1 to 11 are shown in table 1.
Fig. 1 sho~s the creep strength depending on time of the alloys ] to 6 il~ accordance with the invention in comparison with the standard alloys 8 to 11 at a permanent temperature of 1, 000C which is typical for a later use .
The stress is shown herein on the ordinate in form of the tension in N/rt~rr,2 to which the sample is subjected over the logarithmized endurance time in hours on the abscisse.
The two spread bands for the alloys 1 to 6 and 8 to 11 contain the breaking pOillts of the individual alloys. The considerably better creep strength depending on time of the alloys 1 to 6 in accordance with t~le invention over the standard alloys 8 to 11 can be recognized by the shift of the spread band curve for the alloys 1 to 6 towards higher tensions. It can be seen that with the alloys 1 to 6 in accordance with the invention it is possible to achieve approx. 2 . 5 times higher creep strengths depending on time as compared ~lith standard alloys 8 to 11.
Fig 2 descr}bes the thermal endurance of the alloys 1 to 6 in comparison with the alloys 8 to 11.
T~le tensile strength is applied here in N/mm2 on the ordinate against the testing temperature i~l ~C on the abscisse .
8 21~86g42 The alloys 1 to 6 in accordance with the invention are provided in the spread band application over the entire temperature range of room temperature up to 1, 200C with the considerably higher thermal endurances as compared ~lith the standard alloys a to 11.
The results of the oxidation examinations show that by the alloying of nitrogen no deterioration of the o%idation resistance occurs as compared with nitrogen-free standard alloys. On the contrary, the standard alloys and the alloys in accordance with the invention are within the spread band for measured value fluctuations for 750C, 1,000C and 1, 200C .
ig. 3 describes in this respect the cyclic oxidation resistance of the alloys 1 to 6 i,n accordance with the invention in comparison Wit}l the standard alloys a to 11 for the testing temperatures of 750, l,000C and 1,200C.
T~le fi gure shows the change in mass in g/m2h standardized for the examination time and the surface of the sample. The examination occurred in the air, with a cycle period of 24 hours at a dwell time at testing temperature of 16 hours with 2 hours heating time and 6 hours cooling time.
2186~2 _ 9 _ _ O
~o ~ r- o _ o 3 r o I ~ I I I I I o o ,~
o ~
,~ o o ~
~ ~ o ~
~ .
, o , , , ~ t o o o o o o o o o o o o o o o o o o , , I
o C~ o o o o , o ô o C~
o - o o o o . o cO O ~ O O r~ _ --I
oo o o o o o o o o o o o o o o o o o o o o o o o o o -L_, o o o o o o , o o o o o o o o o o _ ~
o o o o o o o o o U'~ o o o o o o o o o O O o~
o o o o o o o o o o . . . _ ~_U~ o o _ ~ o o O ~ r.
o o o o o o o o o ~
~,o o o o o o o o o o < ~ C ~ C <
Claims (3)
1. A highly heat and oxidation-resistant hot- and cold-formable nickel-based alloy with a massive nitrogen content, for the production of objects which must be resistant against oxidation and carbonisation at temperatures in the range of 750 to 1,200°C, even under cyclic exposures, consisting (in mass %) of 0.001 to 0.15 % carbon 0.10 to 3.0 % silicon max. 0.5 % manganese max. 0.015 % phosphorus max. 0.005 % sulphur 28 to 33 % chromium max. 2.0 % iron max. 0.3 % aluminium 0.25 to 1.2 % nitrogen 0.001 to 0.01 % boron 0.01 to 0.5 % yttrium, cerium, lanthanum, zirconium, hafnium and tantalum alone or in combination, the remainder being constituted of nickel and the usual admixtures from the smelting process, with the nickel colltent being at least 64.0 %.
2. A nickel-based alloy as claimed in claim 1 with 0.35 to 0.8 % nitrogen.
3. An application of a nickel-based alloy as claimed in one of the claims 1 or 2, as material for stationary or flying gas turbines, furnance components such as supporting frames for burning kilns, conveyor rails and conveyor belts, heat treatment plants, heat conductors and die cast parts.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE4411228A DE4411228C2 (en) | 1994-03-31 | 1994-03-31 | High-temperature resistant nickel-based alloy and use of the same |
| DEP4411228.9 | 1994-03-31 | ||
| PCT/EP1995/000762 WO1995027087A1 (en) | 1994-03-31 | 1995-03-02 | Highly heat-resistant nickel-based alloy and its use |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2186842A1 true CA2186842A1 (en) | 1995-10-12 |
Family
ID=6514337
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002186842A Abandoned CA2186842A1 (en) | 1994-03-31 | 1995-03-02 | Highly heat-resistant nickel-based alloy and its use |
Country Status (11)
| Country | Link |
|---|---|
| EP (1) | EP0753079A1 (en) |
| JP (1) | JPH10500174A (en) |
| KR (1) | KR970702380A (en) |
| CA (1) | CA2186842A1 (en) |
| CZ (1) | CZ282856B6 (en) |
| DE (1) | DE4411228C2 (en) |
| FI (1) | FI963898A0 (en) |
| MX (1) | MX9604345A (en) |
| RU (1) | RU2113530C1 (en) |
| WO (1) | WO1995027087A1 (en) |
| ZA (1) | ZA952134B (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5997809A (en) * | 1998-12-08 | 1999-12-07 | Inco Alloys International, Inc. | Alloys for high temperature service in aggressive environments |
| US20020005233A1 (en) * | 1998-12-23 | 2002-01-17 | John J. Schirra | Die cast nickel base superalloy articles |
| AT408665B (en) * | 2000-09-14 | 2002-02-25 | Boehler Edelstahl Gmbh & Co Kg | NICKEL BASE ALLOY FOR HIGH TEMPERATURE TECHNOLOGY |
| JP3952861B2 (en) * | 2001-06-19 | 2007-08-01 | 住友金属工業株式会社 | Metal material with metal dusting resistance |
| EP2248923A1 (en) * | 2009-04-27 | 2010-11-10 | Siemens Aktiengesellschaft | Nickel base y/ý superalloy with multiple reactive elements and use of said superalloy in complex material systems |
| RU2515794C1 (en) * | 2013-01-15 | 2014-05-20 | Открытое акционерное общество "Государственный научный центр Научно-исследовательский институт атомных реакторов" | Nickel-based alloy |
| US9719420B2 (en) * | 2014-06-02 | 2017-08-01 | General Electric Company | Gas turbine component and process for producing gas turbine component |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1024719B (en) * | 1951-04-16 | 1958-02-20 | Carpenter Steel Company | Hot-formable alloys |
| JPS5631345B2 (en) * | 1972-01-27 | 1981-07-21 | ||
| US4626408A (en) * | 1984-09-20 | 1986-12-02 | Nippon Yakin Kogyo Kabushiki Kaisha | Ni-based alloy excellent in intergranular corrosion resistance, stress corrosion cracking resistance and hot workability |
| US4877435A (en) * | 1989-02-08 | 1989-10-31 | Inco Alloys International, Inc. | Mechanically alloyed nickel-cobalt-chromium-iron composition of matter and glass fiber method and apparatus for using same |
| JPH051344A (en) * | 1991-02-05 | 1993-01-08 | Sumitomo Metal Ind Ltd | Heat resisting steel for ethylene cracking furnace tube excellent in coking resistance |
| DE4130139C1 (en) * | 1991-09-11 | 1992-08-06 | Krupp-Vdm Ag, 5980 Werdohl, De | |
| DE59205180D1 (en) * | 1992-05-11 | 1996-03-07 | New Sulzer Diesel Ag | Nozzle head for a fuel injector |
-
1994
- 1994-03-31 DE DE4411228A patent/DE4411228C2/en not_active Expired - Fee Related
-
1995
- 1995-03-02 RU RU96120215A patent/RU2113530C1/en not_active IP Right Cessation
- 1995-03-02 EP EP95911281A patent/EP0753079A1/en not_active Withdrawn
- 1995-03-02 MX MX9604345A patent/MX9604345A/en unknown
- 1995-03-02 CZ CZ962838A patent/CZ282856B6/en not_active IP Right Cessation
- 1995-03-02 WO PCT/EP1995/000762 patent/WO1995027087A1/en not_active Application Discontinuation
- 1995-03-02 CA CA002186842A patent/CA2186842A1/en not_active Abandoned
- 1995-03-02 JP JP7525368A patent/JPH10500174A/en active Pending
- 1995-03-02 KR KR1019960705329A patent/KR970702380A/en not_active Application Discontinuation
- 1995-03-15 ZA ZA952134A patent/ZA952134B/en unknown
-
1996
- 1996-09-27 FI FI963898A patent/FI963898A0/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| DE4411228A1 (en) | 1995-10-05 |
| FI963898A (en) | 1996-09-27 |
| MX9604345A (en) | 1997-06-28 |
| EP0753079A1 (en) | 1997-01-15 |
| DE4411228C2 (en) | 1996-02-01 |
| RU2113530C1 (en) | 1998-06-20 |
| ZA952134B (en) | 1995-12-18 |
| FI963898A0 (en) | 1996-09-27 |
| CZ283896A3 (en) | 1997-01-15 |
| WO1995027087A1 (en) | 1995-10-12 |
| CZ282856B6 (en) | 1997-11-12 |
| JPH10500174A (en) | 1998-01-06 |
| KR970702380A (en) | 1997-05-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| RU2605022C1 (en) | Nickel chrome alloy with good machinability, creep limit properties and corrosion resistance | |
| EP0384433B1 (en) | Ferritic heat resisting steel having superior high-temperature strength | |
| US5019332A (en) | Heat, corrosion, and wear resistant steel alloy | |
| EP0232061B1 (en) | High-strength steel for valve springs process for producing the steel, and valve springs made of the same | |
| CN108642373A (en) | A kind of high-temperature oxidation resistant austenitic heat-resistance steel and its preparation process | |
| JPH09296258A (en) | Heat resistant steel and rotor shaft for steam turbine | |
| KR101013843B1 (en) | High Strength and High Oxidation Resist Hi Silicon Ferritic CGI Cast Iron | |
| CA2179214C (en) | Forgeable nickel alloy | |
| CA2186842A1 (en) | Highly heat-resistant nickel-based alloy and its use | |
| US4631169A (en) | Alloys for exhaust valves | |
| EP0124348B1 (en) | Heat resisting steels | |
| CN109680206A (en) | A kind of fire resistant iron chromium aluminium alloy and preparation method thereof | |
| EP1197571A1 (en) | Steel product for oil well having high strength and being excellent in resistance to sulfide stress cracking | |
| US5997809A (en) | Alloys for high temperature service in aggressive environments | |
| CN109594007B (en) | Vermicular graphite cast iron and preparation process and application thereof | |
| CA1043591A (en) | Precipitation hardenable stainless steel | |
| CN1043253C (en) | Al-Mn-Si-N series austenitic stainless acid-resisting steel | |
| MXPA96004345A (en) | Alloy based on highly normally resistant nickel and its u | |
| CN109355585A (en) | A kind of superelevation nitrogen martensite heat resisting cast steel and preparation method thereof | |
| EP0359085A1 (en) | Heat-resistant cast steels | |
| JPH0776721A (en) | Heat treatment of heat resisting cast alloy | |
| WO2004031419A1 (en) | Graphite and nitrogen-free cast alloys | |
| US3431100A (en) | Austenitic steel suitable for exhaust valves subject to great stresses | |
| SU992608A1 (en) | Malleable cast iron | |
| SU1678889A1 (en) | Cast iron |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EEER | Examination request | ||
| FZDE | Dead |