CA2503326C - Heat treatment of alloys having elements for improving grain boundary strength - Google Patents
Heat treatment of alloys having elements for improving grain boundary strength Download PDFInfo
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- CA2503326C CA2503326C CA2503326A CA2503326A CA2503326C CA 2503326 C CA2503326 C CA 2503326C CA 2503326 A CA2503326 A CA 2503326A CA 2503326 A CA2503326 A CA 2503326A CA 2503326 C CA2503326 C CA 2503326C
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
Abstract
The invention relates to heat treatment of cast alloys, such as superalloys, which have at least one addition, so as to improve grain boundary strength. Typically after casting, components often reveal low or no transverse grain boundary strength so that cracks can appear and decrease the yield rate. The invention relates to providing improved grain boundary strength to significantly improve transverse stress rupture strength and ductility of directionally solidified columnar grain castings. The heat treatment involves at least one addition, such as boron, to improve the grain boundary strength.
Description
Heat treatment of alloys having elements for improving grain boundary strength FIELD OF THE INVENTION
The present invention relates to a heat treatment of alloys, especially nickel base superalloy and, more particularly, to castings having a columnar grain microstructure.
BACKGROUND OF THE INVENTION
US-PS 4 597 809 describes single crystal castings made from a nickel base superalloy having a matrix with a composition consisting essentially of, in weight %, of 9.5% to 14% Cr, 7% to 11% Co, 1% to 2.5% Mo, 3% to 6% W, 1% to 4% Ta, 3% to 4% Al, 3% to 5% Ti, 6.5% to 8% Al + Ti, 0% to 1% Nb, and balance essentially nickel with the matrix containing about 0.4 to about 1.5 volume of a phase based an tantalum carbide as a result of the inclusion in the alloy of about 0.05% to about 0.15% C and extra Ta in an amount equal to 1 to 17 times the C content.
Single crystal castings produced from the aforementioned nickel base superalloy exhibit inadequate transverse grain boundary strength. The present inventors attempted to pro-duce directionally solidified (DS) columnar grain castings of the nickel base superalloy. However, the directionally solidified (DS) columnar grain castings produced were un-acceptable as DS castings as a result of the castings exhi-biting essentially no transverse grain boundary strength and no ductility when tested at a temperature of 750 degrees C
(1382 degrees F) and stress of 660 MPa (95.7 Ksi). The transverse grain boundary strength and ductility were so deficient as to render DS columnar grain castings produced from the aforementioned nickel base superalloy unsuitable for use as turbine blades of gas turbine engines.
WO 99/67435 discloses nickel base superalloy castings having boron added to improve transverse stress rupture strength and ductility of DS castings. The castings are heat treated at 1250 C for 4h so that a fully solution of the secondary phase (y'-phase) is performed. Due to the occurrence of grain boundary cracks after the fully solution heat treatment the producibility is so deficient as to render DS
columnar grain castings produced from the aforementioned nickel base superalloy unsuitable for use as turbine blades of gas turbine engines.
An object of the present invention is to provide a heat treatment of alloys, especially of as-cast alloys, e.g. DS
columnar grain castings based on the aforementioned single crystal nickel base superalloy, having substantially improved transverse stress rupture strength and ductility as well as producibility to an extent that the DS castings are acceptable for use as high temperature applications such as turbine blades of a gas turbine engine.
SUMMARY OF THE INVENTION
The present invention involves a heat treatment of cast alloys, such as superalloys, having at least one addition, which improves grain boundary strength such as boron in the nickel base superalloy described here above in a manner discovered to significantly improve transverse stress rupture strength and ductility of directionally solidified (DS) columnar grain castings produced with a heat treatment, which solves a secondary phase only partly, e.g. no fully solution heat treatment is performed.
Boron is often added to superalloy compositions in an effective amount to substantially improve transverse stress rupture strength and ductility of directionally solidified columnar grain castings produced from the boron-modified superalloy. The boron concentration preferably is controlled in the range of about 0.003% to about 0.0175% by weight of the superalloy composition to this end.
In conjunction with addition of boron to the superalloy composition, the carbon concentration preferably is controlled in the range of about 0.05% to about 0.11% by weight of the superalloy composition.
A preferred nickel base superalloy in accordance with an embodiment of the present invention consists essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.50% to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.80% to 5.20% Ta, about 3.40% to 3.80% Al, about 3.9%
to 4.25% Ti, about 0.05% to 0.11% C, about 0.003% to 0.0175%
B, and balance essentially Ni. The boron modified nickel base superalloy can be cast as DS columnar grain castings pursuant to conventional DS casting techniques such as the well known Bridgman mould withdrawal technique.
DS castings produced in this manner typically have a plura-lity of columnar grains extending in the direction of the principal stress axis of the casting with the <001> crystal axis generally parallel to the principal stress axis. DS
columnar grain castings pursuant to the present invention preferably exhibit a stress rupture life of at least about 100 hours and elongation of at least about 2.5% when tested at a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi) and will find use as turbine blades, vanes, outer air seals and other components of a industrial and aero gas turbine engines.
3a One aspect of the invention relates to a method of heat treating a cast nickel or cobalt based superalloy having at least one addition selected from the group of Boron and Carbon to improve grain boundary strength, wherein the superalloy has a secondary phase after casting, which can be completely dissolved in a matrix of the superalloy at a complete dissolution temperature for a complete dissolution treatment, wherein (i) a temperature of the heat treatment is smaller than the complete dissolution temperature and a duration which results in the not solubilized amount of the secondary phase in the matrix being smaller than 90, 70, 50 or 30 vol%, or (ii) a temperature of the heat treatment is the complete dissolution temperature and a duration which results in the not solubilized amount of the secondary phase in the matrix being smaller than 90, 70, 50 or 30 vol%.
The above objects and advantages of the present invention will become more readily apparent from the following detailed description taken with the following drawings.
The present invention relates to a heat treatment of alloys, especially nickel base superalloy and, more particularly, to castings having a columnar grain microstructure.
BACKGROUND OF THE INVENTION
US-PS 4 597 809 describes single crystal castings made from a nickel base superalloy having a matrix with a composition consisting essentially of, in weight %, of 9.5% to 14% Cr, 7% to 11% Co, 1% to 2.5% Mo, 3% to 6% W, 1% to 4% Ta, 3% to 4% Al, 3% to 5% Ti, 6.5% to 8% Al + Ti, 0% to 1% Nb, and balance essentially nickel with the matrix containing about 0.4 to about 1.5 volume of a phase based an tantalum carbide as a result of the inclusion in the alloy of about 0.05% to about 0.15% C and extra Ta in an amount equal to 1 to 17 times the C content.
Single crystal castings produced from the aforementioned nickel base superalloy exhibit inadequate transverse grain boundary strength. The present inventors attempted to pro-duce directionally solidified (DS) columnar grain castings of the nickel base superalloy. However, the directionally solidified (DS) columnar grain castings produced were un-acceptable as DS castings as a result of the castings exhi-biting essentially no transverse grain boundary strength and no ductility when tested at a temperature of 750 degrees C
(1382 degrees F) and stress of 660 MPa (95.7 Ksi). The transverse grain boundary strength and ductility were so deficient as to render DS columnar grain castings produced from the aforementioned nickel base superalloy unsuitable for use as turbine blades of gas turbine engines.
WO 99/67435 discloses nickel base superalloy castings having boron added to improve transverse stress rupture strength and ductility of DS castings. The castings are heat treated at 1250 C for 4h so that a fully solution of the secondary phase (y'-phase) is performed. Due to the occurrence of grain boundary cracks after the fully solution heat treatment the producibility is so deficient as to render DS
columnar grain castings produced from the aforementioned nickel base superalloy unsuitable for use as turbine blades of gas turbine engines.
An object of the present invention is to provide a heat treatment of alloys, especially of as-cast alloys, e.g. DS
columnar grain castings based on the aforementioned single crystal nickel base superalloy, having substantially improved transverse stress rupture strength and ductility as well as producibility to an extent that the DS castings are acceptable for use as high temperature applications such as turbine blades of a gas turbine engine.
SUMMARY OF THE INVENTION
The present invention involves a heat treatment of cast alloys, such as superalloys, having at least one addition, which improves grain boundary strength such as boron in the nickel base superalloy described here above in a manner discovered to significantly improve transverse stress rupture strength and ductility of directionally solidified (DS) columnar grain castings produced with a heat treatment, which solves a secondary phase only partly, e.g. no fully solution heat treatment is performed.
Boron is often added to superalloy compositions in an effective amount to substantially improve transverse stress rupture strength and ductility of directionally solidified columnar grain castings produced from the boron-modified superalloy. The boron concentration preferably is controlled in the range of about 0.003% to about 0.0175% by weight of the superalloy composition to this end.
In conjunction with addition of boron to the superalloy composition, the carbon concentration preferably is controlled in the range of about 0.05% to about 0.11% by weight of the superalloy composition.
A preferred nickel base superalloy in accordance with an embodiment of the present invention consists essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.50% to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.80% to 5.20% Ta, about 3.40% to 3.80% Al, about 3.9%
to 4.25% Ti, about 0.05% to 0.11% C, about 0.003% to 0.0175%
B, and balance essentially Ni. The boron modified nickel base superalloy can be cast as DS columnar grain castings pursuant to conventional DS casting techniques such as the well known Bridgman mould withdrawal technique.
DS castings produced in this manner typically have a plura-lity of columnar grains extending in the direction of the principal stress axis of the casting with the <001> crystal axis generally parallel to the principal stress axis. DS
columnar grain castings pursuant to the present invention preferably exhibit a stress rupture life of at least about 100 hours and elongation of at least about 2.5% when tested at a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi) and will find use as turbine blades, vanes, outer air seals and other components of a industrial and aero gas turbine engines.
3a One aspect of the invention relates to a method of heat treating a cast nickel or cobalt based superalloy having at least one addition selected from the group of Boron and Carbon to improve grain boundary strength, wherein the superalloy has a secondary phase after casting, which can be completely dissolved in a matrix of the superalloy at a complete dissolution temperature for a complete dissolution treatment, wherein (i) a temperature of the heat treatment is smaller than the complete dissolution temperature and a duration which results in the not solubilized amount of the secondary phase in the matrix being smaller than 90, 70, 50 or 30 vol%, or (ii) a temperature of the heat treatment is the complete dissolution temperature and a duration which results in the not solubilized amount of the secondary phase in the matrix being smaller than 90, 70, 50 or 30 vol%.
The above objects and advantages of the present invention will become more readily apparent from the following detailed description taken with the following drawings.
DETAILED DESCRIPTION OF THE INVENTION
Exemplarily as alloy a nickel base superalloy is chosen which consists essentially of, in weight %, of about 9.5% to 14%
Cr, about 7% to 11% Co, about 1% to 2.5% Mo, about 3% to 6%
W, about 1% to 6% Ta, about 3$ to 4% Al, about 3% to 5% Ti, about 0% to 1% Nb, and balance essentially Ni and B present in an amount effective to substantially improve transverse stress rupture strength of a DS casting as compared to a similar casting without boron present.
The inclusion of boron, as an addition, which improves the grain boundary strength in the alloy, is chosen in an amount discovered effective to provide substantial transverse stress rupture strength and ductility of a DS columnar grain casting produced from the alloy as compared to a similar casting without boron present.
Preferably, the nickel base superalloy is modified by the inclusion of boron B in the range of about 0.003% to about 0.0175%, preferably 0.010% to 0.015%, by weight of the superalloy composition to this end.
In conjunction with addition of boron to the superalloy composition, the carbon C concentration is controlled in a preferred range of about 0.05% to about 0.11% by_ weight of the superalloy composition. Also Silicon Si, Zirconium Zr and Hafnium Hf can be used as additon.
Furthermore all combinations of B, C, Si, Zr, Hf are possible.
The transverse stress-rupture strength and ductility as well as the producibility of DS castings produced from nickel base superalloy with the modified heat treatment are provided to an extent that the castings are rendered acceptable for use as turbine blades and other components of gas turbine engines.
A-particularly preferred boron-modified nickel base superalloy casting composition consists essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.5% to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.80%
to 5.20% Ta, about 3.40 to 3.80% Al, about 3.9% to 4.25% Ti, about 0.05% to 0.11% C, about 0.003% to 0.0175% B, and 5 balance essentially Ni and castable to provide a DS columnar grain microstructure.
The DS microstructure of the columnar grain casting typically includes about 0.4 to about 1.5 volume % of a phase based an tantalum carbide.
Although not wishing to be bound by any theory, it is thought that boron and carbon tend to migrate to the grain boundaries in the DS microstructure to add strength and ductility to the grain boundaries at high service temperatures, for example 816 degrees C (1500 degrees F) typical of gas turbine engine blades. DS columnar grain castings produced from the above boron modified nickel base superalloy typically have the <001> crystal axis parallel to the principal stress axis of the casting and exhibit a stress rupture life of at least about 100 hours and elongation of at least about 2.5 % when tested at a temperature of 750 degrees C (1382 degrees F ) and stress of 660 MPa (95.7 Ksi) applied perpendicular to the <001> crystal axis of the casting.
For example, the following DS casting tests were conducted and are offered to further illustrate, but not limit, the present invention.
A heat #1 having a nickel base superalloy composition in accordance with the aforementioned U.S. Patent 4 597 809 and heats #lA and #2 and #3 of boron modified nickel base superalloy were prepared with the following compositions, in weight percentages, set forth in Table I:
Exemplarily as alloy a nickel base superalloy is chosen which consists essentially of, in weight %, of about 9.5% to 14%
Cr, about 7% to 11% Co, about 1% to 2.5% Mo, about 3% to 6%
W, about 1% to 6% Ta, about 3$ to 4% Al, about 3% to 5% Ti, about 0% to 1% Nb, and balance essentially Ni and B present in an amount effective to substantially improve transverse stress rupture strength of a DS casting as compared to a similar casting without boron present.
The inclusion of boron, as an addition, which improves the grain boundary strength in the alloy, is chosen in an amount discovered effective to provide substantial transverse stress rupture strength and ductility of a DS columnar grain casting produced from the alloy as compared to a similar casting without boron present.
Preferably, the nickel base superalloy is modified by the inclusion of boron B in the range of about 0.003% to about 0.0175%, preferably 0.010% to 0.015%, by weight of the superalloy composition to this end.
In conjunction with addition of boron to the superalloy composition, the carbon C concentration is controlled in a preferred range of about 0.05% to about 0.11% by_ weight of the superalloy composition. Also Silicon Si, Zirconium Zr and Hafnium Hf can be used as additon.
Furthermore all combinations of B, C, Si, Zr, Hf are possible.
The transverse stress-rupture strength and ductility as well as the producibility of DS castings produced from nickel base superalloy with the modified heat treatment are provided to an extent that the castings are rendered acceptable for use as turbine blades and other components of gas turbine engines.
A-particularly preferred boron-modified nickel base superalloy casting composition consists essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.5% to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.80%
to 5.20% Ta, about 3.40 to 3.80% Al, about 3.9% to 4.25% Ti, about 0.05% to 0.11% C, about 0.003% to 0.0175% B, and 5 balance essentially Ni and castable to provide a DS columnar grain microstructure.
The DS microstructure of the columnar grain casting typically includes about 0.4 to about 1.5 volume % of a phase based an tantalum carbide.
Although not wishing to be bound by any theory, it is thought that boron and carbon tend to migrate to the grain boundaries in the DS microstructure to add strength and ductility to the grain boundaries at high service temperatures, for example 816 degrees C (1500 degrees F) typical of gas turbine engine blades. DS columnar grain castings produced from the above boron modified nickel base superalloy typically have the <001> crystal axis parallel to the principal stress axis of the casting and exhibit a stress rupture life of at least about 100 hours and elongation of at least about 2.5 % when tested at a temperature of 750 degrees C (1382 degrees F ) and stress of 660 MPa (95.7 Ksi) applied perpendicular to the <001> crystal axis of the casting.
For example, the following DS casting tests were conducted and are offered to further illustrate, but not limit, the present invention.
A heat #1 having a nickel base superalloy composition in accordance with the aforementioned U.S. Patent 4 597 809 and heats #lA and #2 and #3 of boron modified nickel base superalloy were prepared with the following compositions, in weight percentages, set forth in Table I:
TABLE I
Heat Cr Co Mo W Ta Al Ti C B Ni #1 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.07 0.001 balance 441A 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.08 0.010 balance #2 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.09 0.011 balance #3 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.08 0.014 balance Each heat was cast to form DS columnar grain non-cored cas-tings having a rectangular shape for transverse stress ruptu-re testing pursuant to ASTM E-139 testing procedure.
The DS castings were produced e.g. using the conventional Bridgman mould withdrawal directional solidification technique.
For example, each heat was melted in a crucible of a conventional casting furnace under a vacuum of 1 micron and oupcnccated to 1427 degrees C (2600 degrees F). The superheated melt was poured into an investment casting mould having a face coat comprising zircon backed by additional slurry/stucco layers comprising zircon/alumina. The mould was preheated to 1482 degrees C (2700 degrees F) and mounted an a chill plate to effect unidirectional heat removal from the molten alloy in the mould. The melt-filled mould an the chill plate was withdrawn from the furnace into a solidification chamber of the casting furnace at a vacuum of 1 micron at a withdrawal rate of 6-16 inches per hour.
The DS columnar grain castings were cooled to room temperature under vacuum in the chamber, removed from the mould in conventional manner using a mechanical knock-out procedure, heat treated at a temperature and for a duration in such way, that the solution of a secondary phase in the matrix is only partly performed.
The nickel based superalloy has as a secondary phase the y`-phase.
6a For a specimen (e.g. nickel based superalloy) with the composition consisting essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.5%
to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.80%
to 5.20% Ta, about 3.40 to 3.80% Al, about 3.9% to 4.25% Ti, about 0.05%
to 0.11 % C, about 0.003% to 0.0175% B, and balance essentially Ni, the inventive heat treatment is performed after casting at 1213 C for at least 1 h, which is not the solution temperature of a secondary phase (e.g. y' phase) for this alloy. Also the temperature of 1250 C (called fully solution or complete dissolution temperature), which is normally used for a fully solution or complete dissolution treatment, can be used but only as long as the secondary phase is not completely solved in the matrix. The not solubilized amount of the secondary phase in the matrix is smaller than 90, 70, 50 or 30 vol% according to the geometry and producibility after the heat treatment, because grain boundary cracks are avoided, in order to increase the yield rate of specimens and desired mechanical properties of the specimen.
Heat Cr Co Mo W Ta Al Ti C B Ni #1 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.07 0.001 balance 441A 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.08 0.010 balance #2 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.09 0.011 balance #3 12.1 9.0 1.8 3.7 5.2 3.6 4.0 0.08 0.014 balance Each heat was cast to form DS columnar grain non-cored cas-tings having a rectangular shape for transverse stress ruptu-re testing pursuant to ASTM E-139 testing procedure.
The DS castings were produced e.g. using the conventional Bridgman mould withdrawal directional solidification technique.
For example, each heat was melted in a crucible of a conventional casting furnace under a vacuum of 1 micron and oupcnccated to 1427 degrees C (2600 degrees F). The superheated melt was poured into an investment casting mould having a face coat comprising zircon backed by additional slurry/stucco layers comprising zircon/alumina. The mould was preheated to 1482 degrees C (2700 degrees F) and mounted an a chill plate to effect unidirectional heat removal from the molten alloy in the mould. The melt-filled mould an the chill plate was withdrawn from the furnace into a solidification chamber of the casting furnace at a vacuum of 1 micron at a withdrawal rate of 6-16 inches per hour.
The DS columnar grain castings were cooled to room temperature under vacuum in the chamber, removed from the mould in conventional manner using a mechanical knock-out procedure, heat treated at a temperature and for a duration in such way, that the solution of a secondary phase in the matrix is only partly performed.
The nickel based superalloy has as a secondary phase the y`-phase.
6a For a specimen (e.g. nickel based superalloy) with the composition consisting essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.5%
to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.80%
to 5.20% Ta, about 3.40 to 3.80% Al, about 3.9% to 4.25% Ti, about 0.05%
to 0.11 % C, about 0.003% to 0.0175% B, and balance essentially Ni, the inventive heat treatment is performed after casting at 1213 C for at least 1 h, which is not the solution temperature of a secondary phase (e.g. y' phase) for this alloy. Also the temperature of 1250 C (called fully solution or complete dissolution temperature), which is normally used for a fully solution or complete dissolution treatment, can be used but only as long as the secondary phase is not completely solved in the matrix. The not solubilized amount of the secondary phase in the matrix is smaller than 90, 70, 50 or 30 vol% according to the geometry and producibility after the heat treatment, because grain boundary cracks are avoided, in order to increase the yield rate of specimens and desired mechanical properties of the specimen.
The alloy can have a single crystal structure or only having grains along one direction.
Optionally an ageing heat treatment can be performed for this composition at 1080 C for at least 2h after this solution heat treatment. Optionally followed by a second ageing heat treatment at 870 C for at least 12 h.
Especially the inventive heat treatment is used for hollow specimen, especially blades, vanes, or liners because cracks 10, do appear more often in walls, especially in thin walls, than in massive specimens after the normally used heat treatment after casting.
The inventive heat treatment leads to an increased grain boundary strength during this heat treatment, so that the yield rate (components without cracks) after the heat treatment is increased.
Also the transverse stress rupture of the component as final product is increased during use of the component at working conditions, because grain boundary strength is increased.
The inventive method yields also good results for massive components, e.g. of a gas turbine.
The castings were also analysed for chemistry, and machined to specimen configuration.
Optionally an ageing heat treatment can be performed for this composition at 1080 C for at least 2h after this solution heat treatment. Optionally followed by a second ageing heat treatment at 870 C for at least 12 h.
Especially the inventive heat treatment is used for hollow specimen, especially blades, vanes, or liners because cracks 10, do appear more often in walls, especially in thin walls, than in massive specimens after the normally used heat treatment after casting.
The inventive heat treatment leads to an increased grain boundary strength during this heat treatment, so that the yield rate (components without cracks) after the heat treatment is increased.
Also the transverse stress rupture of the component as final product is increased during use of the component at working conditions, because grain boundary strength is increased.
The inventive method yields also good results for massive components, e.g. of a gas turbine.
The castings were also analysed for chemistry, and machined to specimen configuration.
Stress rupture testing was conducted in air at a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi) applied perpendicular to the <001> crystal axis of the specimens.
The results of stress rupture testing are set forth in TABLE II below where LIFE in hours (HRS) indicates the time to fracture of the specimen, ELONGATION is the specimen elongation to fracture, and RED OF AREA is the reduction of area of the specimens to fracture. The BASELINE data corres-ponds to test data for Heat #1, and the #1A, #2 and #3 data corresponds to test data for Heat #1A, #2 and #3, respectively. The BASELINE data represent an average of two stress rupture test specimens, while the #1A, #2 and #3 data represent a single stress rupture test specimen.
TABLE II
Alloy #of Tests Temperature Stress MPa Life (HRS) Elongation Red of C ( F) (KSI) (%) Area (%) Baseline 2 750 (1382) 660 (95,7) 0 0 0 #2 1 750 (1382) 660 (95,7) 182 2,6 6,3 #3 1 750 (1382) 660 (95,7) 173 3,7 10,7 #1A 1 750 (1382) 660 (95,7) 275 3.1 4.7 It is apparent from TABLE II that the DS columnar grain spe-cimens produced from heat #1 exhibited in effect essentially no (e.g. zero hours stress rupture life) transverse grain boundary strength when tested at.a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi). That is, the specimens failed immediately to provide an essentially zero stress rupture life. Moreover, the elongation and reduc-tion of area data were essentially zero. These stress rupture properties are so deficient as to render the DS columnar grain castings produced from heat #1 unacceptable for use as turbine blades of gas turbine engines.
2uoc~5-+895 In contrast, TABLE II reveals that DS columnar grain speci-mens produced from heat #lA exhibited a stress rupture life of 275 hours, an elongation of 3. 1-0., and a reduction of area of 4.7 and specimens from heat #2 exhibited a stress rupture life of 182 hours, an elongation of 2.6%, and a reduction of area of 6.3% when tested at a temperature of 750 degrees C
(1382 degrees F) and stress of 660 MPa (95.7 Ksi). These stress rupture properties of the invention represent an un-expected and surprising improvement over those of specimens produced from heat #1 and render DS columnar grain castings produced from heats #1A, #2 and #3 more suitable for use as turbine blades and other components of gas turbine engines.
The present invention is effective to provide DS columnar grain castings with substantial transverse stress ruptuure strength and ductility. These properties are achieved without adversely affecting other mechanical properties, such as ten-sile strength, creep strength, fatigue strength, and corro-sion resistance of the DS castings- The present invention is especially useful to provide large DS columnar grain indus-trial gas turbine (IGT) blade castings which have the alloy composition described above to impart substantial transverse stress rupture strength and ductility to the castings and which have a length of about 20 centimeters to about 60 cen-timeters and above, such as about 90 centimeters length, used throughout the stages of the turbine of stationary industrial gas turbine engines. The above described boron-modified nickel base superalloy casting composition can be cast as DS
columnar grain or single crystal components.
The invention has been described in terms of specific embodiments thereof, and it is not intended to be limited thereto.
The results of stress rupture testing are set forth in TABLE II below where LIFE in hours (HRS) indicates the time to fracture of the specimen, ELONGATION is the specimen elongation to fracture, and RED OF AREA is the reduction of area of the specimens to fracture. The BASELINE data corres-ponds to test data for Heat #1, and the #1A, #2 and #3 data corresponds to test data for Heat #1A, #2 and #3, respectively. The BASELINE data represent an average of two stress rupture test specimens, while the #1A, #2 and #3 data represent a single stress rupture test specimen.
TABLE II
Alloy #of Tests Temperature Stress MPa Life (HRS) Elongation Red of C ( F) (KSI) (%) Area (%) Baseline 2 750 (1382) 660 (95,7) 0 0 0 #2 1 750 (1382) 660 (95,7) 182 2,6 6,3 #3 1 750 (1382) 660 (95,7) 173 3,7 10,7 #1A 1 750 (1382) 660 (95,7) 275 3.1 4.7 It is apparent from TABLE II that the DS columnar grain spe-cimens produced from heat #1 exhibited in effect essentially no (e.g. zero hours stress rupture life) transverse grain boundary strength when tested at.a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi). That is, the specimens failed immediately to provide an essentially zero stress rupture life. Moreover, the elongation and reduc-tion of area data were essentially zero. These stress rupture properties are so deficient as to render the DS columnar grain castings produced from heat #1 unacceptable for use as turbine blades of gas turbine engines.
2uoc~5-+895 In contrast, TABLE II reveals that DS columnar grain speci-mens produced from heat #lA exhibited a stress rupture life of 275 hours, an elongation of 3. 1-0., and a reduction of area of 4.7 and specimens from heat #2 exhibited a stress rupture life of 182 hours, an elongation of 2.6%, and a reduction of area of 6.3% when tested at a temperature of 750 degrees C
(1382 degrees F) and stress of 660 MPa (95.7 Ksi). These stress rupture properties of the invention represent an un-expected and surprising improvement over those of specimens produced from heat #1 and render DS columnar grain castings produced from heats #1A, #2 and #3 more suitable for use as turbine blades and other components of gas turbine engines.
The present invention is effective to provide DS columnar grain castings with substantial transverse stress ruptuure strength and ductility. These properties are achieved without adversely affecting other mechanical properties, such as ten-sile strength, creep strength, fatigue strength, and corro-sion resistance of the DS castings- The present invention is especially useful to provide large DS columnar grain indus-trial gas turbine (IGT) blade castings which have the alloy composition described above to impart substantial transverse stress rupture strength and ductility to the castings and which have a length of about 20 centimeters to about 60 cen-timeters and above, such as about 90 centimeters length, used throughout the stages of the turbine of stationary industrial gas turbine engines. The above described boron-modified nickel base superalloy casting composition can be cast as DS
columnar grain or single crystal components.
The invention has been described in terms of specific embodiments thereof, and it is not intended to be limited thereto.
Claims (17)
1. A method of heat treating a cast nickel or cobalt based superalloy having at least one addition selected from the group of Boron and Carbon to improve grain boundary strength, wherein the superalloy has a secondary phase after casting, which can be completely dissolved in a matrix of the superalloy at a complete dissolution temperature for a complete dissolution treatment, wherein (i) a temperature of the heat treatment is smaller than the complete dissolution temperature and a duration which results in the not solubilized amount of the secondary phase in the matrix being smaller than 90, 70, 50 or 30 vol%, or (ii) a temperature of the heat treatment is the complete dissolution temperature and a duration which results in the not solubilized amount of the secondary phase in the matrix being smaller than 90, 70, 50 or 30 vol%.
2. A method of claim 1, wherein at least one ageing treatment is performed after the heat treatment.
3. A method of claim 1, wherein the heat treatment is performed with hollow components.
4. A method of claim 3, wherein the heat treatment is performed with hollow components having a length of at least 200mm.
5. A method of claim 3, wherein the heat treatment is performed with hollow components having a thickness of an outer wall smaller than 8mm.
6. A method of claim 1, wherein the secondary phase is a .gamma.'-phase.
7. A method of claim 1, wherein the superalloy has directionally solidified columnar grains.
8. A method of claim 1, wherein the superalloy has a single crystal structure.
9. A method of claim 1, wherein the heat treatment is performed with a directionally solidified columnar grain nickel base superalloy casting, consisting essentially of, in weight % of about 9.5% to 14% Cr, about 7% to 11 % Co, about 1% to 2.5% Mo, about 3% to 6% W, about 1% to 6% Ta, about 3% to 4% Al, about 3% to 5% Ti, about 0% to 1% Nb, and balance essentially Ni and wherein B is present in the range of about 0.003% to about 0.018% by weight.
10. A method of claim 9, wherein the superalloy after the heat treatment has a stress rupture life of at least about 100 hours and elongation to fracture of at least about 2.5%
when tested at a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi) applied in a direction perpendicular to a <001> crystal axis of said casting.
when tested at a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi) applied in a direction perpendicular to a <001> crystal axis of said casting.
11. A method of claim 1, wherein the heat treatment is performed with a directionally solidified columnar grain nickel base superalloy casting consisting essentially of, in weight %, of about 11.6% to 12.70% Cr, about 8.5% to 9.5% Co, about 1.65% to 2.15% Mo, about 3.5% to 4.10% W, about 4.8% to 5.20% Ta, about 3.4% to 3.80% Al, about 3.9% to 4.25% Ti, about 0.05% to 0.11 % C, about 0.003% to 0. 0175% B, balance essentially Ni and having substantially improved transverse stress rupture strength as compared to a similar casting without boron present.
12. A method of claim 11, wherein the superalloy after the heat treatment has a stress rupture life of at least about 120 hours and elongation of at least about 2.5% when tested at a temperature of 750 degrees C (1382 degrees F) and stress of 660 MPa (95.7 Ksi) applied perpendicular to a <001> crystal axis of said casting.
13. A method of claim 1, wherein the heat treatment is performed with directionally solidified columnar grain nickel base superalloy casting having a nominal composition consisting essentially of, in weight %, of about 12.00% Cr, about 9.00% Co, about 1.85% Mo, about 3.70% W, about 5.10% Ta, about 3.60% Al, about 4.00% Ti, about 0.0125% B, about 0.09% C, balance essentially Ni and having a stress rupture life of at least about 100 hours and elongation to fracture of at least about 2.5% when tested at a temperature of 750 degrees C
(1382 degrees F) and stress of 660 MPa (95.7 Ksi) applied perpendicular to a <001> crystal axis of said casting.
(1382 degrees F) and stress of 660 MPa (95.7 Ksi) applied perpendicular to a <001> crystal axis of said casting.
14. A method of claim 1, wherein the heat treatment is performed after casting.
15. A method of claim 5, wherein the hollow components are chosen of the group consisting of vanes, blades and liners.
16. A method of claim 1, wherein the heat treatment is performed with massive components.
17. A method of claim 1, wherein the heat treatment is performed with an alloy having an addition selected from the group consisting of Zirconium, Silicon, Hafnium.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/EP2002/011856 WO2004038056A1 (en) | 2002-10-23 | 2002-10-23 | Heat treatment of alloys having elements for improving grain boundary strength |
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| CA2503326A1 CA2503326A1 (en) | 2004-05-06 |
| CA2503326C true CA2503326C (en) | 2011-02-08 |
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| CA2503326A Expired - Fee Related CA2503326C (en) | 2002-10-23 | 2002-10-23 | Heat treatment of alloys having elements for improving grain boundary strength |
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|---|---|
| EP (1) | EP1438441B1 (en) |
| JP (1) | JP4812301B2 (en) |
| CN (1) | CN100449031C (en) |
| AU (1) | AU2002337170A1 (en) |
| CA (1) | CA2503326C (en) |
| DE (1) | DE60215035T2 (en) |
| ES (1) | ES2276959T3 (en) |
| WO (1) | WO2004038056A1 (en) |
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| EP1849879A1 (en) * | 2006-04-26 | 2007-10-31 | Siemens Aktiengesellschaft | Cyclic heat treatment process for a superalloy |
| ES2444407T3 (en) * | 2006-09-07 | 2014-02-24 | Alstom Technology Ltd | Procedure for heat treatment of nickel-based super-alloys |
| WO2011047714A1 (en) * | 2009-10-20 | 2011-04-28 | Siemens Aktiengesellschaft | Alloy for directional solidification and component made of stem-shaped crystals |
| EP2769802A1 (en) | 2013-02-22 | 2014-08-27 | Siemens Aktiengesellschaft | Improved welding material with regard to weldability and grain stabilisation, method and component |
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| WO1999067435A1 (en) * | 1998-06-23 | 1999-12-29 | Siemens Aktiengesellschaft | Directionally solidified casting with improved transverse stress rupture strength |
-
2002
- 2002-10-23 EP EP02772392A patent/EP1438441B1/en not_active Expired - Fee Related
- 2002-10-23 ES ES02772392T patent/ES2276959T3/en not_active Expired - Lifetime
- 2002-10-23 CA CA2503326A patent/CA2503326C/en not_active Expired - Fee Related
- 2002-10-23 WO PCT/EP2002/011856 patent/WO2004038056A1/en active IP Right Grant
- 2002-10-23 DE DE60215035T patent/DE60215035T2/en not_active Expired - Lifetime
- 2002-10-23 JP JP2004545738A patent/JP4812301B2/en not_active Expired - Fee Related
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| Publication number | Publication date |
|---|---|
| CN100449031C (en) | 2009-01-07 |
| EP1438441B1 (en) | 2006-09-27 |
| DE60215035D1 (en) | 2006-11-09 |
| CA2503326A1 (en) | 2004-05-06 |
| ES2276959T3 (en) | 2007-07-01 |
| AU2002337170A1 (en) | 2004-05-13 |
| AU2002337170A8 (en) | 2004-05-13 |
| EP1438441A1 (en) | 2004-07-21 |
| JP4812301B2 (en) | 2011-11-09 |
| CN1617944A (en) | 2005-05-18 |
| JP2006503980A (en) | 2006-02-02 |
| DE60215035T2 (en) | 2007-01-11 |
| WO2004038056A1 (en) | 2004-05-06 |
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