EP2272993B1 - Method for producing a forged article from a gamma-titanium-aluminium base alloy - Google Patents
Method for producing a forged article from a gamma-titanium-aluminium base alloy Download PDFInfo
- Publication number
- EP2272993B1 EP2272993B1 EP10450090.5A EP10450090A EP2272993B1 EP 2272993 B1 EP2272993 B1 EP 2272993B1 EP 10450090 A EP10450090 A EP 10450090A EP 2272993 B1 EP2272993 B1 EP 2272993B1
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- European Patent Office
- Prior art keywords
- forging
- die
- temperature
- biscuit
- titanium
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/06—Methods for forging, hammering, or pressing; Special equipment or accessories therefor for performing particular operations
- B21J5/08—Upsetting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J9/00—Forging presses
- B21J9/02—Special design or construction
- B21J9/06—Swaging presses; Upsetting presses
- B21J9/08—Swaging presses; Upsetting presses equipped with devices for heating the work-piece
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K3/00—Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like
- B21K3/04—Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like blades, e.g. for turbines; Upsetting of blade roots
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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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05B—INDEXING SCHEME RELATING TO WIND, SPRING, WEIGHT, INERTIA OR LIKE MOTORS, TO MACHINES OR ENGINES FOR LIQUIDS COVERED BY SUBCLASSES F03B, F03D AND F03G
- F05B2230/00—Manufacture
- F05B2230/20—Manufacture essentially without removing material
- F05B2230/25—Manufacture essentially without removing material by forging
Definitions
- the invention relates to a method for producing a forgings for turbine blades made of a gamma titanium-aluminum base alloy
- Titanium alloy of 6 at.% Or 8 at.% And (alpha + beta) or near alpha structure are known from US Pat EP 1 127 953 known and are used for a production of poppet valves. This involves upsetting a rod material above the beta conversion and finish-forging the valve disc with an alpha structure in a heat.
- Titanium-aluminum base alloys are essentially formed of titanium aluminide intermetallics and have a high melting point, low density, a high specific modulus of elasticity, good oxidation behavior and high specific tensile strength and creep resistance in the temperature range of 600 ° C to 800 ° C, So meet the ever-increasing demands on special materials such as for next-generation components of aircraft engines and internal combustion engines.
- Titanium aluminide materials are not yet optimized with regard to their alloy composition and their production and processing.
- An alloy that has good processability as well as balanced mechanical properties that can be created by suitable heat treatments includes the elements titanium, aluminum, niobium, molybdenum and boron and is therefore referred to in the art as TNM alloy.
- the object of the invention is to improve the difficult and expensive processing of titanium aluminide materials and has the task of creating a method of the type mentioned above for economic production.
- This object is achieved in a method for producing a forging, in particular a turbine blade, from a gamma-titanium-aluminum base alloy, in which a cylindrical or rod-shaped starting or starting material in one or more steps at those points at which the forging to be formed or the turbine blade to be formed has a volume concentration, heated by electric current passage or by induction over the cross section to a temperature higher 1150 ° C and deformed by application of force, in particular upsetting deformed and such a forging blank is created with different cross-sectional areas over its longitudinal extent, which blank in one or more subsequent steps is final deformed, wherein the or the subsequent step (s) for the final deformation of the forging blank each of an at least partially coating the surface with a heat radiation and thereby the devisflä is formed from heating the forging blank to forming temperature, from a heat soak and from a reshaping of the same, in particular in a die, is formed.
- the alloy consists mainly of gamma-titanium-aluminum and alpha 2-titanium-aluminum and has only a possibly small proportion of beta-phase, which phase has ductile properties depending on the temperature.
- beta-phase increases in the material, which justifies an improvement in the ductility of the material.
- upsetting may be done at several points in the sequence.
- a forged blank produced according to the invention can now be finally deformed, with advantage being due to the volume concentrations, a Gesenk spallung with less material flow and / or material use can take place.
- a transport of forging blank or intermediate product from the heating furnace to the deformation plant with the tool or with a die, esp. can cause a critical cooling of the surface portion of the deformed part, in an embodiment of the invention, a method in which or the sequential step (s) of final deformation of the forging blank or intermediate product for turbine blade production from at least partially coating the surface with a heat radiation and thereby the superficial one Temperature decrease-reducing agent, a heating of the forging blank or intermediate product to forming temperature, a heat soak, a transfer and a forming thereof, esp.
- a die is formed (be), advantageously feasible.
- the oxide phase acts as a heat-resistant insulating component, with one or more additive (s) or adhesives having smaller proportions connecting (bonding) and retaining (holding) the oxide grains.
- the liquid component (s) serve to homogenize the phases and to adjust a desired level of liquid for homogeneous application to the surface of the workpiece or part.
- a method which can be carried out without error is advantageous in which the final deformation takes place in a die which has a temperature which is at least 300 ° C. lower than the forging blank or the intermediate product.
- a method according to the invention in which the final deformation takes place in a die having up to 900 ° C, preferably up to 800 ° C, lower temperature than the forging blank or the intermediate intensifies the above advantages, because such a low mold temperature Use of commonly used hot working steels for thermally tempered dies allows for no danger the hard waste of the same must be feared in the operation.
- the method of manufacturing turbine blades e.g. made of a TNM alloy, usable.
- a power source (not shown) is connected to a terminal 2 and a slightly concave shaped flat caliper 3.
- a rod 1 is pressed in a press on the flat saddle 3, wherein between the flat saddle 3 and the terminal 2 electric current flows, which heats the rod in this area by the ohmic resistance.
- a heating of a rod or rod part can also be done by means of an induction coil and alternating current.
- titanium-aluminum base alloys have particularly good compression properties and are not prone to buckling. Furthermore, a rapid, targeted heating of a rod area is possible by a heat technology with electrical current passage or by induction, with a precise adjustment of the forming temperature in the so-called. Deformability window of the alloy can be achieved.
- FIG. 3 and FIG. 4 show a puncture of one end of a rod 1 in a mold 3 to form a desired shaped end portion 11th
- Blanks, as in FIG. 3 and FIG. 4 2, for a turbine blade forging, a rod having a diameter of 30mm ⁇ and a length of 225mm was made of an alloy Ti-43.5Al- (Nb-Mo-B) 5 at%.
- the production length was 192mm with a head diameter of 45mm and a head length of 63mm.
- the heating and compression time was 60 sec., With a heating current of 7740 A and a forming temperature of 1250 ° C had been set.
- Fig. 5 shows in a form compressed blanks.
Description
Die Erfindung betrifft ein Verfahren zur Herstellung eines Schmiedestückes für Turbinenschaufieln aus einer Gamma-Titan-Aluminium-BasislegierungThe invention relates to a method for producing a forgings for turbine blades made of a gamma titanium-aluminum base alloy
Titanlegierung mit 6 At.-% oder 8 At.-% und einem (alpha+beta) oder nahe alpha-Gefüge sind aus der
Titan-Aluminium-Basisiegierungen sind Im Wesentlichen aus intermetallischen Titan-Aluminiden gebildet und weisen einen hohen Schmelzpunkt, geringe Dichte, einen hohen, spezifischen Elastizitätsmodul, gutes Oxidationsverhalten sowie hohe, spezifische Zugfestigkeit sowie Kriechfestigkeit im Temperaturbereich von 600°C bis 800°C auf, erfüllen also die ständig steigenden Anforderungen an Sonderwerkstoffe wie z.B. für Komponenten der nächsten Generation von Flugzeugtriebwerken und Verbrennungsmotoren.Titanium-aluminum base alloys are essentially formed of titanium aluminide intermetallics and have a high melting point, low density, a high specific modulus of elasticity, good oxidation behavior and high specific tensile strength and creep resistance in the temperature range of 600 ° C to 800 ° C, So meet the ever-increasing demands on special materials such as for next-generation components of aircraft engines and internal combustion engines.
Titan-Aluminid-Werkstoffe sind bezüglich ihrer Legierungszusammensetzung sowie ihrer Herstellung und Verarbeitung noch nicht optimiert.Titanium aluminide materials are not yet optimized with regard to their alloy composition and their production and processing.
Eine Legierung, die eine gute Verarbeitbarkeit, sowie ausgewogene, mechanische Eigenschaften aufweist, die durch geeignete Wärmebehandlungen erstellt werden können, weist die Elemente Titan, Aluminium, Niob, Molybdän und Bor auf und wird deshalb in der Fachwelt als TNM-Legierung bezeichnet.An alloy that has good processability as well as balanced mechanical properties that can be created by suitable heat treatments includes the elements titanium, aluminum, niobium, molybdenum and boron and is therefore referred to in the art as TNM alloy.
Auf Grund des intermetallischen Charakters der Titan-Aluminid-Legierungen, ggf, auch der TNM-Werkstoffe, mit anderen Worten: ihres spröden Verhaltens bei ungeeigneten Verformungsbedingungen wegen, ist besonders eine Herstellung von Schmiedestücken wie Turbinenschaufeln kritisch und meist mit hohen Abfallraten verbunden.Due to the intermetallic nature of the titanium aluminide alloys, and possibly also of the TNM materials, in other words their brittle behavior under inappropriate deformation conditions, especially the production of forgings such as turbine blades is critical and usually associated with high waste rates.
Es ist bekannt, eine Schmiedeumformung unter isothermen Bedingungen durchzuführen, was ein besonderes Hochtemperatur-Schmiedegesenk mit Schutzgasatmosphäre erfordert und daher kostenintensiv ist.It is known to forge remoulding under isothermal conditions perform what a special high-temperature forging sink with inert gas atmosphere requires and therefore costly.
Die Erfindung setzt sich zum Ziel, die schwierige und kostenintensive Verarbeitung von Titan-Aluminid-Werkstoffen zu verbessern und hat die Aufgabe, ein Verfahren der eingangs genannten Art zur wirtschaftlichen Herstellung zu schaffen.The object of the invention is to improve the difficult and expensive processing of titanium aluminide materials and has the task of creating a method of the type mentioned above for economic production.
Dieses Ziel wird bei einem Verfahren zur Herstellung eines Schmiedestückes, insbesondere einer Turbinenschaufel, aus einer Gamma-Titan-Aluminium-Basislegierung erreicht, bei welchem ein zylindrisches oder stabförmiges Ausgangs- oder Vormaterial in einem oder mehreren Schritten an jenen Stellen, an welchen das auszuformende Schmiedestück bzw. die auszuformende Turbinenschaufel eine Volumenkonzentration aufweist, durch elektrischen Stromdurchgang oder durch Induktion über den Querschnitt auf eine Temperatur von höher 1150°C erwärmt und durch Kraftbeaufschlagung verformt, insbesondere stauchverformt und derart ein Schmiederohling mit unterschiedlichen Querschnittsflächen über dessen Längserstreckung erstellt wird, welcher Rohling in einem oder mehreren Folgeschritten endverformt wird, wobei der oder die Folgeschritt(e) zur Endverformung des Schmiederohlings jeweils aus einem zumindest teilweisen Beschichten der Oberfläche mit einem die Wärmeabstrahlung und dadurch den oberflächlichen Temperaturabfall mindernden Mittel, aus einem Erwärmen des Schmiedrohlings auf Umformtemperatur, aus einem Durchwärmen und aus einem Umformen desselben, insbesondere in einem Gesenk, gebildet wird(werden).This object is achieved in a method for producing a forging, in particular a turbine blade, from a gamma-titanium-aluminum base alloy, in which a cylindrical or rod-shaped starting or starting material in one or more steps at those points at which the forging to be formed or the turbine blade to be formed has a volume concentration, heated by electric current passage or by induction over the cross section to a temperature higher 1150 ° C and deformed by application of force, in particular upsetting deformed and such a forging blank is created with different cross-sectional areas over its longitudinal extent, which blank in one or more subsequent steps is final deformed, wherein the or the subsequent step (s) for the final deformation of the forging blank each of an at least partially coating the surface with a heat radiation and thereby the oberflä is formed from heating the forging blank to forming temperature, from a heat soak and from a reshaping of the same, in particular in a die, is formed.
Die mit der Erfindung erreichten Vorteile sind im Wesentlichen in einer wirtschaftlichen Vormaterialerstellung für eine Turbinenschaufelfertigung mit in der Längserstreckung unterschiedlichen Querschnittsflächen und in dadurch günstigen Werkstofffließbedingungen bei der Endformung des Schmiedestückes zu sehen. Obwohl Gamma-Titan-Aluminium-Basislegierungen eine hohe spezifische Steifigkeit aufweisen, hat es sich als günstig erwiesen, ein zylindrisches oder stabförmiges Ausgangsmaterial zu verwenden und dieses durch Induktion oder insb. durch direkten Stromdurchgang zwischen Klemm- oder Anschlussbereichen am Stab auf eine Temperatur von höher als 1150°C zu erwärmen. Durch dieses Aufheizen wird trotz Abstrahlung von der Oberfläche eine Verteilung der Temperatur über den Querschnitt gleichmäßig ausgebildet, weil offensichtlich durch eine Stromverdrängung der spezifische Stromfluss und damit die Wärmeentwicklung im Oberflächenbereich vergrößert sind.The advantages achieved with the invention are essentially to be seen in an economic pre-material production for a turbine blade production with different cross-sectional areas in the longitudinal extent and in thus favorable material flow conditions in the final shaping of the forging. Although gamma-titanium-aluminum base alloys have a high specific stiffness, it has proved to be beneficial to use a cylindrical or rod-shaped starting material and to increase it to a higher temperature by induction or in particular by direct passage of current between terminal or terminal areas on the rod to heat as 1150 ° C. By this heating, despite the radiation from the surface, a distribution of the temperature over the Cross section formed uniformly, because obviously by a current displacement of the specific current flow and thus the heat development in the surface area are increased.
Bei Raumtemperatur besteht die Legierung hauptsächlich aus Gamma-Titan-Aluminium und Alpha 2-Titan-Aluminium und weist nur einen ggf. geringen Anteil an Beta-Phase auf, welche Phase je nach Temperatur duktile Eigenschaften hat. Bei einer Erwärmung auf über 1150°C, mit Vorteil auf über 1250°C, vergrößert sich der Anteil an Beta-Phase im Werkstoff, was eine Verbesserung der Verformbarkeit des Werkstoffes begründet.At room temperature, the alloy consists mainly of gamma-titanium-aluminum and alpha 2-titanium-aluminum and has only a possibly small proportion of beta-phase, which phase has ductile properties depending on the temperature. When heated to more than 1150 ° C, with advantage over 1250 ° C, the proportion of beta-phase increases in the material, which justifies an improvement in the ductility of the material.
Mit einem Stauchen, wie oben erwähnt, bei gezielter und homogener Erwärmung über den Querschnitt des Stabes auf hohe Temperatur kann eine gleichmäßige und gezielte Volumenkonzentration und eine gewünschte Feinkorngefügestruktur desselben erreicht werden.With a upsetting, as mentioned above, with targeted and homogeneous heating over the cross-section of the rod to high temperature, a uniform and targeted volume concentration and a desired fine-grain structure of the same can be achieved.
Wird mehr als ein Bereich mit vergrößertem Querschnitt des Stabes für Sonderschaufelformen gewünscht, kann ein Stauchumformen an mehreren Stellen in der Folge vorgenommen werden.If more than one area of enlarged cross-section of the special blade bar is desired, upsetting may be done at several points in the sequence.
Ein nach oben beschriebenen Schritten erfindungsgemäß hergestellter Schmiederohling kann nun nach Aufwärmen, bspw. in einem Schmiedeofen, in einem oder mehreren Folgeschritt(en), insb. in einem Gesenk, endverformt werden, wobei mit Vorteil auf Grund der Volumenkonzentrationen eine Gesenkfüllung bei geringerem Materialfluss und/oder Materialeinsatz erfolgen kann.In a forging furnace, in one or more subsequent step (s), esp. In a die, a forged blank produced according to the invention can now be finally deformed, with advantage being due to the volume concentrations, a Gesenkfüllung with less material flow and / or material use can take place.
Weil nun ein Transport des Schmiederohlings oder Zwischenproduktes vom Wärmeofen zur Verformungsanlage mit dem Werkzeug bzw. mit einem Gesenk, insb. bei zeitaufwändigen Verbringungswegen, eine kritische Abkühlung des Oberflächenbereiches des zu verformenden Teiles bewirken kann, ist in Ausgestaltung der Erfindung ein Verfahren, bei welchem der oder die Folgeschritt(e) zur Endverformung des Schmiederohlings oder des Zwischenproduktes für eine Turbinenschaufelfertigung aus einem zumindest teilweisen Beschichten der Oberfläche mit einem die Wärmeabstrahlung und dadurch den oberflächlichen Temperaturabfall mindernden Mittel, einem Erwärmen des Schmiederohlings oder Zwischenproduktes auf Umformtemperatur, einem Durchwärmen, einem Verbringen und einem Umformen desselben, insb. in einem Gesenk gebildet wird (werden), vorteilhaft durchführbar.Because now a transport of forging blank or intermediate product from the heating furnace to the deformation plant with the tool or with a die, esp. At time-consuming movement paths, can cause a critical cooling of the surface portion of the deformed part, in an embodiment of the invention, a method in which or the sequential step (s) of final deformation of the forging blank or intermediate product for turbine blade production from at least partially coating the surface with a heat radiation and thereby the superficial one Temperature decrease-reducing agent, a heating of the forging blank or intermediate product to forming temperature, a heat soak, a transfer and a forming thereof, esp. In a die is formed (be), advantageously feasible.
Es hat sich gezeigt, dass ein Beschichten der Oberfläche des Schmiederohlings oder Zwischenproduktes mit einem Mittel zur Verminderung der Wärmeabstrahlung schon mit einer Dicke von größer 0.1 mm einen Temperaturverlust der Randzone in der Zeiteinheit deutlich verringern kann und derart eine erforderliche hohe Umformtemperatur des Werkstückes im Oberflächenbereich bei Vermeidung einer Rissbildung bei einer Umformung erhalten bleibt.
Gemäß der Erfindung wirkt die Oxidphase als hitzebeständige Isolierkomponente, wobei ein oder mehrere Additiv(e) bzw. Haftmittel mit geringeren Anteilen die Oxidkörner verbindet (verbinden) und auf dem Substrat hält (halten). Die flüssige(n) Komponente(n) dient (dienen) der Homogenisierung der Phasen und einer Einstellung eines gewünschten Flüssigkeitsgrades zur homogenen Aufbringung auf die Oberfläche des Werkstückes oder Teiles.It has been found that coating the surface of the forging blank or intermediate product with a means for reducing the heat radiation even with a thickness of greater than 0.1 mm can significantly reduce a temperature loss of the edge zone in the unit time and thus a required high forming temperature of the workpiece in the surface area Prevention of cracking during forming remains intact.
According to the invention, the oxide phase acts as a heat-resistant insulating component, with one or more additive (s) or adhesives having smaller proportions connecting (bonding) and retaining (holding) the oxide grains. The liquid component (s) serve to homogenize the phases and to adjust a desired level of liquid for homogeneous application to the surface of the workpiece or part.
Ein Mittel, bei welchem die Hauptkomponente bzw. Oxidphase aus Zirkonoxid mit einem Anteil in Gew.-% von größer 70, bevorzugt von 80 bis 98, insb. von 90 bis 97, gebildet ist, hat sich im Hinblick auf eine wesentliche Verringerung der Wärmeabstrahlung als besonders günstig herausgestellt.An agent in which the main component or oxide phase is formed of zirconium oxide in a proportion in wt .-% of greater than 70, preferably from 80 to 98, esp. From 90 to 97, has been in view of a significant reduction in heat radiation turned out to be particularly favorable.
Vorteilhaft kann weiters bei einer Ausführungsvariante der Erfindung ein fehlerfrei durchführbares Verfahren sein, bei welchem die Endverformung in einem Gesenk erfolgt, welches eine um mindestens 300°C niedrigere Temperatur als der Schmiederohling oder das Zwischenprodukt aufweist. Dadurch werden anlagentechnische Vereinfachungen bei verbesserter Wirtschaftlichkeit erreicht.Advantageously, in another embodiment of the invention, a method which can be carried out without error is advantageous in which the final deformation takes place in a die which has a temperature which is at least 300 ° C. lower than the forging blank or the intermediate product. As a result, plant-technical simplifications are achieved with improved efficiency.
Ein Verfahren nach der Erfindung, bei welchem die Endverformung in einem Gesenk erfolgt, welches eine bis zu 900°C, bevorzugt bis zu 800°C, niedrigere Temperatur als der Schmiederohling oder das Zwischenprodukt hat, intensiviert obige Vorteile, weil eine derart niedrige Werkzeugtemperatur eine Verwendung von gebräuchlichen Warmarbeitsstählen für thermisch vergütete Gesenke zulässt, ohne dass eine Gefahr des Härteabfalles derselben im Betrieb befürchtet werden muss.A method according to the invention, in which the final deformation takes place in a die having up to 900 ° C, preferably up to 800 ° C, lower temperature than the forging blank or the intermediate intensifies the above advantages, because such a low mold temperature Use of commonly used hot working steels for thermally tempered dies allows for no danger the hard waste of the same must be feared in the operation.
Ein Verfahren, bei welchem die Endumformung als Schnellumformung mit einer Verformungsgeschwindigkeit von > 0.3mm/sec, insb. von 0.5 bis 5mm/sec., erfolgt, erbringt sowohl schmiedetechnische Vorteile als auch eine wesentlich verbesserte Mikrostruktur des Schmiedestückes.A process in which the final deformation as a rapid forming with a deformation rate of> 0.3mm / sec, esp. From 0.5 to 5mm / sec., Takes place, provides both forging advantages and a significantly improved microstructure of the forging.
Mit Vorteil ist das Verfahren für eine Herstellung von Turbinenschaufeln, z.B. aus einer TNM-Legierung, verwendbar.Advantageously, the method of manufacturing turbine blades, e.g. made of a TNM alloy, usable.
An Hand von Ausführungsbeispielen, welche jeweils lediglich einen Verfahrensweg darstellen, soll die Erfindung näher erläutert werden.With reference to exemplary embodiments, which each represent only one process path, the invention will be explained in more detail.
Es zeigen schematisch:
- Fig.1
- in Ansicht und
Fig. 2 im axialen Schnitt ein freies Aufstauchen eines Stabendes - Fig. 3
- in Ansicht und
Fig. 4 im axialen Schnitt ein Aufstauchen eines Stabendes in einer Form - Fig. 5
- in einer Form aufgestauchte Endenbereiche von Stäben einer Ti-Al-Basislegierung bzw. Vormaterial für eine Gesenkschmiedung
- Fig. 1 und Fig. 2
- zeigen ein Aufstauchen eines
Stabes 1 bei freier Breitung.
- Fig.1
- in view and
Fig. 2 in the axial section a free upsetting of a rod end - Fig. 3
- in view and
Fig. 4 in axial section an upsetting of a rod end in a mold - Fig. 5
- in a mold upturned end portions of rods of a Ti-Al base alloy or starting material for a drop forging
- Fig. 1 and Fig. 2
- show an upsetting of a
bar 1 with free expansion.
Eine Stromquelle (nicht dargestellt) ist mit einer Klemme 2 und einem leicht konkav geformten Flachsattel 3 verbunden. Für eine Umformung wird ein Stab 1 in einer Presse an den Flachsattel 3 angedrückt, wobei zwischen dem Flachsattel 3 und der Klemme 2 elektrischer Strom fließt, welcher in diesem Bereich durch den Ohm'schen Widerstand den Stab erwärmt.A power source (not shown) is connected to a
Eine Erwärmung eines Stabes oder Stabteiles kann auch mittels einer Induktionsspule und Wechselstrom erfolgen.A heating of a rod or rod part can also be done by means of an induction coil and alternating current.
Durch eine Stauchkraft erfolgt nach einem Aufwärmen eines Stabteiles ein Aufstauchen eines Stabendes, im gegebenen Fall mit freier Breitung.By an upsetting force occurs after warming up of a rod part upsetting a rod end, in the given case with free expansion.
Es hat sich gezeigt, dass Titan-Aluminium-Basislegierungen besonders gute Staucheigenschaften aufweisen und nicht zum Ausknicken neigen. Weiters ist durch eine Wärmetechnologie mit elektrischem Stromdurchgang oder durch Induktion eine rasche, gezielte Durchwärmung eines Stabbereiches möglich, wobei eine genaue Einstellung der Umformtemperatur im sog. Verformbarkeitsfenster der Legierung erreichbar ist.It has been found that titanium-aluminum base alloys have particularly good compression properties and are not prone to buckling. Furthermore, a rapid, targeted heating of a rod area is possible by a heat technology with electrical current passage or by induction, with a precise adjustment of the forming temperature in the so-called. Deformability window of the alloy can be achieved.
Derart kann eine genaue Abmessung eines Schmiederohlings für eine Endformgebung hergestellt werden.Thus, an accurate dimension of a forging blank for final forming can be made.
Rohlinge, wie in
Die Erwärmungs- und Stauchzeit war 60 sec., wobei ein Heizstrom mit 7740 A und eine Umformtemperatur von 1250°C eingestellt worden waren.The heating and compression time was 60 sec., With a heating current of 7740 A and a forming temperature of 1250 ° C had been set.
Claims (6)
- A method of preparing a forged object, particularly a turbine blade, from a gamma-titanium/aluminium basic alloy, in which, in one or more steps, a cylindrical or bar-shaped starting or preliminary material is, at those sites where the object to be forged, or the turbine blade to be forged, respectively, has a volume concentration, heated to a temperature of more than 1150 °C upon dectrical power passage or upon induction throughout the cross-section and deformed, particularly deformed by upsetting, upon imposing force, thus preparing a forging biscuit having different cross-sectional areas along its longitudinal dimension, which biscuit is end-shaped in one or more subsequent steps, wherein the, or each, subsequent step of end-shaping the forging biscuit is formed by at least partially coating the surface with an agent decreasing heat radiation and thus surface temperature drop, heating the forging biscuit to a transformation temperature, through-heating and reshaping the same, in particular within a die.
- The method of claim 1, wherein said agent decreasing surface temperature drop is formed by an oxide phase as the main component and one or more adhesive(s) as additive(s) as well as liquid components.
- The method of any one of claims 1 to 2, wherein said coating agent is formed by zirconium oxide at a content of more than 70, preferably of from 80 to 98, and particularly of from 90 to 97, per cent by weight.
- The method of any one of claims 1 to 3, in which said end shaping is conducted within a die having a temperature of at least 300 °C below that of said forging die.
- The method of any one of claims 1 or 4, in which said end shaping is conducted within a die having a temperature of up to 900 °C, preferably of up to 800 °C, below that of said forging die or said intermediate.
- The method of any one of claims 1 to 5, in which said end shaping is conducted in the form of rapid reshaping at a deformation rate of > 0.3 mm/sec, particularly of from 0.5 to 5 mm/sec.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PL10450090T PL2272993T3 (en) | 2009-06-05 | 2010-05-19 | Method for producing a forged article from a gamma-titanium-aluminium base alloy |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
ATA879/2009A AT508323B1 (en) | 2009-06-05 | 2009-06-05 | METHOD FOR PRODUCING A FORGING PIECE FROM A GAMMA TITANIUM ALUMINUM BASE ALLOY |
Publications (2)
Publication Number | Publication Date |
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EP2272993A1 EP2272993A1 (en) | 2011-01-12 |
EP2272993B1 true EP2272993B1 (en) | 2013-09-18 |
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ID=42711831
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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EP10450090.5A Not-in-force EP2272993B1 (en) | 2009-06-05 | 2010-05-19 | Method for producing a forged article from a gamma-titanium-aluminium base alloy |
Country Status (8)
Country | Link |
---|---|
US (1) | US8828160B2 (en) |
EP (1) | EP2272993B1 (en) |
JP (1) | JP5669451B2 (en) |
AT (1) | AT508323B1 (en) |
CA (1) | CA2706289C (en) |
ES (1) | ES2434016T3 (en) |
IL (1) | IL206181A (en) |
PL (1) | PL2272993T3 (en) |
Families Citing this family (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AT509768B1 (en) | 2010-05-12 | 2012-04-15 | Boehler Schmiedetechnik Gmbh & Co Kg | METHOD FOR PRODUCING A COMPONENT AND COMPONENTS FROM A TITANIUM ALUMINUM BASE ALLOY |
DE102012201082B4 (en) | 2012-01-25 | 2017-01-26 | MTU Aero Engines AG | Method for producing forged components from a TiAl alloy and correspondingly manufactured component |
JP6369753B2 (en) * | 2013-10-01 | 2018-08-08 | 日立金属株式会社 | Hot forging method |
CN103586392B (en) * | 2013-11-15 | 2015-05-27 | 西安航空动力股份有限公司 | Method for manufacturing large titanium alloy fan damping platform blade blank |
CN104308068A (en) * | 2014-08-29 | 2015-01-28 | 孙金福 | Cross-shaped forged piece |
DE102015103422B3 (en) | 2015-03-09 | 2016-07-14 | LEISTRITZ Turbinentechnik GmbH | Process for producing a heavy-duty component of an alpha + gamma titanium aluminide alloy for piston engines and gas turbines, in particular aircraft engines |
DE102015115683A1 (en) * | 2015-09-17 | 2017-03-23 | LEISTRITZ Turbinentechnik GmbH | A method for producing an alpha + gamma titanium aluminide alloy preform for producing a heavy duty component for reciprocating engines and gas turbines, in particular aircraft engines |
DE102017212082A1 (en) * | 2017-07-14 | 2019-01-17 | MTU Aero Engines AG | FORGING AT HIGH TEMPERATURES, IN PARTICULAR OF TITANALUMINIDES |
CN109454403A (en) * | 2017-09-06 | 2019-03-12 | 丹阳蓝思信息技术有限公司 | A kind of titanium alloy rod bar and preparation method thereof |
CN111085644B (en) * | 2020-01-20 | 2021-08-31 | 南京中远海运船舶设备配件有限公司 | Method for improving large-size electric upsetting end surface depression and promoting uniform grain refinement |
CN116967724B (en) * | 2023-09-25 | 2023-12-05 | 陕西长羽航空装备股份有限公司 | Forming method of large-diameter high-cylinder thin-wall forging for manufacturing aeroplane parts |
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US1849185A (en) * | 1927-10-10 | 1932-03-15 | Holding Des Brevets Et Procede | Method of and apparatus for shaping metallic stock |
FR1086289A (en) * | 1952-06-27 | 1955-02-10 | Massey Harris Co Ltd | Method and apparatus for obtaining, using low pressures, high deformations of mechanical parts such as machine shafts |
GB901251A (en) * | 1959-07-08 | 1962-07-18 | Daniel Alfred Cavanagh | Improvements in precision forging methods and apparatus |
JPS6123548A (en) * | 1984-07-11 | 1986-02-01 | Goto Tanko Kk | Forging method of flanged axle |
US5076858A (en) * | 1989-05-22 | 1991-12-31 | General Electric Company | Method of processing titanium aluminum alloys modified by chromium and niobium |
US5304344A (en) * | 1989-06-02 | 1994-04-19 | General Electric Company | Gamma titanium aluminum alloys modified by chromium and tungsten and method of preparation |
JP2728305B2 (en) * | 1989-12-25 | 1998-03-18 | 新日本製鐵株式会社 | Hot working method of intermetallic compound TiA ▲ -based alloy |
JPH0771717B2 (en) * | 1990-03-26 | 1995-08-02 | 本田技研工業株式会社 | Engine valve manufacturing method |
EP0464366B1 (en) * | 1990-07-04 | 1994-11-30 | Asea Brown Boveri Ag | Process for producing a work piece from an alloy based on titanium aluminide containing a doping material |
DE59106047D1 (en) * | 1991-05-13 | 1995-08-24 | Asea Brown Boveri | Process for manufacturing a turbine blade. |
DE4416471C2 (en) * | 1994-05-10 | 1999-05-20 | Langenstein & Schemann Gmbh | Die of an electric upsetting machine for die upsetting |
JPH0824984A (en) * | 1994-07-18 | 1996-01-30 | Fuji Oozx Inc | Electrode of electric forged upsetting machine |
JPH09327746A (en) * | 1996-06-12 | 1997-12-22 | Fuji Oozx Inc | Electrode device for electric upsetting machine |
JPH10156473A (en) * | 1996-11-25 | 1998-06-16 | Nippon Steel Corp | Hot working method of tial base intermetallic compound |
JP4287991B2 (en) * | 2000-02-23 | 2009-07-01 | 三菱重工業株式会社 | TiAl-based alloy, method for producing the same, and moving blade using the same |
JP2001234313A (en) * | 2000-02-23 | 2001-08-31 | Fuji Oozx Inc | Method for manufacturing engine valve mede of titanium alloy |
JP4209092B2 (en) * | 2001-05-28 | 2009-01-14 | 三菱重工業株式会社 | TiAl-based alloy, method for producing the same, and moving blade using the same |
DE102005022506B4 (en) * | 2005-05-11 | 2007-04-12 | Universität Stuttgart | Method for forging a titanium alloy component |
JP2008132527A (en) * | 2006-11-29 | 2008-06-12 | Honda Motor Co Ltd | Upsetting device |
-
2009
- 2009-06-05 AT ATA879/2009A patent/AT508323B1/en not_active IP Right Cessation
-
2010
- 2010-05-19 EP EP10450090.5A patent/EP2272993B1/en not_active Not-in-force
- 2010-05-19 ES ES10450090T patent/ES2434016T3/en active Active
- 2010-05-19 PL PL10450090T patent/PL2272993T3/en unknown
- 2010-05-31 CA CA2706289A patent/CA2706289C/en not_active Expired - Fee Related
- 2010-06-02 JP JP2010138709A patent/JP5669451B2/en not_active Expired - Fee Related
- 2010-06-03 IL IL206181A patent/IL206181A/en not_active IP Right Cessation
- 2010-06-03 US US12/793,410 patent/US8828160B2/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
JP2010280002A (en) | 2010-12-16 |
ES2434016T3 (en) | 2013-12-13 |
PL2272993T3 (en) | 2014-02-28 |
CA2706289A1 (en) | 2010-12-05 |
US8828160B2 (en) | 2014-09-09 |
IL206181A (en) | 2016-02-29 |
AT508323B1 (en) | 2012-04-15 |
EP2272993A1 (en) | 2011-01-12 |
JP5669451B2 (en) | 2015-02-12 |
US20100329877A1 (en) | 2010-12-30 |
CA2706289C (en) | 2014-02-04 |
IL206181A0 (en) | 2010-12-30 |
AT508323A1 (en) | 2010-12-15 |
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