EP2386663B1 - Method for producing a component and component from a gamma-titanium-aluminium base alloy - Google Patents
Method for producing a component and component from a gamma-titanium-aluminium base alloy Download PDFInfo
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- EP2386663B1 EP2386663B1 EP11450055.6A EP11450055A EP2386663B1 EP 2386663 B1 EP2386663 B1 EP 2386663B1 EP 11450055 A EP11450055 A EP 11450055A EP 2386663 B1 EP2386663 B1 EP 2386663B1
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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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
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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
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Definitions
- the invention relates to a method for producing a component from a titanium-aluminum base alloy.
- the invention relates to a component made of a titanium-aluminum base alloy, produced with dimensions close to the final dimensions.
- Titanium-aluminum base alloys generally have high strength, low density, and good corrosion resistance, and are preferably used as components in gas turbines and aircraft engines.
- Alloys having a composition of: aluminum 40 at.% To 50 at.%, Niobium 3 at.% To 10 at.%, Molybdenum to 4 at.%, And optionally the elements manganese, are suitable for the above fields of application. Boron, silicon, carbon, oxygen and nitrogen in low concentrations as well as titanium as the remainder of interest.
- a schematic diagram ( Fig. 1 ) shows microstructures as a function of the temperature and the aluminum concentration with temperature range information used by the person skilled in the art.
- Prepared the components can be by casting an ingot or powder by H schreib- I sostatisches- P ests (HIPing) of alloyed metal powder as well as by casting an ingot and optionally HIPing thereof followed by extrusion molding and each with a subsequent forging of the ingot or intermediate to a Component, which is subsequently subjected to heat treatments.
- HIPing H prolongation- I sostatisches- P ests
- Titanium-aluminum materials have only a narrow temperature window for a hot forming, although through the alloying elements niobium and molybdenum can be extended, nevertheless, there are limitations with respect to the deformation or forging of the parts. It is known, by slow, isothermal deformation, familiar to those skilled in the art as Isothermschmieden to produce a component at least partially by chipless shaping, but this is associated with great expense.
- a component produced by the above technologies will usually not have a homogeneous microstructure because, on the one hand, a low and unequal recrystallization potential of the slowly isothermally deformed material is given, and / or, on the other hand, a time-consuming diffusion of the atoms of the elements niobium and / or molybdenum are important for a deformability of a material, align themselves with the forming structure and thus can adversely affect the structure.
- components made of a titanium-aluminum base alloy are required, which have direction-independent, homogeneous, mechanical properties, the ductility, strength and creep resistance of the material are balanced even at high operating temperatures at a high level.
- the present invention has the object to provide a method by which a component having a homogeneous, fine and uniform microstructure can be produced, which component in balanced form, a ductility, strength and creep resistance of the material in all directions substantially the same has desired, high level and can be economically produced with dimensions close to final dimensions.
- the invention further aims at a component which, in the case of a targeted phase shaping of the microstructure, has desired mechanical properties, in particular the yield strength R p0.2 and strength R m and total elongation A t in the tensile test at room temperature and at a temperature of 700 ° C. ,
- a melt or powder metallurgy manufactured starting material having a chemical composition of in At .-%: Aluminum (Al) 41 to 48 optionally Niobium (Nb) 4 to 9 Molybdenum (Mo) 0.1 to 3.0 Manganese (Mn) to 2.4 Boron (B) to 1.0 Silicon (Si) to 1.0 Carbon (C) to 1.0 Oxygen (O) to 0.5 Nitrogen (N) to 0.5
- a melt or powder metallurgy produced material requires only compaction by hot isostatic pressing thereof, after which the blank is heated in a second step at an elevated isothermal forging temperature and, as found, at a favorably improved hot working capability of the material of a high speed -Massivumformung at a speed greater than 0.4 mm / sec and a compression ratio ⁇ of greater than 0.3 is subjected.
- This rapid massive forming of the blank can, surprisingly for the expert, be carried out at elevated temperature with high forming speed, according to the invention a high minimum deformation and subsequent cooling with high cooling rate for a formation of a high, for the time being frozen recrystallization potential in the structure are required.
- This recrystallization potential or stored energy resulting from the rapid deformation, which is also formed from the driving force from the chemical phase imbalance, in a third step causes the alloy to undergo a transformation in the region of the eutectoid temperature of the alloy extremely fine-globular microstructure from the phases GAMMA, BETA 0 , ALPHA 2 with ordered at room temperature atomic structure with certain phase proportions, which microstructure serves as a favorable fine grain starting structure for a subsequent, achievable by heat treatment (s), provided with regard to desired properties of the material structure formation ,
- the object is also achieved by a method of the type mentioned, in which in a first step, a melt or powder metallurgy manufactured starting material having a chemical composition of in At .-%: al 42 to 44.5 optionally Nb 3.5 to 4.5 Not a word 0.5 to 1.5 Mn to 2.2 B 12:05 to 0.2 Si 0001 to 12:01 C 0001 to 1.0 O 0001 to 0.1 N 0.0001 to 12:02
- the supersaturated ALPHA 2 grains and a fine but non-optimized microstructural shape give low material ductility and toughness at high strength values.
- Improved mechanical properties of the material can be achieved by means of a narrowed chemical composition, but the property profile is oriented only to specific uses.
- a choice of annealing time at a post-anneal close to the alpha transus temperature (T ⁇ ) can be made with a view to setting desired phase amounts and grain sizes.
- the ⁇ -phase is generally reduced as the annealing time increases.
- the structural phases After a thermal treatment in the Alpha-Transus area and a forced Cooling, the structural phases essentially have a disordered atomic structure.
- the supersaturated ALPHA 2 grains are converted into a lamellar ALPHA 2 / GAMMA structure without any significant change in grain size.
- a lamellar structure in the formerly supersaturated structural grains greatly improves the creep resistance of the material at high temperatures of around 700 ° C in the temperature range.
- This created with high efficiency of manufacturing component has a fine, globular, homogeneous microstructure with the same property profile in all directions of the material, which is advantageously used for a variety of applications.
- Fig. 1 schematically the microstructures of titanium-aluminum base alloys are shown as a function of the temperature and the aluminum concentration. Furthermore, the temperature data used by the expert can be seen.
- the in the Fig. 2 to Fig. 5 The microstructures shown are from a test series with an alloy Ti, 43.2 at.% Al, 4 at.% Nb, 1 at.% Mo, 0.1 at.% B.
- micrographs were taken at 200X magnification on the scanning electron microscope in electron backscatter contrast.
- a typical directed deformation texture shows as components directed GAMMA-BETA 0 -ALPHA 2 grains.
- Fig. 3 shows the structure of the deformed part after a heat treatment in the region of the eutectioden temperature (T eu ) in the present case at 1150 ° C, followed by a cooling.
- the microstructure consisted of globular ALPHA 2 grains with a particle size (measured as the diameter of the smallest circumscribed circle) of 3.2 ⁇ m ⁇ 1.9 ⁇ m with a volume fraction of approximately 25% from globular BETA 0 grains with a particle size of 3.7 ⁇ m ⁇ 2.1 ⁇ m with a volume fraction of about 26% and globular GAMMA grains with a grain size of 5.7 ⁇ m ⁇ 2.4 ⁇ m with a volume fraction of 49%.
- Fig. 4 is the structure of the deformed and subsequently annealed at 1150 ° C and cooled part after a subsequent annealing in the range of the alpha transus temperature (T ⁇ ) in the given case at a temperature of 1240 ° C and a cooling of this to 700 ° C in 5 min and further cooling in air.
- T ⁇ alpha transus temperature
- microstructural constituents were: ALPHA 2 granules with a particle size of 11.0 ⁇ m ⁇ 5.8 ⁇ m with a volume fraction of 73%, globular BETA 0 grains with a particle size of 4.5 ⁇ m ⁇ 2.6 ⁇ m with a volume fraction of 11% and globular GAMMA grains with a grain size of 4.2 ⁇ m ⁇ 2.2 ⁇ m with a volume fraction of 16%.
- Fig. 5 shows the structure of the deformed part after a fine grain annealing in the eutectoid temperature range (T eu ), followed by a high-temperature annealing in the ( ⁇ + ⁇ + ⁇ ) phase space or an alpha transus annealing (T ⁇ ) at 1240 ° C and a forced cooling stabilizing annealing in a given case at 875 ° C followed by slow cooling at a rate of 2 ° C / min.
- T eu eutectoid temperature range
- microstructure of the microstructure and the property profile of the material can be adjusted by varying the annealing temperature and / or the annealing time.
- the structure consisted of globular ALPHA 2 / GAMMA grains with lamellar ⁇ / ⁇ structure with a grain size of 7.1 ⁇ m ⁇ 3.8 ⁇ m with a volume fraction of 64% from globular BETA 0 grains with a grain size of 2.3 ⁇ m ⁇ 2.2 ⁇ m with a volume fraction of 13% and of globular GAMMA phases with a grain size of 2.7 ⁇ m ⁇ 2.1 ⁇ m with a volume fraction of 23%.
- a value A p of less than 0.65% was determined in the creep test (ASTME139 or EN2005-5) at a test voltage in the sample of 250 MPa and a stress duration of 100 hours.
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Description
Die Erfindung betrifft ein Verfahren zur Herstellung eines Bauteiles aus einer Titan-Aluminium-Basislegierung.The invention relates to a method for producing a component from a titanium-aluminum base alloy.
Weiters bezieht sich die Erfindung auf ein Bauteil aus einer Titan-Aluminium-Basislegierung, hergestellt mit endabmessungsnahen Dimensionen.Furthermore, the invention relates to a component made of a titanium-aluminum base alloy, produced with dimensions close to the final dimensions.
Titan-Aluminium-Basislegierungen weisen im Allgemeinen eine hohe Festigkeit, eine geringe Dichte und eine gute Korrosionsbeständigkeit auf und werden bevorzugt als Bauteile in Gasturbinen und Flugtriebwerken eingesetzt.Titanium-aluminum base alloys generally have high strength, low density, and good corrosion resistance, and are preferably used as components in gas turbines and aircraft engines.
Für obige Anwendungsgebiete sind insbesondere Legierungen mit einer Zusammensetzung von: Aluminium 40 At.-% bis 50 At.-%, Niob 3 At.-% bis 10 At.-%, Molybdän bis 4 At.-% sowie optional die Elemente Mangan, Bor, Silicium, Kohlenstoff, Sauerstoff und Stickstoff in geringen Konzentrationen sowie Titan als Rest von Interesse.Alloys having a composition of:
Diese Legierungen erstarren vorzugsweise vollständig über den β-Mischkristall und durchlaufen bei einer nachfolgenden Abkühlung eine Reihe von Phasenumwandlungen. Ein Prinzipschaubild (
Hergestellt können die Bauteile werden durch Gießen eines Blockes oder pulvermetallurgisch durch Heiß-Isostatisches-Pressen (HIPen) von legiertem Metallpulver sowie durch Gießen eines Blockes und gegebenenfalls HIPen desselben mit anschließendem Strangpressen und jeweils mit einem nachfolgenden Schmieden des Blockes oder Zwischenproduktes zu einem Bauteil, welches in der Folge Wärmebehandlungen unterworfen wird.Prepared the components can be by casting an ingot or powder by H eiß- I sostatisches- P ests (HIPing) of alloyed metal powder as well as by casting an ingot and optionally HIPing thereof followed by extrusion molding and each with a subsequent forging of the ingot or intermediate to a Component, which is subsequently subjected to heat treatments.
Titan-Aluminium-Werkstoffe haben für eine Warmformgebung nur ein schmales Temperaturfenster, welches zwar durch die Legierungselemente Niob und Molybdän erweitert werden kann, trotzdem ergeben sich Limitierungen bezüglich der Verformung bzw. Schmiedung der Teile. Es ist bekannt, durch langsames, isothermes Verformen, dem Fachmann geläufig als Isothermschmieden, ein Bauteil zumindest teilweise durch spanlose Formgebung herzustellen, allerdings ist dies mit hohem Aufwand verbunden.Titanium-aluminum materials have only a narrow temperature window for a hot forming, although through the alloying elements niobium and molybdenum can be extended, nevertheless, there are limitations with respect to the deformation or forging of the parts. It is known, by slow, isothermal deformation, familiar to those skilled in the art as Isothermschmieden to produce a component at least partially by chipless shaping, but this is associated with great expense.
Allenfalls wird ein nach obigen Technologien hergestelltes Bauteil zumeist keine homogene Gefügestruktur aufweisen, weil einerseits ein geringes und ungleiches Rekristallisationspotential des langsam isotherm verformten Werkstoffes gegeben ist, und/oder andererseits die einen hohen Zeitaufwand fordernde Diffusion der Atome der Elemente Niob und/oder Molybdän, die für eine Verformbarkeit eines Werkstoffes wichtig sind, sich nach der Umformstruktur ausrichten und derart das Gefüge nachteilig beeinflussen können.At most, a component produced by the above technologies will usually not have a homogeneous microstructure because, on the one hand, a low and unequal recrystallization potential of the slowly isothermally deformed material is given, and / or, on the other hand, a time-consuming diffusion of the atoms of the elements niobium and / or molybdenum are important for a deformability of a material, align themselves with the forming structure and thus can adversely affect the structure.
Eine Homogenisierung der Gefügeausbildung und damit ein Erreichen isotroper, mechanischer Eigenschaften des Werkstoffes durch zeitaufwändige Glühbehandlungen sind zwar grundsätzlich möglich, erfordert allerdings einen hohen Aufwand.Although a homogenization of the structure formation and thus an achievement of isotropic, mechanical properties of the material by time-consuming annealing treatments are in principle possible, however, requires a lot of effort.
Für die industrielle Praxis sind Bauteile aus einer Titan-Aluminium-Basislegierung erforderlich, welche richtungsunabhängig homogene, mechanische Eigenschaften aufweisen, wobei die Duktilität, Festigkeit und Kriechbeständigkeit des Werkstoffes auch bei hohen Einsatztemperaturen ausgewogen auf hohem Niveau vorliegen.For industrial practice, components made of a titanium-aluminum base alloy are required, which have direction-independent, homogeneous, mechanical properties, the ductility, strength and creep resistance of the material are balanced even at high operating temperatures at a high level.
Aus dem Stand der Technik sind die folgenden Verfahren bzw. Bauteile bekannt:From the prior art, the following methods or components are known:
-
SCHMOELZER T ET AL: "Phase fractions, transition and ordering temperatures in TiAl-Nb-Mo alloys: An in- and ex-situ studySCHMOELZER T ET AL: "Phase fractions, transition and ordering temperatures in TiAl-Nb-Mo alloys: An in- and ex-situ study -
CLEMENS H ET AL: "In and ex situ investigations of the beta-phase in a Nb and Mo containing gamma-TiAl based alloyCLEMENS H ET AL: "In and ex situ investigations of the beta-phase in a Nb and Mo containing gamma-TiAl based alloy -
HABEL U ET AL: "PROCESSING, MICROSTRUCTURE AND TENSILE PROPERTIES OF .GAMMA.-TIAL PM ALLOY 395MMHABEL U ET AL: "PROCESSING, MICROSTRUCTURE AND TENSILE PROPERTIES OF .GAMMA.-TIAL PM ALLOY 395MM -
D. ZHANG ET AL: "Effect of heat-treatments and hot-isostatic pressing on phase transformation and microstructure in a B/B2 containing Gamma-TiAl based alloyD. ZHANG ET AL: "Effect of heat-treatments and hot-isostatic pressing on phase transformation and microstructure in a B / B2 containing gamma-TiAl based alloy -
H. CLEMENS ET AL: "Design of Novel B-Solidifying TiAl Alloys with Adjustable B/B2-Phase Fraction and Excellent Hot-WorkabilityH. CLEMENS ET AL: "Design of Novel B-Solidifying TiAl Alloys with Adjustable B / B2 Phase Fraction and Excellent Hot Workability -
Auch in derAlso in the
DE 10 2004 056582 A1DE 10 2004 056582 A1 EP 0 464 366EP 0 464 366
Ausgehend vom Stand der Technik liegt der vorliegenden Erfindung die Aufgabe zugrunde, ein Verfahren anzugeben, mit welchem ein Bauteil mit homogener, feiner und gleichmäßiger Gefügestruktur herstellbar ist, welches Bauteil in ausgewogener Form eine Duktilität, Festigkeit und Kriechbeständigkeit des Werkstoffes in allen Richtungen im Wesentlichen gleich auf gewünschtem, hohen Niveau aufweist und mit endabmessungsnahen Dimensionen wirtschaftlich herstellbar ist.Based on the prior art, the present invention has the object to provide a method by which a component having a homogeneous, fine and uniform microstructure can be produced, which component in balanced form, a ductility, strength and creep resistance of the material in all directions substantially the same has desired, high level and can be economically produced with dimensions close to final dimensions.
Die Erfindung zielt weiters auf ein Bauteil ab, welches bei einer gezielten Phasenausformung des Gefüges gewünschte, mechanische Eigenschaften, insbesondere der Dehngrenze Rp0.2 und Festigkeit Rm sowie Gesamtdehnung At im Zugversuch bei Raumtemperatur und bei einer Temperatur von 700°C, aufweist.The invention further aims at a component which, in the case of a targeted phase shaping of the microstructure, has desired mechanical properties, in particular the yield strength R p0.2 and strength R m and total elongation A t in the tensile test at room temperature and at a temperature of 700 ° C. ,
Die Aufgabe wird durch ein Verfahren der eingangs genannten Art gelöst, bei welchem in einem ersten Schritt ein schmelz- oder pulvermetallurgisch gefertigtes Vormaterial mit einer chemischen Zusammensetzung von in At.-%:
Titan und Verunreinigungen als Rest,
hergestellt und dieses Vormaterial bei einer Druckerhöhung auf mindestens 150 MPa bei einer Temperatur von mindestens 1000°C nach einer Durchwärmung während einer Zeitdauer von mindestens 60 min isostatisch zu einem Rohteil gepresst wird, wonach in einem zweiten Schritt das HIP-Rohteil einer Warmformgebung durch eine Schnell-Massivumformung mit einer Geschwindigkeit von größer 0.4 mm/sec und einer Umformung durch Stauchen gemessen als lokale Dehnung ϕ von größer 0.3, wobei ϕ wie folgt definiert ist:
- hf = Höhe des Werkstückes nach dem Stauchen
- ho = Höhe des Werkstückes vor dem Stauchen
and this starting material is isostatically pressed to a blank at a pressure of at least 150 MPa at a temperature of at least 1000 ° C after a soak for a period of at least 60 min, after which in a second step the HIP blank of a hot forming by a Rapid massive forming with a speed of greater than 0.4 mm / sec and a deformation by compression measured as local elongation φ of greater than 0.3, where φ is defined as follows:
- h f = height of the workpiece after swaging
- h o = height of the workpiece before swaging
Rekristallisationsenergiepotential aufweist, gebildet wird, wonach das Bauteil für ein Einstellen gewünschter Werkstoffeigenschaften in einem dritten Schritt einer Wärmebehandlung unterworfen wird, bei welcher im Bereich der eutektoiden Temperatur der Legierung, insbesondere von 1010 bis 1180°C in einer Zeitspanne von 30 bis 1000 min aus dem Verformungsgefüge, aufgrund der gespeicherten Verformungsenergie und der Triebkraft, welche aus dem chemischen Phasenungleichgewicht nach dem Verformen und Abkühlen besteht, eine homogene, feinglobulare Mikrostruktur, bestehend aus den bei Raumtemperatur eine geordnete Atomstruktur aufweisenden Phasen:
GAMMA, BETA0, ALPHA2 (γ,β0,α2)
mit einer Ausformung:
- ALPHA2:
- globular mit einer Korngröße von 1 bis 50 µm mit einem Volumsanteil von 1 bis 50% die vereinzelte, gröbere γ-Lamellen mit einer Dicke von > 100 nm enthalten können
- BETA0:
- globular die α2-Phase umgebend, mit einer Korngröße von 1 bis 25 µm mit einem Volumsanteil von 1 bis 50%
- GAMMA:
- globular die α2-Phase umgebend, mit einer Korngröße von 1 bis 25 µm mit einem Volumsanteil von 1 bis 60%
GAMMA, BETA 0 , ALPHA 2 (γ, β 0 , α 2 )
with a shape:
- ALPHA 2 :
- Globular with a particle size of 1 to 50 microns with a volume fraction of 1 to 50%, the scattered, coarser γ-lamellae with a thickness of> 100 nm may contain
- BETA 0 :
- Globular surrounding the α 2 -phase, with a grain size of 1 to 25 μm with a volume fraction of 1 to 50%
- GAMMA:
- Globular surrounding the α 2 -phase, with a particle size of 1 to 25 μm with a volume fraction of 1 to 60%
Mit dem erfindungsgemäßen Verfahren wird eine Vielzahl von technischen und wirtschaftlichen Vorteilen erreicht.With the method according to the invention a variety of technical and economic advantages is achieved.
Im ersten Schritt des Verfahrens erfordert ein schmelz- oder pulvermetallurgisch hergestelltes Vormaterial lediglich eine Kompaktierung durch heißisostatisches Pressen desselben, wonach das Rohteil in einem zweiten Schritt bei einer gegenüber einem Isothermschmieden erhöhten Temperatur und, wie gefunden wurde, bei einem vorteilhaft verbesserten Warmumformvermögen des Materials einer Schnell-Massivumformung mit einer Geschwindigkeit von größer 0.4 mm/sec und einem Stauchgrad ϕ von größer 0.3 unterzogen wird. Diese Schnell-Massivumformung des Rohteiles kann, für den Fachmann überraschend, bei erhöhter Temperatur mit hoher Umformgeschwindigkeit erfolgen, wobei erfindungsgemäß eine hohe Mindestverformung und eine nachfolgende Abkühlung mit hoher Kühlrate für eine Ausbildung eines hohen, vorerst eingefrorenen Rekristallisierungspotentials im Gefüge erforderlich sind.In the first step of the process, a melt or powder metallurgy produced material requires only compaction by hot isostatic pressing thereof, after which the blank is heated in a second step at an elevated isothermal forging temperature and, as found, at a favorably improved hot working capability of the material of a high speed -Massivumformung at a speed greater than 0.4 mm / sec and a compression ratio φ of greater than 0.3 is subjected. This rapid massive forming of the blank can, surprisingly for the expert, be carried out at elevated temperature with high forming speed, according to the invention a high minimum deformation and subsequent cooling with high cooling rate for a formation of a high, for the time being frozen recrystallization potential in the structure are required.
Dieses Rekristallisationspotential bzw. diese gespeicherte aus der Schnell-Verformung resultierende Energie, welches bzw. welche auch aus der Triebkraft aus dem chemischen Phasenungleichgewicht gebildet ist, bewirkt in einem dritten Schritt bei einer Glühung des Werkstoffes im Bereich der eutektoiden Temperatur der Legierung eine Umwandlung in eine äußerst feinglobulare Mikrostruktur aus den Phasen GAMMA, BETA0, ALPHA2 mit bei Raumtemperatur geordneter Atomstruktur mit bestimmten Phasenanteilen, welche Gefügestruktur als günstige Feinkorn-Ausgangsstruktur für eine nachfolgende, durch Wärmebehandlung(en) erreichbare, im Hinblick auf gewünschte Eigenschaften des Werkstoffes vorgesehene Gefügeausformung dient.This recrystallization potential or stored energy resulting from the rapid deformation, which is also formed from the driving force from the chemical phase imbalance, in a third step causes the alloy to undergo a transformation in the region of the eutectoid temperature of the alloy extremely fine-globular microstructure from the phases GAMMA, BETA 0 , ALPHA 2 with ordered at room temperature atomic structure with certain phase proportions, which microstructure serves as a favorable fine grain starting structure for a subsequent, achievable by heat treatment (s), provided with regard to desired properties of the material structure formation ,
Die Aufgabe wird auch durch ein Verfahren der eingangs genannten Art gelöst, bei welchem in einem ersten Schritt ein schmelz- oder pulvermetallurgisch gefertigtes Vormaterial mit einer chemischen Zusammensetzung von in At.-%:The object is also achieved by a method of the type mentioned, in which in a first step, a melt or powder metallurgy manufactured starting material having a chemical composition of in At .-%:
Titan und Verunreinigungen als Rest
hergestellt und dieses Vormaterial bei einer Druckerhöhung auf mindestens 150 MPa bei einer Temperatur von mindestens 1000°C nach einer Durchwärmung während einer Zeitdauer von mindestens 60 min isostatisch zu einem Rohteil gepresst wird, wonach in einem zweiten Schritt das HIP-Rohteil einer Warmformgebung durch eine Schnell-Massivumformung mit einer Geschwindigkeit von größer 0.4 mm/sec und einer Umformung durch Stauchen gemessen als lokale Dehnung ϕ von größer 0.3, wobei ϕ wie folgt definiert ist:
- hf = Höhe des Werkstückes nach dem Stauchen
- ho = Höhe des Werkstückes vor dem Stauchen
GAMMA, BETA0, ALPHA2 (γ,β0,α2)
mit einer Ausformung:
- ALPHA2:
- globular mit einer Korngröße von 1 bis 10 µm mit einem Volumsanteil von 10 bis 35% die vereinzelte, gröbere γ-Lamellen mit einer Dicke von > 100 nm enthalten können
- BETA0:
- globular die α2-Phase umgebend, mit einer Korngröße von 1 bis 10 µm mit einem Volumsanteil von 15 bis 45%
- GAMMA:
- globular die α2-Phase umgebend, mit einer Korngröße von 1 bis 10 µm mit einem Volumsanteil von 15 bis 60%
Stabilisierungsglühung des Bauteiles, erfolgt (erfolgen). Titanium and impurities as rest
and this starting material is isostatically pressed to a blank at a pressure of at least 150 MPa at a temperature of at least 1000 ° C after a soak for a period of at least 60 min, after which in a second step the HIP blank of a hot forming by a Fast -Massivumformung with a speed of greater than 0.4 mm / sec and a deformation by compression measured as a local elongation φ of greater than 0.3, where φ is defined as follows:
- h f = height of the workpiece after swaging
- h o = height of the workpiece before swaging
GAMMA, BETA 0 , ALPHA 2 (γ, β 0 , α 2 )
with a shape:
- ALPHA 2 :
- Globular with a particle size of 1 to 10 microns with a volume fraction of 10 to 35%, the isolated, coarser γ-lamellae with a thickness of> 100 nm may contain
- BETA 0 :
- globular surrounding the α 2 -phase, with a grain size of 1 to 10 μm with a volume fraction of 15 to 45%
- GAMMA:
- Globular surrounding the α 2 -phase, with a grain size of 1 to 10 μm with a volume fraction of 15 to 60%
Stabilizing annealing of the component, carried out (done).
Eine derartige, in den Konzentrationen der Elemente eingeschränkte, chemische Zusammensetzung des Werkstoffes kann ein durch die Verfahrensparameter erreichtes, günstiges Verhalten bezüglich der Gefügeum- und -ausbildung intensivieren.Such, limited in the concentrations of the elements, chemical composition of the material can intensify a achieved by the process parameters, favorable behavior in terms of structural transformation and education.
Die Feinkornausbildung im Werkstoff, geschaffen nach obigem Verfahren, bewirkt zwar bei isotroper Gefügemorphologie eine erhöhte Festigkeit in engeren Grenzen, wobei jedoch die Zähigkeit und die Kriechbeständigkeit des Materials für bestimmte Anwendungsgebiete als nicht ausreichend erachtet werden können. Diese Feinkornstruktur bildet jedoch allenfalls eine Voraussetzung für den Erhalt eines weitgehend feinen, homogenen Gefüges bei weiteren Glühbehandlungen zur Einstellung gewünschter, mechanischer Eigenschaften des Bauteiles.The fine grain formation in the material, created by the above method, although in isotropic microstructure morphology causes increased strength within narrow limits, but the toughness and the creep resistance of the material for certain applications can not be considered sufficient. However, this fine grain structure is at best a prerequisite for obtaining a substantially fine, homogeneous structure in further annealing treatments for setting desired, mechanical properties of the component.
Um insbesondere die Hochtemperatureigenschaften des Werkstoffes betreffend eine Verbesserung der Duktilität bzw. eine Erhöhung der Zähigkeit und einer Erhöhung der Kriechbeständigkeit zu erreichen, ist gemäß der Erfindung vorgesehen, das Bauteil mit einer im dritten Schritt geschaffenen Feinkornstruktur zur Einstellung von optimierten Hochtemperaturwerkstoffeigenschaften mindestens einer Folgeglühung zu unterwerfen, welche Folgeglühung im Bereich nahe der Alpha-Transus-Temperatur (Tα) der Legierung im Dreiphasenraum (Alpha, Beta, Gamma) während einer Zeitdauer von mindestens 30 bis 6000 min erfolgt, wonach das Teil in einer Zeitspanne von weniger als 10 min auf eine Temperatur von 700°C und anschließend weiter, vorzugsweise an Luft, abgekühlt wird und derart eine Phasenausformung:
- ALPHA2:
- globular übersättigt, gegebenenfalls gering feine γ-Lamellen enthaltend, mit einer Korngröße von 5 µm bis 100 µm mit einem Volumsanteil von 25% bis 98%
- BETA0:
- globular, mit einer
Korngröße von 1 µm bis 25 µm miteinem Volumsanteil von 1% bis 25% - GAMMA:
- globular, mit einer
Korngröße von 1 µm bis 25 µm miteinem Volumsanteil von 1% bis 50%
- ALPHA 2 :
- Globular supersaturated, possibly containing low-fine γ-lamellae, with a particle size of 5 μm to 100 μm with a volume fraction of 25% to 98%
- BETA 0 :
- globular, with a particle size of 1 μm to 25 μm with a volume fraction of 1% to 25%
- GAMMA:
- globular, with a particle size of 1 μm to 25 μm with a volume fraction of 1% to 50%
Insbesondere die übersättigten ALPHA2-Körner und eine zwar feine, jedoch nicht optimierte Gefügeausformung ergeben bei hohen Festigkeitswerten eine niedrige Materialduktilität und Zähigkeit. Durch eine eingeengte, chemische Zusammensetzung sind verbesserte, mechanische Werkstoffeigenschaften erreichbar, jedoch ist das Eigenschaftsprofil nur auf bestimmte Verwendungszwecke ausgerichtet.In particular, the supersaturated ALPHA 2 grains and a fine but non-optimized microstructural shape give low material ductility and toughness at high strength values. Improved mechanical properties of the material can be achieved by means of a narrowed chemical composition, but the property profile is oriented only to specific uses.
Eine eingeengte, chemische Zusammensetzung des Werkstoffes, wie vorstehend angegeben, kann zwar für ein Erreichen von günstigen Anteilen der Gefügebestandteile mit engeren Abmessungen und engeren Gehaltsgrenzen genutzt werden, wobei sich die daraus ergebenden Vorteile in einer gewissen Präzisierung der mechanischen Eigenschaftswerte niederschlagen; im Wesentlichen werden damit jedoch in höchst vorteilhafter Weise die Voraussetzungen für eine Optimierung des Hochtemperaturverhaltens eines Bauteiles aus einer Titan-Aluminium-Basislegierung erstellt.Although a narrowed chemical composition of the material, as stated above, can be used to achieve favorable proportions of the microstructural constituents with narrower dimensions and narrower content limits, the resulting advantages are reflected in a certain refinement of the mechanical property values; Essentially, however, the prerequisites for optimizing the high-temperature behavior of a component made of a titanium-aluminum base alloy are created in a highly advantageous manner.
Eine Wahl der Glühzeit bei einer Folgeglühung nahe der Alpha-Transus-Temperatur (Tα) kann im Hinblick auf eine Einstellung von gewünschten Phasenmengen und der Korngrößen erfolgen. Beispielsweise wird die β-Phase mit zunehmender Glühdauer generell reduziert.A choice of annealing time at a post-anneal close to the alpha transus temperature (T α ) can be made with a view to setting desired phase amounts and grain sizes. For example, the β-phase is generally reduced as the annealing time increases.
Nach einer thermischen Behandlung im Alpha-Transus-Gebiet und einer forcierten Abkühlung weisen die Gefügephasen im Wesentlichen eine ungeordnete Atomstruktur auf.After a thermal treatment in the Alpha-Transus area and a forced Cooling, the structural phases essentially have a disordered atomic structure.
Wenn beim Herstellungsverfahren das Bauteil nach einer Folgeglühung mindestens einer Stabilisierungsglühung unterworfen wird, welche in einem Temperaturbereich von 700°C bis 1000°C, allenfalls oberhalb der Anwendungstemperatur des Bauteiles mit einer Dauer von 60 min bis 1000 min und einer anschließenden Langsam- bzw. Ofenabkühlung mit einer Geschwindigkeit von weniger als 5°C/min, vorzugsweise von weniger als 1°C/min, zur Einstellung bzw. Ausformung der Gefügebestandteile:
- ALPHA2 / GAMMA:
- Lamellarkorn mit einer Korngröße von 5 µm bis 100 µm mit einem Volumsanteil von 25% bis 98% mit einer (α2/γ) Lamellen-Feinstruktur vorzugsweise mit einem mittleren Lamellenabstand von 10
nm bis 1 µm - BETA0:
- globular, mit einer
Korngröße von 1 µm bis 25 µm miteinem Volumsanteil von 1% bis 25% - GAMMA:
- globular, mit einer
Korngröße von 1 µm bis 25 µm miteinem Volumsanteil von 1% bis 50%
- ALPHA 2 / GAMMA:
- Lamellar grain with a grain size of 5 .mu.m to 100 .mu.m with a volume fraction of 25% to 98% with a (α 2 / γ) lamellar fine structure, preferably with a mean fin spacing of 10 nm to 1 .mu.m
- BETA 0 :
- globular, with a particle size of 1 μm to 25 μm with a volume fraction of 1% to 25%
- GAMMA:
- globular, with a particle size of 1 μm to 25 μm with a volume fraction of 1% to 50%
Mittels einer Stabilisierungsglühung mit einer Langsamabkühlung, in welcher eine ausreichende Atomdiffusion erhalten bleibt, erfolgt eine Umwandlung der übersättigten ALPHA2-Körner in eine lamellare ALPHA2 / GAMMA-Struktur ohne wesentliche Änderung der Korngröße. Eine Lamellenstruktur in den ehemals übersättigten Gefügekörnern verbessert im hohen Maße die Kriechbeständigkeit des Werkstoffes bei hohen Belastungen im Temperaturbereich um 700°C.By means of a stabilization annealing with a slow cooling, in which sufficient atomic diffusion is maintained, the supersaturated ALPHA 2 grains are converted into a lamellar ALPHA 2 / GAMMA structure without any significant change in grain size. A lamellar structure in the formerly supersaturated structural grains greatly improves the creep resistance of the material at high temperatures of around 700 ° C in the temperature range.
Das weitere Ziel der Erfindung wird mit einem endabmessungsnahe Dimensionen aufweisenden Bauteil aus einer Titan-Aluminium-Basislegierung mit einer chemischen Zusammensetzung gemäß Anspruch 1 oder 2, hergestellt mit einem Gefüge des Werkstoffes, bestehend aus den bei Raumtemperatur eine geordnete Atomstruktur aufweisenden Phasen:
GAMMA, BETA0, ALPHA2 (γ,β0,α2)
mit einer Ausformung:
- ALPHA2:
- globular übersättigt mit einer
Korngröße von 1µm bis 50 µm miteinem Volumsanteil von 1% bis 50%, die vereinzelte, gröbere γ-Lamellen mit einer Dicke von > 100 nm enthalten können - BETA0:
- globular die α2-Phase umgebend, mit einer
Korngröße von 1 µm bis 25 µm miteinem Volumsanteil von 1% bis 50% - GAMMA:
- globular die α2-Phase umgebend, mit einer
Korngröße von 1 µm bis 25 µm miteinem Volumsanteil von 1% bis 60%
- Festigkeit und Bruchdehnung bei Raumtemperatur:
- ∘ Rp0.2: 650 bis 910 MPa
- ∘ Rm: 680 bis 1010 MPa
- ∘ At: 0.5% bis 3%
- Festigkeit und Bruchdehnung bei 700°C:
- ∘ Rp0.2: 520 bis 690 MPa
- ∘ Rm: 620 bis 970 MPa
- ∘ At: 1% bis 3.5%
GAMMA, BETA 0 , ALPHA 2 (γ, β 0 , α 2 )
with a shape:
- ALPHA 2 :
- Globular supersaturated with a particle size of 1 .mu.m to 50 .mu.m with a volume fraction of 1% to 50%, which may contain isolated, coarser γ-lamellae with a thickness of> 100 nm
- BETA 0 :
- globular surrounding the α 2 -phase, with a grain size of 1 μm to 25 μm with a volume fraction of 1% to 50%
- GAMMA:
- globular surrounding the α 2 -phase, with a grain size of 1 μm to 25 μm with a volume fraction of 1% to 60%
- Strength and elongation at room temperature:
- P R p0.2 : 650 to 910 MPa
- ∘ R m : 680 to 1010 MPa
- ∘ A t : 0.5% to 3%
- Strength and elongation at 700 ° C:
- P R p0.2 : 520 to 690 MPa
- ∘ R m : 620 to 970 MPa
- ∘ A t : 1% to 3.5%
Dieses mit hoher Wirtschaftlichkeit der Herstellung geschaffene Bauteil hat eine feine, globulare, homogene Gefügestruktur mit in allen Richtungen gleichem Eigenschaftsprofil des Werkstoffes, welches für eine Vielzahl von Anwendungszwecken vorteilhaft einsetzbar ist.This created with high efficiency of manufacturing component has a fine, globular, homogeneous microstructure with the same property profile in all directions of the material, which is advantageously used for a variety of applications.
Um eine Verbesserung der mechanischen Materialeigenschaften, insbesondere eine Erhöhung der Kriechbeständigkeit, zu erreichen, ist es von Vorteil, wenn das Bauteil mit einem Gefüge des Werkstoffes aus:
- ALPHA2:
- globular übersättigt, gegebenenfalls gering feine γ-Lamellen enthaltend, mit einer Korngröße von 5 µm bis 80 µm mit
einem Volumsanteil von 50% bis 95% - BETA0:
- globular, mit einer
Korngröße von 1 µm bis 20 µm mit einem Volumsanteil von 31% bis 25% - GAMMA:
- globular, mit einer
Korngröße von 1 µm bis 20 µm miteinem Volumsanteil von 1% bis 28%
- Festigkeit und Bruchdehnung (nach ASTM E8M, EN 2002-1) bei Raumtemperatur:
- ∘ Rp0.2: 650 bis 940 MPa
- ∘ Rm: 730 bis 1050 MPa
- ∘ At: 0.2% bis 2%
- Festigkeit und Bruchdehnung bei 700°C:
- ∘ Rp0.2: 430 bis 620 MPa
- ∘ Rm: 590 bis 940 MPa
- ∘ At: 1% bis 2.5%
- ALPHA 2 :
- globular supersaturated, optionally containing small fine γ-lamellae, with a particle size of 5 μm to 80 μm with a volume fraction of 50% to 95%
- BETA 0 :
- globular, with a grain size of 1 μm to 20 μm with a volume fraction of 31% to 25%
- GAMMA:
- globular, with a grain size of 1 μm to 20 μm with a volume fraction of 1% to 28%
- Strength and elongation at break (according to ASTM E8M, EN 2002-1) at room temperature:
- P R p0.2 : 650 to 940 MPa
- ∘ R m : 730 to 1050 MPa
- ∘ A t : 0.2% to 2%
- Strength and elongation at 700 ° C:
- P R p0.2 : 430 to 620 MPa
- ∘ R m : 590 to 940 MPa
- ∘ A t : 1% to 2.5%
Ein besonderer Vorteil im Hinblick auf eine Duktilität, Festigkeit und Kriechbeständigkeit des Werkstoffes in allen Richtungen in gleichem Maße auf einem hohen Niveau wird erreicht, wenn das Bauteil mit einem Gefüge des Werkstoffes, bestehend aus den Bestandteilen mit einer Ausformung:
- ALPHA2 / GAMMA:
- Lamellarkorn mit einer Korngröße von 5 µm bis 100 µm mit einem Volumsanteil von 25% bis 98% mit einer (α2/γ) Lamellen-Feinstruktur vorzugsweise mit einem mittleren Lamellenabstand von 10
nm bis 1 nm - BETA0:
- globular, mit einer Korngröße von 0.5 µm bis 25 µm mit
einem Volumsanteil von 1% bis 25% - GAMMA:
- globular, mit einer Korngröße von 0.5 µm bis 25 µm mit
einem Volumsanteil von 1% bis 50%
- vorzugsweise eingestellt nach einem Verfahren gemäß Anspruch 6 oder 7 gebildet ist, wobei das Material folgende, mechanische Eigenschaften im Bereich von:
- Festigkeit und Bruchdehnung (nach ASTM E8M, EN 2002-1) bei Raumtemperatur:
- ∘ Rp0.2: 710 bis 1020 MPa
- ∘ Rm: 800 bis 1250 MPa
- ∘ At: 0.8
% bis 4%
- Festigkeit und Bruchdehnung bei 700°C:
- ∘ Rp0.2: 540 bis 760 MPa
- ∘ Rm: 630 bis 1140 MPa
- ∘ At: 1 % bis 4.5%
- Festigkeit und Bruchdehnung (nach ASTM E8M, EN 2002-1) bei Raumtemperatur:
- ALPHA 2 / GAMMA:
- Lamellar grain with a grain size of 5 .mu.m to 100 .mu.m with a volume fraction of 25% to 98% with a (α 2 / γ) lamellar fine structure, preferably with a mean fin spacing of 10 nm to 1 nm
- BETA 0 :
- globular, with a particle size of 0.5 μm to 25 μm with a volume fraction of 1% to 25%
- GAMMA:
- globular, with a particle size of 0.5 μm to 25 μm with a volume fraction of 1% to 50%
- preferably adjusted according to a method according to claim 6 or 7, wherein the material has the following mechanical properties in the range of:
- Strength and elongation at break (according to ASTM E8M, EN 2002-1) at room temperature:
- P R p0.2 : 710 to 1020 MPa
- ∘ R m : 800 to 1250 MPa
- ∘ A t : 0.8% to 4%
- Strength and elongation at 700 ° C:
- P R p0.2 : 540 to 760 MPa
- ∘ R m : 630 to 1140 MPa
- ∘ A t : 1% to 4.5%
- Strength and elongation at break (according to ASTM E8M, EN 2002-1) at room temperature:
Im Folgenden soll die Erfindung anhand lediglich eine Legierungszusammensetzung umfassenden Bildern näher erläutert werden.In the following, the invention will be explained in more detail with reference to images comprising only one alloy composition.
Es zeigen:
- Fig. 1
- Gefügeausbildung in Abhängigkeit von der Temperatur und der Aluminiumkonzentration mit vom Fachmann verwendeten Temperaturbereichsangaben (Prinzipschaubild)
- Fig. 2
- Gefüge der Ti-AI-Basislegierung nach einer Massivumformung und anschließender Abkühlung
- Fig. 3
- Gefüge der Legierung nach einer Glühung im Bereich der eutektoiden Temperatur (Teu) und Abkühlung
- Fig. 4
- Gefüge der Legierung nach einer Glühung bei Alpha-Transus-Temperatur (Tα)
- Fig. 5
- Gefüge der Legierung nach einer Stabilisierungsglühung
- Fig. 1
- Structure formation as a function of the temperature and the aluminum concentration with temperature range data used by the person skilled in the art (schematic diagram)
- Fig. 2
- Microstructure of the Ti-Al base alloy after massive forming and subsequent cooling
- Fig. 3
- Structure of the alloy after annealing at the eutectoid temperature (T eu ) and cooling
- Fig. 4
- Microstructure of Alloy After Annealing at Alpha Transus Temperature (T α )
- Fig. 5
- Structure of the alloy after stabilization annealing
In
Die in den
Diese Legierung hat eine eutektoide Temperatur von Teu 1165°C ± 7°C und eine Alpha-Transus-Temperatur Tα = 1243°C ± 7°C, welche Temperaturen mit der Differentialthermoanalyse bestimmt wurden.This alloy has a eutectoid temperature of T eu 1165 ° C ± 7 ° C and an alpha transus temperature T α = 1 243 ° C ± 7 ° C, which temperatures were determined by differential thermal analysis.
Die Gefügebilder wurden mit einer 200-fachen Vergrößerung am Rasterelektronenmikroskop im Elektronenrückstreukontrast aufgenommen.The micrographs were taken at 200X magnification on the scanning electron microscope in electron backscatter contrast.
Das Gefüge bestand aus globularen ALPHA2-Körnern mit einer Korngröße (gemessen als Durchmesser des kleinsten umschreibenden Kreises) von 3.2 µm ± 1.9 µm mit einem Volumsanteil von ca. 25% aus globularen BETA0-Körnern mit einer Korngröße von 3.7 µm ± 2.1 µm mit einem Volumsanteil von ca. 26% und aus globularen GAMMA-Körnern mit einer Korngröße von 5.7 µm ± 2.4 µm mit einem Volumsanteil von 49%.The microstructure consisted of globular ALPHA 2 grains with a particle size (measured as the diameter of the smallest circumscribed circle) of 3.2 μm ± 1.9 μm with a volume fraction of approximately 25% from globular BETA 0 grains with a particle size of 3.7 μm ± 2.1 μm with a volume fraction of about 26% and globular GAMMA grains with a grain size of 5.7 μm ± 2.4 μm with a volume fraction of 49%.
In
Die ermittelten Gefügebestandteile waren: ALPHA2-Körner in globularer Ausformung mit einer Korngröße von 11.0 µm ± 5.8 µm mit einem Volumsanteil von 73%, globulare BETA0-Körner mit einer Korngröße von 4.5 µm ± 2.6 µm mit einem Volumsanteil von 11 % und globulare GAMMA-Körner mit einer Korngröße von 4.2 µm ± 2.2 µm mit einem Volumsanteil von 16%.The microstructural constituents were: ALPHA 2 granules with a particle size of 11.0 μm ± 5.8 μm with a volume fraction of 73%, globular BETA 0 grains with a particle size of 4.5 μm ± 2.6 μm with a volume fraction of 11% and globular GAMMA grains with a grain size of 4.2 μm ± 2.2 μm with a volume fraction of 16%.
An dieser Stelle soll festgestellt werden, dass durch Variationen der Glühtemperatur und/oder der Glühzeit die Mikrostruktur des Gefüges und das Eigenschaftsprofil des Werkstoffes einstellbar sind.It should be noted at this point that the microstructure of the microstructure and the property profile of the material can be adjusted by varying the annealing temperature and / or the annealing time.
Nach obiger Wärmebehandlung bestand das Gefüge aus globularen ALPHA2/GAMMA-Körnern mit lamellarer α/γ-Struktur mit einer Korngröße von 7.1 µm ± 3.8 µm mit einem Volumsanteil von 64% aus globularen BETA0-Körnern mit einer Korngröße von 2.3 µm ± 2.2 µm mit einem Volumsanteil von 13% und aus globularen GAMMA-Phasen mit einer Korngröße von 2.7 µm ± 2.1 µm mit einem Volumsanteil von 23%.After the above heat treatment, the structure consisted of globular ALPHA 2 / GAMMA grains with lamellar α / γ structure with a grain size of 7.1 μm ± 3.8 μm with a volume fraction of 64% from globular BETA 0 grains with a grain size of 2.3 μm ± 2.2 μm with a volume fraction of 13% and of globular GAMMA phases with a grain size of 2.7 μm ± 2.1 μm with a volume fraction of 23%.
Wie auch die übrigen Proben von Versuchsreihen wurden an diesem Teil die wichtigsten mechanischen Eigenschaften gemessen. Bei Raumtemperatur lagen die Festigkeitswerte Rp0.2 über 720 MP, Rm über 810 MP und die Bruchdehnung über 1.6%.Like the other samples from series of tests, the most important mechanical properties were measured on this part. At room temperature, the strength values R p0.2 exceeded 720 MP, R m exceeded 810 MP and the elongation at break exceeded 1.6%.
Bei 700°C wurde im Kriechversuch (ASTME139 bzw. EN2005-5) bei einer Prüfspannung in der Probe von 250 MPa und einer Beanspruchungsdauer von 100 Std. ein Wert Ap von kleiner 0.65% ermittelt.At 700 ° C., a value A p of less than 0.65% was determined in the creep test (ASTME139 or EN2005-5) at a test voltage in the sample of 250 MPa and a stress duration of 100 hours.
Claims (9)
- Method for the production of a component made of a titanium-aluminum base alloy, in which, in a first step, a primary material which has been produced by melting or powder metallurgy and has a chemical composition in At.-% of:
Aluminum (Al) 41 to 48 optionally Niobium (Nb) 4 to 9 Molybdenum (Mo) 0.1 to 3.0 Manganese (Mn) to 2.4 Boron (B) to 1 .0 Silicon (Si) to 1.0 Carbon (C) to 1.0 Oxygen (0) to 0.5 Nitrogen (N) to 0.5
wherein this primary material is isostatically pressed into a blank under a pressure increase to at least 150 MPa at a temperature of at least 1000 °C after heating for a period of at least 60 min, whereupon, in a second step, the HIP blank is subjected to a thermoforming process by means of rapid-forming though a rapid mass forming at a rate greater than 0.4 mm/sec and a forming by compression measured as a local strain ϕ of greater than 0.3, where ϕ is defined as follows:hf = height of the workpiece after compressionho = height of the workpiece before compressionor another forming method with an equally high minimum forming, in particular by forging at a temperature in the range from 1000 to 1350 °C, to form a component with a subsequent cooling thereof, wherein the time until a temperature of 700 °C. is reached is at most 10 min, wherein a structure which may only be dynamically recovered or recrystallized in small subregions, but substantially has a forming structure with high recrystallization energy potential, wherein the component is subjected to heat treatment in a third step for the adjustment of desired material properties, which in the region of the eutectoid temperature (Teu) of the alloy, in particular from 1010 to 1180 °C, over a period of 30 to 1000 min from the forming structure, due to the stored forming energy and the driving force to the structural change, which consists of the chemical phase equilibrium after the forming and cooling, after cooling in air, a homogeneous fine-globular microstructure, formed from the phases having an ordered atomic structure at room temperature:
GAMMA, BETA0, ALPHA2 (γ, β0, α2)
having a formation:ALPHA2: globular with a grain size of 1 to 50 µm with a volume fraction of 1 to 50%, which may contain isolated, coarser γ-lamellae with a thickness > 100 nm BETA0: globular surrounding the α2 phase with a grain size of 1 to 25 µm with a volume fraction of 1 to 50%GAMMA: Globular surrounding the α2 phase with a grain size of 1 to 25 µm with a volume fraction of 1 to 50%wherein, in a subsequent step, at least one further heat treatment, in particular subsequent annealing and/or stabilizing annealing of the component, takes place. - Method for the production of a component from a titanium-aluminum base alloy, wherein, in a first step, a primary material which has been produced by melting or powder metallurgy and has a chemical composition in At.-% of at least.
Al 42 to 44.5 optionally Nb 3.5 to 4.5 Mo 0.5 to 1.5 Mn to 2.2 B 0.05 to 0.2 Si 0.001 to 0.01 C 0.001 to 1.0 O 0.001 to 0.1 N 0.0001 to 0.02
wherein this preliminary material is isostatically pressed into a blank at a pressure increase of at least 150 MPa at a temperature of at least 1000 °C after heating for a period of at least 60 minutes, whereupon, in a second step, the hot blank is subjected to a hot forming process by means of rapid-forming though rapid mass forming at a rate greater than 0.4 mm/sec and forming by compression measured as a local strain ϕ greater than 0.3, where ϕ is defined as follows:hf = height of the workpiece after compressionho = height of the workpiece before compressionor another forming method with an equally high minimum forming, in particular by forging at a temperature in the range from 1000 to 1350° C to form a component with subsequent cooling thereof, wherein the time until a temperature of 700 °C is reached is at most 10 min, wherein a structure which may be dynamically recovered or recrystallized only in small subregions, but essentially has a forming structure with a high recrystallization energy potential, after which the component is subjected to heat treatment in a third step in the range of the eutectoid temperature (Teu) of the alloy, in particular from 1040 to 1170 °C over a period of 30 to 600 min, for adjusting the desired material properties in a third step, wherein from the forming structures after cooling in air, a homogeneous, fine-lobular microstructure is produced consisting of the phases having an ordered atomic structure at room temperature:
GAMMA, BETA0, ALPHA2 (γ, β0, α2)
having a formation:ALPHA2: globular with a grain size of 1 to 10 µm with a volume fraction of 1 to 35%, which may contain isolated coarser γ-lamellae with a thickness of > 100 nm BETA0: globular surrounding the α2 phase with a grain size of 1 to 10 µm with a volume fraction of 15 to 45%GAMMA: globular surrounding the α2 phase with a grain size of 1 to 10 µm with a volume fraction of 15 to 60%wherein, optionally, at least one further heat treatment, in particular subsequent annealing and/or stabilizing annealing of the component, takes place in a subordinate step. - Method according to claim 1, wherein the component with a fine structure produced in the third step for the adjustment of optimum high temperature material properties is subjected to at least a following annealing in the range near the alpha transus temperature (To) of the alloy in the thee phases (Alpha, Beta, Gamma) during a time period of at least 30 to maximum of 6000 min, after which the part is cooled to a temperature of 700 °C in a period of less than 10 min and then further preferably in air, and a phase forming in this way:ALPHA2: globular supersaturated, optionally containing small fine γ-lamellae, with a grain size of 5 to 100 µm with a volume fraction of 25 to 98%BETAo: globular, with a grain size of 1 to 25 µm with a volume fraction of 1 to 25% GAMMA: globular, with a grain size of 1 to 25 µm with a volume fraction of 1 to 50%.
- Method according to claim 2, wherein the component having a fine structure created in the third step for the adjustment of optimized high temperature properties, is subjected to at least one subsequent annealing which is carried out in the region close to the alpha transus temperature (To) of the alloy in the three-phase space (Alpha, Beta, Gamma) for a period of at least 30 to a maximum of 6000 min, after which the part is cooled to a temperature of 700 °C over a period of less than 10 min and then further, preferably in air, and a phase forming in such a way:ALPHA2: globular super saturated, optionally containing small fine γ-lamellae, with a grain size of 5 to 80 µm with a volume fraction of 50 to 98%BETAo: globular, with a grain size of 1 to 20 µm with a volume fraction of 1 to 25% GAMMA: globular, with a grain size of 1 to 20 µm with a volume fraction of 1 to 28%.
- Method according to claim 3, wherein the component is subjected to at least one stabilizing annealing after a subsequent annealing according to claim 3, which is carried out in a temperature range from 700 to 1000 °C, possibly above the application temperature of the component with a duration of 60 to 1000 min, and a subsequent slow or furnace cooling at a rate of less than 5 °C/min, preferably less than 1 °C/min, for setting or shaping the structural constituents:ALPHA2/GAMMA: Lamellar grain with a grain size of 5 to 100 µm with a volume fraction of 25 to 98%, and an (α2/γ) lamellar fine structure, preferably with a mean lamellar spacing of 10 nm to 1 µmBETAo: globular, with a grain size of 1 to 25 µm with a volume fraction of 1 to 25% GAMMA: globular, with a grain size of 1 to 25 µm with a volume fraction of 1 to 50%.
- Method according to claim 4, wherein the component is subjected to at least one stabilizing annealing after a subsequent annealing according to claim 4, which is carried out in a temperature range of from 700 to 1000 °C, possibly above the application temperature of the component with a duration of 60 to 1000 min, and followed by slow or furnace cooling at a rate of less than 5 °C/min, preferably of less than 1 °C/min, for setting or shaping the structural components:ALPHA2/GAMMA: Lamellar grain with a grain size of 5 to 80 µm with an (α2/γ) lamellar fine structure, preferably with a mean lamellar spacing of 10 to 30 nm and with a volume fraction of 45 to 90%BETAo: globular, with a grain size of 1 to 20 µm with a volume fraction of 1 to 25% GAMMA: globular, with a grain size of 1 to 20 µm with a volume fraction of 1 to 25%.
- Component made of a titanium-aluminum base alloy with a chemical composition according to claim 1 or 2, produced with dimensions close to the final dimensions, obtainable by a method according to claim 1 or 2 with a structure of the material comprising the ordered atomic structure at room temperature phases:
GAMMA, BETA0, ALPHA2 (γ, β0, α2)
with a formation:ALPHA2: globular with a grain size of 1 to 50 µm with a volume fraction of 1 to 50%, which may contain isolated, coarser γ-lamellae with a thickness > 100 nm BETAo: globular surrounding the α2 phase, with a grain size of 1 to 25 µm with a volume fraction of 1 to 50%GAMMA: globularly surrounding the α2 phase, with a grain size of 1 to 25 µm, with a volume fraction of 1 to 60%,obtainable by a method according to claim 1 or 2, wherein the material has the following mechanical properties in the range of:• Strength and elongation at break at room temperature:∘ Rp0.2: 650 to 910 MPa∘ Rm: 680 to 1010 Mpa∘ At: 0.5 to 3%• Strength and elongation at break at 700 °C:Rp0.2: 520 to 690 MPa∘ Rm: 620 to 970 MPa∘ At: 1 to 3.5%. - Component made of a titanium-aluminum base alloy with a chemical composition according to claim 1 or 2, produced with dimensions close to the final dimensions, with a microstructure of the material consisting of:ALPHA2: globular super saturated, optionally containing small fine γ-lamellae, with a grain size of 5 to 80 µm with a volume fraction of 50 to 95%BETAo: globular, with a grain size of 1 to 20 µm with a volume fraction of 1 to 25%GAMMA: globular, with a grain size of 1 to 20 µm with a volume fraction of 1 to 28% adjusted by a method according to claim 3 or 4, wherein said material has the following mechanical properties in the range of:• Strength and elongation at break (according to ASTM E8M, EN 2002-1) at room temperature:∘ Rp0.2: 650 to 940 MPa∘ Rm: 730 to 1050 MPa∘ At: 0.2 to 2%• Strength and elongation at break at 700 °C:∘ Rp0.2: 430 to 620 MPa∘ Rm: 590 to 940 MPa∘ At: 1 to 2.5%.
- Component made of a titanium-aluminum base alloy with a chemical composition according to claim 1 or 2, produced with dimensions close to the final dimensions, with a microstructure of the material consisting of the components with a shaping:ALPHA2/GAMMA: Lamellar grain with a grain size of 5 to 100 µm with a volume fraction of 25 to 98% with an (α2/γ) lamellar fine structure, preferably with a mean lamellar spacing of 10 to 1 nmBETAo: globular, with a grain size of 0.5 to 25 µm with a volume fraction of 1 to 25%GAMMA: globular, with a grain size of 0.5 to 25 µm with a volume fraction of 1 to 50% adjusted by a method according to claim 5 or 6, wherein the material has the following mechanical properties in the range of:• Strength and elongation at break (according to ASTM E8M, EN 2002-1) at room temperature:∘ Rp0.2: 710 to 1020 MPa∘ Rm: 800 to 1250 MPa∘ At: 0.8 to 4%• Strength and elongation at break at 700 °C:∘ Rp0.2: 540 to 760 MPa∘ Rm: 630 to 1140 MPa∘ At: 1 to 4.5% having.
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