EP0256449B1 - Powder-metallurgical manufacture of work pieces from a heat-resisting aluminium alloy - Google Patents
Powder-metallurgical manufacture of work pieces from a heat-resisting aluminium alloy Download PDFInfo
- Publication number
- EP0256449B1 EP0256449B1 EP87111462A EP87111462A EP0256449B1 EP 0256449 B1 EP0256449 B1 EP 0256449B1 EP 87111462 A EP87111462 A EP 87111462A EP 87111462 A EP87111462 A EP 87111462A EP 0256449 B1 EP0256449 B1 EP 0256449B1
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- European Patent Office
- Prior art keywords
- weight
- powder
- alloy
- production
- workpiece according
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/002—Making metallic powder or suspensions thereof amorphous or microcrystalline
- B22F9/008—Rapid solidification processing
-
- 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
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
Definitions
- Heat-resistant aluminum alloys which are made from powders obtained at high cooling rates by atomizing a melt. High content of alloy components not permitted under the usual solidification conditions, e.g. Fe and Cr.
- the invention relates to the production of aluminum alloy powders and the production of moldings from these powders.
- Aluminum alloys which are suitable for the production of powders from melts by means of gas jet atomization using very high cooling speeds (105 ° C./s and more) and can be used for the production of heat-resistant workpieces, have become known in numerous variations.
- An important group are the polynary alloys of the type AI / Fe / X, which generally have relatively high iron contents, where X denotes at least one of the elements Ti, Zr, Hf, V, Nb, Cr, Mo, W.
- An alloy with 8% by weight Fe and 2% by weight Mo apparently occupies a special position (cf. GB-PS 2 088 409 A).
- the invention has for its object to provide a method for powder metallurgical production of a workpiece from a heat-resistant aluminum alloy taking into account the optimum alloy composition and adaptation of the process steps, which leads to tougher and more ductile finished products without sacrificing strength. In doing so, powder production should also be carried out at higher temperatures. stable phases are achieved, which - regardless of the particle size - are homogeneously distributed over the whole powder grain and give it a high deformability.
- an alloy which contains 8 to 14% by weight Fe, 0.5 to 2% by weight V and 0.2 to 1% by weight Mn, the rest being aluminum and contains any impurities, the alloy being melted, the melt being atomized at a cooling rate of at least 105 ° C./s in a gas stream to give particles with a diameter of 1 to 40 11 m, the dispersoids formed thereby being homogeneously distributed and not micro-eutectic Zone is present within a powder particle, and that the powder is compacted at a temperature of 350 to 450 ° C under a pressure of 2000 to 6000 bar in such a way that the intermetallic phase stabilized by Mn forms Al 6 Fe in fine distribution and the phase AI 3 Fe is largely suppressed.
- the melt was first atomized in a device by means of a gas stream (nitrogen) while maintaining a cooling rate of at least 105 ° C./s to a powder.
- the average particle diameter was approx. 20 ⁇ m, the maximum approx. 40 ⁇ m.
- the structure of the particles was characterized by an even distribution of the dispersoids, while the disruptive micro-eutectic that otherwise occurs with conventional alloys was missing.
- Approx. 160 g of the powder were compacted by hot pressing in a mold under a pressure of 3000 bar at a temperature of 400 ° C. to a press bolt of approximately 99% theoretical density.
- the heating time in the mold was about 45 minutes.
- the press bolt had a diameter of 40 mm and a height of 60 mm. This press bolt was inserted into the cylinder of an extrusion press and pressed under a pressure of 5000 bar at a temperature of 400 ° C to a rod of 13 mm in diameter.
- the reduction ratio was approximately 9: 1.
- Test pieces were cut out of the bar and the mechanical properties measured at room temperature and at 300 ° C. The yield point at room temperature was 450 MPa. A metallographic examination revealed the presence of considerable volume fractions of the Al 6 Fe phase, while practically no Al 3 Fe could be found. Furthermore, there were no non-deformed powder particles containing Al 3 Fe in the compacted material.
- the cooling rate during powder production should be at least 10 5 ° C / s.
- the particle diameter of the powder produced by gas jet atomization should be within the limits of 1 to 40 ⁇ m.
- the powder can be compressed at temperatures between 350 and 450 ° C under pressures of 2000 to 6000 bar. Preferred values are 400 ° C for powder compaction.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
- Materials For Medical Uses (AREA)
Description
Warmfeste Aluminiumlegierungen, welche aus mit hoher Abkühlungsgeschwindigkeit durch Zerstäuben einer Schmelze gewonnenen Pulvern hergestellt werden. Hoher Gehalt an unter sonst üblichen Erstarrungsbedingungen nicht zulässigen Legierungsbestandteilen wie z.B. Fe und Cr.Heat-resistant aluminum alloys which are made from powders obtained at high cooling rates by atomizing a melt. High content of alloy components not permitted under the usual solidification conditions, e.g. Fe and Cr.
Die Erfindung bezieht sich auf die Erzeugung von Aluminiumlegierungspulvern und die Herstellung von Formkörpern aus diesen Pulvern.The invention relates to the production of aluminum alloy powders and the production of moldings from these powders.
Insbesondere betrifft sie die pulvermetallurgische Herstellung eines Werkstücks aus einer warmfesten Aluminiumlegierung des Typs AI/Fe/X mit 5 bis 15 Gew.-% Fe, wobei X für das Element V und/oder Mn steht. (Vergl. GB-PS 2 088 409 A).In particular, it relates to the powder-metallurgical production of a workpiece from a heat-resistant aluminum alloy of the type AI / Fe / X with 5 to 15% by weight Fe, where X stands for the element V and / or Mn. (See GB-PS 2 088 409 A).
Aluminiumlegierungen, welche sich für die Erzeugung von Pulvern aus Schmelzen mittels Gasstrahlzerstäubung unter Anwendung sehr hoher Abkühlungsgeschwindigkeiten (105 °C/s und mehr) eignen und für die Herstellung warmfester Werkstücke verwenden lassen, sind in zahlreichen Variationen bekannt geworden. Eine bedeutende Gruppe stellen die polynären, meist relativ hohe Eisengehalte aufweisenden Legierungen des Typs AI/Fe/X dar, wobei X mindestens eines der Elemente Ti, Zr, Hf, V, Nb, Cr, Mo, W, bedeutet. Dabei nimmt offenbar eine Legierung mit 8 Gew.-% Fe und 2 Gew.-% Mo eine Sonderstellung ein (Vergl. GB-PS 2 088 409 A).Aluminum alloys, which are suitable for the production of powders from melts by means of gas jet atomization using very high cooling speeds (105 ° C./s and more) and can be used for the production of heat-resistant workpieces, have become known in numerous variations. An important group are the polynary alloys of the type AI / Fe / X, which generally have relatively high iron contents, where X denotes at least one of the elements Ti, Zr, Hf, V, Nb, Cr, Mo, W. An alloy with 8% by weight Fe and 2% by weight Mo apparently occupies a special position (cf. GB-PS 2 088 409 A).
Es wird ganz allgemein versucht, bei diesen Aluminiumlegierungen Ausscheidungs- und/oder Dispersionshärtung aufeinander abzustimmen und zu optimieren. Dabei spielen binäre und ternäre intermetallische Verbindungen eine wesentliche Rolle. In diesem Zusammenhang wird oft auf die intermetallische Verbindung AI3Fe als wichtige konstituierende Phase und auf ein im Pulverkorn bei hoher Abkühlungsgeschwindigkeit gebildetes Mikro-Eutektikum hingewiesen (Vergl. C.M. Adam and R.G. Bourdeau in: R. Mehrabian et al, eds., Rapid Solidification Processing, Batou Rouge, 1980, p. 246; C.M. Adam in: B.H. Kear et al, eds., "Rapidly Solidified Amorphous and Crystalline Alloys", 1982; W.J. Boettinger, L. Bendersky, J.G. Early, submitted to Met. Trans A (1985) und M.J. Couper and R.F. Singer in: M. Koczak and G. Hildeman (eds.), Conference proceedings, High Strength PM Aluminium Alloys, 1985, in Press.).In general, attempts are made to coordinate and optimize precipitation and / or dispersion hardening in these aluminum alloys. Binary and ternary intermetallic compounds play an important role in this. In this context, reference is often made to the intermetallic compound AI 3 Fe as an important constituent phase and to a micro-eutectic formed in the powder grain at a high cooling rate (see CM Adam and RG Bourdeau in: R. Mehrabian et al, eds., Rapid Solidification Processing, Batou Rouge, 1980, p. 246; CM Adam in: BH Kear et al, eds., "Rapidly Solidified Amorphous and Crystalline Alloys", 1982; WJ Boettinger, L. Bendersky, JG Early, submitted to Met. Trans A (1985) and MJ Couper and RF Singer in: M. Koczak and G. Hildeman (eds.), Conference proceedings, High Strength PM Aluminum Alloys, 1985, in Press.).
Die Eigenschaften der bekannten Legierungen und der daraus nach pulvermetallurgischen Methoden erzeugten Press- und Formkörper lassen noch zu wünschen übrig. Insbesondere ist die Zähigkeit und die Duktilität derartiger Werkstücke für viele Verwendungen ungenügend.The properties of the known alloys and the pressed and molded bodies produced from them using powder metallurgical methods leave something to be desired. In particular, the toughness and ductility of such workpieces is insufficient for many uses.
Es besteht daher ein grosses Bedürfnis, bekannte Legierungen weiterhin zu verbessern und die Herstellungsmethoden für Fertigerzeugnisse zu verfeinern.There is therefore a great need to further improve known alloys and to refine the manufacturing methods for finished products.
Der Erfindung liegt die Aufgabe zugrunde, ein Verfahren zur pulvermetallurgischen Herstellung eines Werkstücks aus einer warmfesten Aluminiumlegierung unter Berücksichtigung optimaler Legierungszusammensetzung und Anpassung der Verfahrensschritte anzugeben, welches zu zäheren und duktileren Fertigerzeugnissen ohne Einbusse an Festigkeit führt. Dabei sollen bei der Pulverherstellung auch bei höheren Temperaturen. stabile Phasen erzielt werden, welche - unabhängig von der Partikelgrösse - über das ganze Pulverkorn homogen verteilt sind und ihm eine hohe Verformbarkeit verleihen.The invention has for its object to provide a method for powder metallurgical production of a workpiece from a heat-resistant aluminum alloy taking into account the optimum alloy composition and adaptation of the process steps, which leads to tougher and more ductile finished products without sacrificing strength. In doing so, powder production should also be carried out at higher temperatures. stable phases are achieved, which - regardless of the particle size - are homogeneously distributed over the whole powder grain and give it a high deformability.
Diese Aufgabe wird dadurch gelöst, dass beim eingangs erwähnten Verfahren eine Legierung gewählt wird, die 8 bis 14 Gew.-% Fe, 0,5 bis 2 Gew.-% V und 0,2 bis 1 Gew.-% Mn, Rest Aluminium und allfällige Verunreinigungen enthält, wobei die Legierung erschmolzen, die Schmelze unter einer Abkühlungsgeschwindigkeit von mindestens 105 °C/s in einem Gasstrom zu Partikeln mit einem Durchmesser von 1 bis 40 11m zerstäubt wird, wobei die dabei gebildeten Dispersoide homogen verteilt und keine mikro-eutektische Zone innerhalb eines Pulverpartikels vorhanden ist, und dass das Pulver bei einer Temperatur von 350 bis 450°C unter einem Druck von 2000 bis 6000 bar dergestalt verdichtet wird, dass die intermetallische, durch Mn stabilisierte Phase AI6Fe in feiner Verteilung gebildet und die Phase AI3Fe weitgehend unterdrückt wird.This object is achieved in that in the method mentioned at the outset an alloy is selected which contains 8 to 14% by weight Fe, 0.5 to 2% by weight V and 0.2 to 1% by weight Mn, the rest being aluminum and contains any impurities, the alloy being melted, the melt being atomized at a cooling rate of at least 105 ° C./s in a gas stream to give particles with a diameter of 1 to 40 11 m, the dispersoids formed thereby being homogeneously distributed and not micro-eutectic Zone is present within a powder particle, and that the powder is compacted at a temperature of 350 to 450 ° C under a pressure of 2000 to 6000 bar in such a way that the intermetallic phase stabilized by Mn forms Al 6 Fe in fine distribution and the phase AI 3 Fe is largely suppressed.
Die Erfindung wird anhand des nachfolgenden Ausführungsbeispiels erläutert.The invention is explained on the basis of the exemplary embodiment below.
Es wurde eine Legierung der nachfolgenden Zusammensetzung erschmolzen:
- Fe = 10 Gew.-%
- V = 1 Gew.-%
- Mn = 0,5 Gew.-%
- AI = Rest
- Fe = 10% by weight
- V = 1% by weight
- Mn = 0.5% by weight
- AI = rest
Die Schmelze wurde in einer Vorrichtung mittels eines Gasstromes (Stickstoff) unter Wahrung einer Abkühlungsgeschwindigkeit von mindestens 105 °C/s zu einem Pulver zuerstäubt. Der mittlere Partikeldurchmesser betrug ca. 20 µm, der maximale ca. 40 µm. Die Struktur der Partikel war durch eine gleichmässige Verteilung der Dispersoide gekennzeichnet, während das sonst bei herkömmlichen Legierungen auftretende störende Mikro-Eutektikum fehlte.The melt was first atomized in a device by means of a gas stream (nitrogen) while maintaining a cooling rate of at least 105 ° C./s to a powder. The average particle diameter was approx. 20 µm, the maximum approx. 40 µm. The structure of the particles was characterized by an even distribution of the dispersoids, while the disruptive micro-eutectic that otherwise occurs with conventional alloys was missing.
Ca. 160 g des Pulvers wurden durch Heisspressen in einer Form unter einem Druck von 3000 bar bei einer Temperatur von 400°C zu einem Pressbolzen von ca. 99 % theoretischer Dichte verdichtet. Die Aufheizzeit in der Form betrug dabei ca. 45 min. Der Pressbolzen hatte einen Durchmesser von 40 mm und eine Höhe von 60 mm. Dieser Pressbolzen wurde in den Zylinder einer Strangpresse eingesetzt und unter einem Druck von 5000 bar bei einer Temperatur von 400°C zu einer Stange von 13 mm Durchmesser verpresst. Das Reduktionsverhältnis betrug ca. 9:1.Approx. 160 g of the powder were compacted by hot pressing in a mold under a pressure of 3000 bar at a temperature of 400 ° C. to a press bolt of approximately 99% theoretical density. The heating time in the mold was about 45 minutes. The press bolt had a diameter of 40 mm and a height of 60 mm. This press bolt was inserted into the cylinder of an extrusion press and pressed under a pressure of 5000 bar at a temperature of 400 ° C to a rod of 13 mm in diameter. The reduction ratio was approximately 9: 1.
Aus der Stange wurden Probestücke herausgeschnitten und die mechanischen Eigenschaften bei Raumtemperatur und bei 300°C gemessen. Die Streckgrenze bei Raumtemperatur betrug 450 MPa. Eine metallographische Untersuchung ergab das Vorhandensein beträchtlicher Volumenanteile der Phase Al6Fe während praktisch kein AI3Fe festgestellt werden konnte. Ferner waren keine nicht-deformierten, AI3Fe enthaltenden Pulverpartikel im verdichteten Material vorhanden.Test pieces were cut out of the bar and the mechanical properties measured at room temperature and at 300 ° C. The yield point at room temperature was 450 MPa. A metallographic examination revealed the presence of considerable volume fractions of the Al 6 Fe phase, while practically no Al 3 Fe could be found. Furthermore, there were no non-deformed powder particles containing Al 3 Fe in the compacted material.
Die Erfindung ist nicht auf das Ausführungsbeispiel beschränkt. Die Aluminiumlegierung kann grundsätzlich folgende Zusammensetzung haben:
- Fe = 8 bis 14 Gew.-%
- (vorzugsweise 10 bis 14 Gew.-%)
- V = 0,5 bis 2 Gew.-%
- Mn = 0,2 bis 1 Gew.-%
- AI = Rest.
- Fe = 8 to 14% by weight
- (preferably 10 to 14% by weight)
- V = 0.5 to 2% by weight
- Mn = 0.2 to 1% by weight
- AI = rest.
Die Abkühlungsgeschwindigkeit bei der Pulverherstellung soll mindestens 105 °C/s betragen. Der Partikeldurchmesser des durch Gasstrahl-Zerstäubung hergestellten Pulvers soll sich innerhalb der Grenzen 1 bis 40 µm bewegen. Die Verdichtung des Pulvers kann bei Temperaturen zwischen 350 und 450°C unter Drücken von 2000 bis 6000 bar erfolgen. Bevorzugte Werte sind 400°C für die Pulververdichtung.The cooling rate during powder production should be at least 10 5 ° C / s. The particle diameter of the powder produced by gas jet atomization should be within the limits of 1 to 40 µm. The powder can be compressed at temperatures between 350 and 450 ° C under pressures of 2000 to 6000 bar. Preferred values are 400 ° C for powder compaction.
Weitere vorteilhafte Legierungszusammensetzungen sind:
- Fe = 10 bis 12 Gew.-%
- V = 1 Gew.-%
- Mn = 0,4 bis 1,0 Gew.-%
- AI = Rest,
- oder:
- Fe = 12 Gew.-%
- V = 1,5 Gew.-%
- Mn =1,0 Gew.-%
- AI = Rest.
- Fe = 10 to 12% by weight
- V = 1% by weight
- Mn = 0.4 to 1.0% by weight
- AI = rest,
- or:
- Fe = 12% by weight
- V = 1.5% by weight
- Mn = 1.0% by weight
- AI = rest.
Claims (6)
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CH3232/86 | 1986-08-12 | ||
| CH3232/86A CH673242A5 (en) | 1986-08-12 | 1986-08-12 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP0256449A1 EP0256449A1 (en) | 1988-02-24 |
| EP0256449B1 true EP0256449B1 (en) | 1990-05-16 |
Family
ID=4251507
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP87111462A Expired - Lifetime EP0256449B1 (en) | 1986-08-12 | 1987-08-07 | Powder-metallurgical manufacture of work pieces from a heat-resisting aluminium alloy |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US4737339A (en) |
| EP (1) | EP0256449B1 (en) |
| JP (1) | JPS6347343A (en) |
| CH (1) | CH673242A5 (en) |
| DE (1) | DE3762756D1 (en) |
| DK (1) | DK415787A (en) |
| NO (1) | NO873365L (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CH673240A5 (en) * | 1986-08-12 | 1990-02-28 | Bbc Brown Boveri & Cie | |
| FR2636974B1 (en) * | 1988-09-26 | 1992-07-24 | Pechiney Rhenalu | ALUMINUM ALLOY PARTS RETAINING GOOD FATIGUE RESISTANCE AFTER EXTENDED HOT HOLDING AND METHOD FOR MANUFACTURING SUCH PARTS |
| EP0577436B1 (en) * | 1992-07-02 | 1997-12-03 | Sumitomo Electric Industries, Limited | Nitrogen-combined aluminum sintered alloys and method of producing the same |
| JPH08325660A (en) * | 1995-05-31 | 1996-12-10 | Ndc Co Ltd | Porous aluminum sintered material |
| US7794520B2 (en) * | 2002-06-13 | 2010-09-14 | Touchstone Research Laboratory, Ltd. | Metal matrix composites with intermetallic reinforcements |
| CN1658989A (en) * | 2002-06-13 | 2005-08-24 | 塔奇斯通研究实验室有限公司 | Metal matrix composites with intermetallic reinforcements |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2311391A1 (en) * | 1975-05-14 | 1976-12-10 | Pechiney Aluminium | ELECTRICAL CONDUCTORS IN AL FE ALLOYS OBTAINED BY SHELL SPINNING |
| US4347076A (en) * | 1980-10-03 | 1982-08-31 | Marko Materials, Inc. | Aluminum-transition metal alloys made using rapidly solidified powers and method |
| US4647321A (en) * | 1980-11-24 | 1987-03-03 | United Technologies Corporation | Dispersion strengthened aluminum alloys |
| US4435213A (en) * | 1982-09-13 | 1984-03-06 | Aluminum Company Of America | Method for producing aluminum powder alloy products having improved strength properties |
| DE3524276A1 (en) * | 1984-07-27 | 1986-01-30 | BBC Aktiengesellschaft Brown, Boveri & Cie., Baden, Aargau | Aluminium alloy for producing ultrafine-grained powder having improved mechanical and microstructural properties |
| US4734130A (en) * | 1984-08-10 | 1988-03-29 | Allied Corporation | Method of producing rapidly solidified aluminum-transition metal-silicon alloys |
-
1986
- 1986-08-12 CH CH3232/86A patent/CH673242A5/de not_active IP Right Cessation
-
1987
- 1987-08-07 DE DE8787111462T patent/DE3762756D1/en not_active Expired - Fee Related
- 1987-08-07 EP EP87111462A patent/EP0256449B1/en not_active Expired - Lifetime
- 1987-08-10 DK DK415787A patent/DK415787A/en not_active Application Discontinuation
- 1987-08-11 US US07/084,017 patent/US4737339A/en not_active Expired - Fee Related
- 1987-08-11 NO NO873365A patent/NO873365L/en unknown
- 1987-08-12 JP JP62201686A patent/JPS6347343A/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| DE3762756D1 (en) | 1990-06-21 |
| NO873365D0 (en) | 1987-08-11 |
| EP0256449A1 (en) | 1988-02-24 |
| JPS6347343A (en) | 1988-02-29 |
| US4737339A (en) | 1988-04-12 |
| DK415787A (en) | 1988-02-13 |
| DK415787D0 (en) | 1987-08-10 |
| NO873365L (en) | 1988-02-15 |
| CH673242A5 (en) | 1990-02-28 |
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