EP0587960B1 - Herstellung von Eisenaluminid-Werkstoffen - Google Patents
Herstellung von Eisenaluminid-Werkstoffen Download PDFInfo
- Publication number
- EP0587960B1 EP0587960B1 EP92810713A EP92810713A EP0587960B1 EP 0587960 B1 EP0587960 B1 EP 0587960B1 EP 92810713 A EP92810713 A EP 92810713A EP 92810713 A EP92810713 A EP 92810713A EP 0587960 B1 EP0587960 B1 EP 0587960B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- temperature
- dispersoids
- dispersoid
- rolling
- 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.)
- Expired - Lifetime
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0068—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only nitrides
Definitions
- the invention relates to a method for producing Iron aluminide materials and according to the process manufactured materials.
- Iron aluminides which mainly consist of Fe 3 Al, are characterized by an ordered crystal structure with DO 3 symmetry: half of the lattice sites that form a cubic lattice are occupied by Fe atoms; the other half of the lattice sites, which are centered on the cubes of the first lattice, have a checkerboard arrangement of Fe and Al atoms.
- the iron aluminide base alloy is an ordered intermetallic alloy. It is called Fe 3 Al-based alloy in the following.
- the Fe 3 Al-based alloy also has a B2 structure (or CsCl structure) or a disordered body-centered Alfa structure.
- Fe 3 Al-based alloys In the case of known Fe 3 Al-based alloys to which up to 10 at.% Chromium and small amounts of molybdenum, niobium, zirconium, yttrium, vanadium, carbon and / or boron are mixed, no low-melting eutectics are formed.
- Fe 3 Al-based alloys have a protective aluminum oxide layer covering the surface.
- iron aluminides and many of the Fe 3 Al-based alloys have a very low ductility at room temperature. Only when the great brittleness of these materials can be overcome can they be used as materials.
- Ductility can usually be improved if the graininess of the structure is refined using alloy additives.
- alloy additives are known, for example, from US-A-3 026 197 and US-A-5 084 109.
- a Fe 3 Al-based alloy is known from a publication (SADavid et al (1989), Welding Research Sup., P.372), in which an increase in ductility at room temperature has been achieved by adding titanium diboride (TiB 2 ) .
- TiB 2 titanium diboride
- heat cracking was observed in welding tests (with electron beam, arc). Investigations with secondary ion mass spectrometry showed that enriched boron and titanium occur on the crack surface.
- the titanium diboride dissolves in the melt; it has no influence on the grain formation. Titanium and boron are not incorporated into the crystal structure of the grains, so these components can finally be found at the grain interfaces after the Fe 3 Al-based alloy has solidified. Due to the influence of heat during welding, the adhesion between neighboring grains is greatly reduced due to the titanium diboride (due to the local melting point lowering at the grain boundaries), which can result in heat cracking. As a result, it is advisable not to add titanium diboride or substances that lead to similar phenomena, despite the improvement in ductility.
- the dispersoids must be very small (in the range of 100 nm), it is recommended to pass these particles through Precipitate from the melt.
- To components of the dispersoid compound are mixed in the melt to which ones go into solution first. While a hold time between 100 and 1000 seconds then the dissolved components together, whereby it precipitates the dispersoid-shaped compound form.
- dispersoids were obtained with a size distribution in which the dispersoid diameters are mostly between 50 and 200 nm.
- the alloy FA-129 known from WO 90/10722 composition: 28% Al, 5% Cr, 0.5% Nb, 0.2% C, rest Fe) was used as the starting alloy.
- the melt has a considerable increase in its viscosity due to the dispersoids. For this reason, the melt must be poured when the superheat is relatively high (around 200 K) - in contrast to the pouring of the dispersoid-free melt. As a result, the microstructural grains of small samples, despite the dispersoids, turn out to be roughly the same size as the original Fe 3 Al-based alloy; in the case of large castings, even much larger grains form.
- Metallurgical studies have shown that dispersoids are embedded in the monocrystalline phase thanks to the good coherence of the crystal structures. When forming by hot rolling, the grains formed during solidification are reduced to fine grains by breaking up new grain boundaries at the points where the dispersoids are embedded in the phase. Annealing the hot-rolled alloy at temperatures between 800 and 1000 ° C results in a stable high-temperature material.
- dispersion hardening also takes place. This is confirmed by hardness measurements.
- the hardness (Vickers hardness HV, test load 1 kg) is 260 after casting, 280 after hot rolling (900 ° C, 90%) and further 280 after annealing (600 ° C, 24 h) ; the corresponding values for the dispersoid-free alloy are: 230, 275 and 255. Thanks to the dispersion hardening, the creeping capacity of the material is advantageously reduced.
- FIG. 1 is shown in FIG schematic form and on a smaller scale in Fig.2 recognizable.
- the square section 2 in Fig.1 is shown enlarged in Fig.3.
- the dispersoids unfold an important one Effect: As with hot rolling from 1 to 2 kg heavy, dispersoid-containing castings, grains that are 25 microns wide (and 0.5 mm long), while the corresponding transformation at a particle-free alloy to 60 micron grains Width (length also 0.5 mm) leads. After this Hot rolling are the grains of the invention Material significantly finer than that of the dispersoid-free Alloy, despite the fact that after the Pour the conditions were just reversed.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Powder Metallurgy (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Description
- Fig. 1
- eine Probe einer erfindungsgemässen Legierung (500-fach vergrössert, nach einem Rasterelektronenmikroskopie-Bild gezeichnet),
- Fig. 2
- eine schematische Darstellung der gleichen Probe wie in Fig.1, bei kleinerer Vergrösserung (200-fach), und
- Fig. 3
- einen Ausschnitt aus der Probe von Fig.1 mit Dispersoiden (5000-fach vergrössert).
Claims (6)
- Verfahren zum Herstellen von Eisenaluminid-Werkstoffen aus einer Fe3Al-Basis-Legierung mit 18-35 at% Al, mit 3-15 at% Cr, mit 0.2-0.5 at% B und/oder C, und mit gesamthaft 0-8 at% folgender Legierungszusätze, Mo, Nb, Zr, Y, und/oder V, sowie mit Fe als vorherrschendem Rest, welches Verfahren folgende Schritte umfasst:Schmelzen der Legierung im Vakuum,Herstellen einer Schutzgasatmosphäre über der Schmelze, mit einem Gasdruck zwischen 0.2 und 1 bar,Zugeben von Ti, Zr und eine N-haltige Fe-Cr-Legierung bei einer Temperatur 200 - 400 K über der Liquidustemperatur zur Bildung von 2 - 10 Volumenprozent (Ti,Zr)N-Dispersoiden,Abpumpen des Schutzgases nach einer zwischen 100 und 1000 s dauernden Haltezeit,Giessen der dispersoidhaltigen Schmelze bei einer Temperatur, die 100 - 200 K über der Liquidustemperatur liegt, und Erstarrenlassen,Warmwalzen bei einer Temperatur zwischen 650 und 1000°C, wobei bis zu einer Querschnittsreduktion von mindestens 80% gewalzt wird.
- Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass nach dem Warmwalzen die Legierung bei einer Temperatur zwischen 400 und 1000°C geglüht wird.
- Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, und dass bei rund 900°C gewalzt wird.
- Verfahren nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass anschliessend an das Walzen während rund 24 Stunden bei rund 600°C geglüht wird.
- Werkstoff, hergestellt nach einem der Verfahren gemäss einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass der kleinste Durchmesser der Gefügekörner kleiner als rund 30 Mikrometer ist.
- Werkstoff nach Anspruch 5, dadurch gekennzeichnet, dass als Ausganglegierung die dispersoidfreie Fe3Al-Basis-Legierung aus 26-30 at% Al, 3-10 at% Cr, 0.3-0.8 at% Nb, 0.1-0.5 at% C, Rest Fe verwendet wurde.
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT92810713T ATE166112T1 (de) | 1992-09-16 | 1992-09-16 | Herstellung von eisenaluminid-werkstoffen |
DE59209325T DE59209325D1 (de) | 1992-09-16 | 1992-09-16 | Herstellung von Eisenaluminid-Werkstoffen |
EP92810713A EP0587960B1 (de) | 1992-09-16 | 1992-09-16 | Herstellung von Eisenaluminid-Werkstoffen |
US08/120,718 US5346562A (en) | 1992-09-16 | 1993-09-13 | Method of production of iron aluminide materials |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP92810713A EP0587960B1 (de) | 1992-09-16 | 1992-09-16 | Herstellung von Eisenaluminid-Werkstoffen |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0587960A1 EP0587960A1 (de) | 1994-03-23 |
EP0587960B1 true EP0587960B1 (de) | 1998-05-13 |
Family
ID=8211992
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP92810713A Expired - Lifetime EP0587960B1 (de) | 1992-09-16 | 1992-09-16 | Herstellung von Eisenaluminid-Werkstoffen |
Country Status (4)
Country | Link |
---|---|
US (1) | US5346562A (de) |
EP (1) | EP0587960B1 (de) |
AT (1) | ATE166112T1 (de) |
DE (1) | DE59209325D1 (de) |
Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE19603515C1 (de) * | 1996-02-01 | 1996-12-12 | Castolin Sa | Spritzwerkstoff auf Eisenbasis zum Herstellen einer korrosionsbeständigen Beschichtung, Herstellungsverfahren für die Beschichtung sowie Verwendung der Schicht |
DE19735217B4 (de) * | 1997-08-14 | 2004-09-09 | SCHWäBISCHE HüTTENWERKE GMBH | Verbundwerkstoff mit hohem Anteil intermetallischer Phasen, vorzugsweise für Reibkörper |
US6030472A (en) | 1997-12-04 | 2000-02-29 | Philip Morris Incorporated | Method of manufacturing aluminide sheet by thermomechanical processing of aluminide powders |
US6114058A (en) * | 1998-05-26 | 2000-09-05 | Siemens Westinghouse Power Corporation | Iron aluminide alloy container for solid oxide fuel cells |
US6816934B2 (en) * | 2000-12-22 | 2004-11-09 | Hewlett-Packard Development Company, L.P. | Computer system with registered peripheral component interconnect device for processing extended commands and attributes according to a registered peripheral component interconnect protocol |
US6524405B1 (en) * | 2000-02-11 | 2003-02-25 | Hui Lin | Iron base high temperature alloy |
DE102009020922A1 (de) | 2009-05-12 | 2010-11-18 | Christoph Henrik Sterzel | Die Anwendung von niedrigviskosem Schwefel als Wärmeträger- und Wärmespeicherflüssigkeit |
EP2733829A1 (de) * | 2012-11-15 | 2014-05-21 | Siemens Aktiengesellschaft | Bauteil für eine dynamoelektrische Maschine |
AT513255B1 (de) * | 2012-12-28 | 2014-03-15 | Miba Gleitlager Gmbh | Mehrschichtgleitlager |
CN108603257B (zh) * | 2016-01-20 | 2021-02-26 | 蒂森克虏伯钢铁欧洲股份公司 | 扁钢产品和其生产方法 |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US1990650A (en) * | 1932-06-25 | 1935-02-12 | Smith Corp A O | Heat resistant alloy |
US2726952A (en) * | 1954-05-05 | 1955-12-13 | Ford Motor Co | Method of preparation of iron aluminum alloys |
US2768915A (en) * | 1954-11-12 | 1956-10-30 | Edward A Gaughler | Ferritic alloys and methods of making and fabricating same |
US3026197A (en) * | 1959-02-20 | 1962-03-20 | Westinghouse Electric Corp | Grain-refined aluminum-iron alloys |
US4961903A (en) * | 1989-03-07 | 1990-10-09 | Martin Marietta Energy Systems, Inc. | Iron aluminide alloys with improved properties for high temperature applications |
US5084109A (en) * | 1990-07-02 | 1992-01-28 | Martin Marietta Energy Systems, Inc. | Ordered iron aluminide alloys having an improved room-temperature ductility and method thereof |
DE59007276D1 (de) * | 1990-07-07 | 1994-10-27 | Asea Brown Boveri | Oxydations- und korrosionsbeständige Legierung für Bauteile für einen mittleren Temperaturbereich auf der Basis von dotiertem Eisenaluminid Fe3Al. |
-
1992
- 1992-09-16 AT AT92810713T patent/ATE166112T1/de not_active IP Right Cessation
- 1992-09-16 EP EP92810713A patent/EP0587960B1/de not_active Expired - Lifetime
- 1992-09-16 DE DE59209325T patent/DE59209325D1/de not_active Expired - Fee Related
-
1993
- 1993-09-13 US US08/120,718 patent/US5346562A/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
EP0587960A1 (de) | 1994-03-23 |
ATE166112T1 (de) | 1998-05-15 |
DE59209325D1 (de) | 1998-06-18 |
US5346562A (en) | 1994-09-13 |
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