EP2031080A1 - High temperature alloy - Google Patents
High temperature alloy Download PDFInfo
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- EP2031080A1 EP2031080A1 EP08163031A EP08163031A EP2031080A1 EP 2031080 A1 EP2031080 A1 EP 2031080A1 EP 08163031 A EP08163031 A EP 08163031A EP 08163031 A EP08163031 A EP 08163031A EP 2031080 A1 EP2031080 A1 EP 2031080A1
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 50
- 239000000956 alloy Substances 0.000 title claims abstract description 50
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract 3
- 238000000034 method Methods 0.000 claims abstract 2
- 239000000203 mixture Substances 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 229910052715 tantalum Inorganic materials 0.000 claims description 6
- 230000001681 protective effect Effects 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 abstract description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 2
- 229910052796 boron Inorganic materials 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 238000002844 melting Methods 0.000 abstract description 2
- 230000008018 melting Effects 0.000 abstract description 2
- 229910052727 yttrium Inorganic materials 0.000 abstract description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 abstract 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 abstract 1
- 238000005275 alloying Methods 0.000 abstract 1
- 239000011651 chromium Substances 0.000 abstract 1
- 238000005096 rolling process Methods 0.000 abstract 1
- 239000010703 silicon Substances 0.000 abstract 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 abstract 1
- 239000000463 material Substances 0.000 description 28
- 230000003647 oxidation Effects 0.000 description 17
- 238000007254 oxidation reaction Methods 0.000 description 17
- 229910000953 kanthal Inorganic materials 0.000 description 8
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 4
- 229910001175 oxide dispersion-strengthened alloy Inorganic materials 0.000 description 4
- 239000000470 constituent Substances 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910017060 Fe Cr Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000003993 interaction Effects 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000000567 combustion gas Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 239000004848 polyfunctional curative Substances 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000005486 sulfidation Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
Definitions
- the invention relates to the field of materials technology. It relates to a high-temperature iron-based alloy containing about 20% by weight of Cr and several parts by weight of Al and minor amounts of other constituents, and which have good mechanical properties and very good oxidation resistance at service temperatures of up to 1000 ° C.
- ODS oxide-dispersion-strengthened, oxide dispersion strengthened
- iron z. B. ferritic ODS FeCrAI alloys
- They are due to their excellent mechanical properties at high temperatures preferred for thermally and mechanically highly stressed components, eg. B. for gas turbine blades used.
- thermocouple protection tubes used, for example, in temperature control gas turbine sequential combustion gas turbines where they are exposed to extremely high temperatures and oxidizing atmospheres.
- Table 1 sets forth the nominal chemical compositions (in weight%): Table 1: Nominal composition of known ODS-FeCrAlTi alloys component Fe Cr al Ti Si Addition of reactive elements (in the form of an oxide dispersion) alloy designation Kanthal APM rest 20.0 5.5 12:03 12:23 ZrO 2 -Al 2 O 3 MA 956 rest 20.0 4.5 0.5 - Y 2 O 3 -Al 2 O 3 PM 2000 rest 20.0 5.5 0.5 - Y 2 O 3 -Al 2 O 3
- the materials mentioned have very high creep ruptures at very high temperatures and also excellent high-temperature oxidation resistance by forming an Al 2 O 3 protective film, as well as a high resistance to sulfidation and steam oxidation. They have strong directional characteristics. For example, in pipes, the creep strength in the transverse direction is only about 50% of the creep strength in the longitudinal direction.
- the aim of the invention is to avoid the mentioned disadvantages of the prior art.
- the invention is based on the object to develop a suitable material for the above applications, which is less expensive than the known from the prior art material PM 2000, but has at least as good oxidation resistance.
- the material according to the invention should be readily thermoformable and should have better mechanical properties than z.
- KANTHAL APM which is used for heating elements.
- the alloy preferably contains 5 to 6% by weight of Al, particularly preferably 5.5 to 6% by weight of Al. This forms a good Al 2 O 3 protective film on the material surface which enhances the high temperature oxidation resistance.
- the material according to the invention particularly preferably comprises 2-4% by weight of Mo and / or 2-4% by weight of Ta.
- Ta, Zr and B are elements which act as precipitation strengthening agents.
- Table 2 Compositions of the investigated alloys according to the invention component Fe Cr al Ta Not a word Zr B Y Si alloy designation 2007 rest 20 5.5 4 - 0.2 12:05 0.1 - 2008 rest 20 5.5 - 4 0.2 12:05 0.1 - 2009 rest 20 8th - 4 0.2 12:05 0.1 - 2010 rest 20 6 - 8th 0.2 12:05 0.1 - 2011 rest 20 5.5 - 4 0.2 12:05 0.1 0.5 2012 rest 20 6 2 2 0.2 12:05 0.1 - 2013 rest 20 6 4 4 0.2 12:05 0.1 - 2014 rest 20 6 - 4 0.2 12:05 0.1 0.5 2015 rest 20 5.5 4 4 0.2 12:05 0.1 - 2016 rest 20 5.5 - 4 0.2 12:05 0.1 12:25
- novel alloys were prepared by arc melting the specified elements and then rolled at temperatures of 900-800 ° C before, inter alia, the tensile specimens were prepared.
- Fig. 1 For the alloys listed, the weight change at 1100 ° C over time over a period of 12 hours is shown.
- the alloy according to the invention 2008 (inter alia with 4% Mo and 5.5% Al) shows about a comparable oxidation behavior as the comparative alloy PM 2000 and is even better with the long removal times (lower weight change), while the alloy 2009 (inter alia with 4% Mo and 8% Al) is worst in this respect and can not reach the values of PM 2000 at these temperatures. This is due to the comparatively high aluminum content, the 8% by weight of Al being the maximum value, the optimum being 5 to 6% by weight of Al.
- Fig. 2 For the specified alloys, the weight change at 1000 ° C in air over time over a period of 1000 hours is shown. It turns out that the two inventive alloys 2014 and 2013, but especially the alloy 2013, have a significantly improved oxidation behavior. After 1000 hours of aging in air at 1000 ° C, the weight changes in the two inventive alloys only one-third (alloy 2013) to less than half (alloy 2014) of the weight change compared to the known alloy PM 2000. Apparently affects a combination of Mo and Ta in equal proportions particularly well on the oxidation behavior at 1000 ° C from. In particular, Ta increases the activity of Al in the given range and improves the oxidation resistance.
- FIGS. 3 to 5 the results of tensile tests in the temperature range from room temperature to 1000 ° C are shown.
- Fig. 3 shows the dependence of the tensile strength on the temperature of the specified materials. At room temperature, the values of the investigated materials are relatively close to each other. Some of the materials according to the invention (eg alloys 2007 and 2013) are stronger at room temperature than those known from the prior art Materials), in others there are hardly any differences to the well-known alloys PM 2000 and Kanthal APM.
- the tensile strength values remain approximately constant as a function of the temperature, then they drop markedly as expected.
- the inventive alloys investigated invariably have higher tensile strengths than Kanthal APM and somewhat lower tensile strengths than PM 2000. However, this is associated with the excellent oxidation behavior of these alloys at 1000 ° C. (see Fig. 2 ), then these are very good property combinations.
- Fig. 4 the dependence of the yield strength on the temperature is shown. The tendency corresponds approximately to the course of the tensile strength according to Fig. 3 ,
- Fig. 5 finally shows the dependence of the elongation at break of the temperature in the range from room temperature to 1000 ° C.
- the elongation at break values in the range from RT to 400 ° C. are approximately constant, at 600 ° C. the maximum value is twice the value compared with RT, then the elongation at break values decrease with increasing temperature until at 1000 ° C. approx. half of the value is reached at RT.
- the increase in ductility of PM 2000 at about 600 ° C is due to the softening of the material.
- novel materials can also be hot rolled well, they have a good plastic deformability.
- thermocouple thermowell They are very useful as a thermocouple thermowell, the latter being used, for example, in gas turbines with sequential combustion for temperature control where they are exposed to oxidizing atmospheres.
- the alloys according to the invention have a very high oxidation resistance at 1000 ° C. They have better mechanical properties than the Kanthal APM alloy known from the prior art. Although the strength values of the alloys according to the invention are somewhat lower at high temperatures than those of the alloy PM 2000, the ductility is considerably better for this purpose. Moreover, at 1000 ° C., the oxidation resistance is more than twice as high as in PM 2000. Since the alloys according to the invention are also cheaper than PM 2000 (cheaper components, easier production), they are outstandingly suitable as a replacement for PM 2000 for the fields of application described above.
Abstract
Description
Die Erfindung bezieht sich auf das Gebiet der Werkstofftechnik. Sie betrifft eine Hochtemperaturlegierung auf Eisenbasis, welche ca. 20 Gew. -% Cr und mehrere Gew. -% Al sowie geringfügige Mengen anderer Bestandteile enthalten, und welche bei Einsatztemperaturen bis zu 1000 °C gute mechanische Eigenschaften und einen sehr guten Oxidationswiderstand aufweisen.The invention relates to the field of materials technology. It relates to a high-temperature iron-based alloy containing about 20% by weight of Cr and several parts by weight of Al and minor amounts of other constituents, and which have good mechanical properties and very good oxidation resistance at service temperatures of up to 1000 ° C.
Seit einiger Zeit sind ODS (oxide-dispersion-strengthened, oxiddispersionsverfestigte) Werkstoffe auf Eisenbasis, z. B. ferritische ODS-FeCrAI-Legierungen, bekannt. Sie werden aufgrund ihrer hervorragenden mechanischen Eigenschaften bei hohen Temperaturen bevorzugt für thermisch und mechanisch höchstbeanspruchte Bauteile, z. B. für Gasturbinenschaufeln, verwendet.For some time ODS (oxide-dispersion-strengthened, oxide dispersion strengthened) materials based on iron, z. B. ferritic ODS FeCrAI alloys, known. They are due to their excellent mechanical properties at high temperatures preferred for thermally and mechanically highly stressed components, eg. B. for gas turbine blades used.
Die Anmelderin setzt derartiger Materialien für Rohre zum Schutz von Thermoelementen ein, welche beispielsweise in Gasturbinen mit sequenzieller Verbrennung zur Temperaturkontrolle verwendet werden und dort extrem hohen Temperaturen und oxidierenden Atmosphären ausgesetzt sind.The Applicant employs such materials for thermocouple protection tubes used, for example, in temperature control gas turbine sequential combustion gas turbines where they are exposed to extremely high temperatures and oxidizing atmospheres.
Für bekannte ferritische ODS-Legierungen auf Eisenbasis sind in der Tabelle 1 die nominalen chemischen Zusammensetzungen (in Gew.- %) angegeben:
Die Einsatztemperaturen dieser metallischen Werkstoffe reichen bis ca. 1350°C. Sie haben ein Eigenschaftspotential, welches eher für keramische Werkstoffe typisch ist.The operating temperatures of these metallic materials reach up to 1350 ° C. They have a property potential which is more typical for ceramic materials.
Die genannten Werkstoffe weisen sehr hohe Zeitstandfestigkeiten bei sehr hohen Temperaturen auf und ausserdem eine hervorragende Hochtemperatur-Oxidationsbeständigkeit durch Bildung eines Al2O3-Schutzfilmes, sowie einen hohen Widerstand gegen Sulfidierung und Dampfoxidation. Sie haben stark ausgeprägte richtungsabhängige Eigenschaften. So beträgt beispielsweise in Rohren die Kriechfestigkeit in Querrichtung nur ca. 50 % der Kriechfestigkeit in Längsrichtung.The materials mentioned have very high creep ruptures at very high temperatures and also excellent high-temperature oxidation resistance by forming an Al 2 O 3 protective film, as well as a high resistance to sulfidation and steam oxidation. They have strong directional characteristics. For example, in pipes, the creep strength in the transverse direction is only about 50% of the creep strength in the longitudinal direction.
Die Herstellung solcher ODS-Legierungen erfolgt auf pulvermetallurgischem Wege unter Verwendung mechanisch legierter Pulvermischungen, die auf bekannte Weise, z. B. durch Strangpressen oder durch heissisostatisches Pressen, kompaktiert werden. Anschliessend wird der Pressling stark plastisch verformt, meist durch Warmwalzen, und einer Rekristallisationsglühbehandlung unterworfen. Diese Art der Herstellung, aber auch die beschriebenen Materialzusammensetzungen bedeuten u.a., dass diese Legierungen sehr teuer sind.The production of such ODS alloys by powder metallurgy using mechanically alloyed powder mixtures, the known manner, for. B. by extrusion or by hot isostatic pressing, compacted. Subsequently, the compact is strongly plastically deformed, usually by hot rolling, and subjected to recrystallization annealing. This type of production, but also the material compositions described mean, inter alia, that these alloys are very expensive.
Ziel der Erfindung ist es, die genannten Nachteile des Standes der Technik zu vermeiden. Der Erfindung liegt die Aufgabe zu Grunde, ein für die oben angegebenen Anwendungen geeignetes Material zu entwickeln, welches kostengünstiger als das aus dem Stand der Technik bekannte Material PM 2000 ist, aber einen mindestens ebenso guten Oxidationswiderstand aufweist. Das erfindungsgemässe Material soll ausserdem gut warmumformbar sein und möglichst bessere mechanische Eigenschaften aufweisen als z. B. die bekannte Legierung KANTHAL APM, welche für Heizelemente eingesetzt wird.The aim of the invention is to avoid the mentioned disadvantages of the prior art. The invention is based on the object to develop a suitable material for the above applications, which is less expensive than the known from the prior
Erfindungsgemäss wird dies dadurch erreicht, dass die Hochtemperaturlegierung vom Typ FeCrAl-Legierung folgende chemische Zusammensetzung (Angaben in Gew. -%) aufweist:
- 20 Cr,
- 4-8 Al,
- mindestens eines der Elemente aus der Gruppe Ta und Mo mit insgesamt 4-8,
- 0-0.2 Zr,
- 0.02-0.05 B,
- 0.1-0.2 Y,
- 0-0.5 Si,
- Rest Fe.
- 20 Cr,
- 4-8 Al,
- at least one of the elements from the group Ta and Mo with a total of 4-8,
- 0-0.2 Zr,
- 0.02-0.05 B,
- 0.1-0.2 Y,
- 0-0.5 Si,
- Rest Fe.
Bevorzugt enthält die Legierung 5 bis 6 Gew. -% Al, besonders bevorzugt 5.5 bis 6 Gew.- % Al. Damit wird ein guter Al2O3-Schutzfilm auf der Materialoberfläche gebildet, der die Hochtemperatur-Oxidationsbeständigkeit erhöht.The alloy preferably contains 5 to 6% by weight of Al, particularly preferably 5.5 to 6% by weight of Al. This forms a good Al 2 O 3 protective film on the material surface which enhances the high temperature oxidation resistance.
Weiterhin bevorzugte Bereiche sind 0-8 Gew.- % Mo und 0-4 Gew. -% Ta, wobei gilt, dass die Summe (Mo + Ta) = 4-8 Gew.- % ist, und wobei beispielsweise der Maximalwert von 8 % Mo dem unabhängigen Anspruch 1 entsprechend nur dann gilt, wenn kein Ta vorhanden ist. Besonders bevorzugt weist das erfindungsgemässe Material 2-4 Gew.- % Mo und/oder 2-4 Gew.- % Ta auf.Further preferred ranges are 0-8% by weight of Mo and 0-4% by weight of Ta, with the proviso that the sum (Mo + Ta) = 4-8% by weight, and where, for example, the maximum value of 8 % Mo according to the
Sind die Gehalte von (Ta + Mo) geringer als die angegebenen Werte, dann wird die Hochtemperaturfestigkeit zu stark reduziert, sind sie höher, dann wird in unerwünschter Weise der Oxidationswiderstand reduziert und das Material wird ausserdem zu teuer.If the contents of (Ta + Mo) are lower than the specified values, the high-temperature strength is excessively reduced, if they are higher, the oxidation resistance is undesirably reduced and the material becomes too expensive.
Vorteilhaft ist auch die Zugabe von 0.25, max. 0.5 Gew.- % Si, weil dadurch der Oxidationswiderstand weiter verstärkt wird.Also advantageous is the addition of 0.25, max. 0.5% by weight of Si, because this further enhances the oxidation resistance.
Weiterhin sind bevorzugt 0.2 Gew. -% Zr und 0.1 Gew. -% Y im erfindungsgemässen Material vorhanden.Furthermore, 0.2% by weight of Zr and 0.1% by weight of Y are preferably present in the material according to the invention.
Überraschenderweise hat sich gezeigt, dass es nicht nötig ist, wie es bei den aus dem Stand der Technik bekannten und oben beschriebenen Legierungen der Fall ist, Titan zuzugeben. Ti und Cr wirken als Mischkristall-Verfestiger. Mo hat im Bereich von 2-8 Gew.- % eine ähnliche Wirkung, ist aber wesentlich billiger als Ti. Hinzu kommt, dass Mo, wenn es zusammen mit Zr zugegeben wird, wie es bei der vorliegenden Erfindung bei bevorzugten Ausführungsvarianten der Fall ist, zu verbesserten Zugfestigkeiten und Zeitstandfestigkeiten führt.Surprisingly, it has been found that it is not necessary, as is the case with the alloys known from the prior art and described above, to add titanium. Ti and Cr act as solid solution hardeners. Mo has a similar effect in the range of 2-8% by weight, but is considerably cheaper than Ti. In addition, Mo, when added together with Zr, as in the present invention in preferred embodiments, is the case. leads to improved tensile strength and creep strength.
Ta, Zr und B sind Elemente, welche als Ausscheidungs-Verfestiger wirken. Das Zusammenspiel dieser Bestandteile mit den anderen Bestandteilen, insbesondere dem Cr und dem Mo, sofern letzteres vorhanden ist, führt zu guten Festigkeitswerten, während Al, Y und auch Zr die Oxdationsbeständigkeit erhöhen. Cr beeinflusst positiv die Duktilität.Ta, Zr and B are elements which act as precipitation strengthening agents. The interaction of these constituents with the other constituents, in particular the Cr and the Mo, if present, leads to good strength values, while Al, Y and also Zr increase the oxidation resistance. Cr positively influences ductility.
In den Zeichnungen sind Ausführungsbeispiele der Erfindung dargestellt.In the drawings, embodiments of the invention are shown.
Es zeigen:
- Fig. 1
- das Oxidationsverhalten bei 1100°C/12h für PM 2000 und für ausgewählte erfindungsgemässe Materialien;
- Fig. 2
- das Oxidationsverhalten bei 1000°C an Luft über einen Zeitraum von 1000 Stunden für PM 2000 und für ausgewählte erfindungsgemässe Materialien;
- Fig. 3
- die Zugfestigkeit im Bereich von Raumtemperatur bis 1000°C für PM 2000 und Kanthal APM und für ausgewählte erfindungsgemässe Materialien;
- Fig. 4
- die Streckgrenze im Bereich
von Raumtemperatur bis 1000°C für PM 2000 und für ausgewählte erfindungsgemässe Materialien und - Fig. 5
- die Bruchdehnung im Bereich
von Raumtemperatur bis 1000°C für PM 2000 und für ausgewählte erfindungsgemässe Materialien.
- Fig. 1
- the oxidation behavior at 1100 ° C / 12h for
PM 2000 and for selected materials according to the invention; - Fig. 2
- the oxidation behavior at 1000 ° C in air over a period of 1000 hours for
PM 2000 and for selected materials according to the invention; - Fig. 3
- the tensile strength in the range of room temperature to 1000 ° C for
PM 2000 and Kanthal APM and for selected materials according to the invention; - Fig. 4
- the yield strength in the range of room temperature to 1000 ° C for
PM 2000 and for selected materials according to the invention and - Fig. 5
- the elongation at break in the range of room temperature to 1000 ° C for
PM 2000 and for selected materials according to the invention.
Nachfolgend wird die Erfindung anhand von Ausführungsbeispielen und den Zeichnungen näher erläutert.The invention will be explained in more detail with reference to embodiments and the drawings.
Es wurden die aus dem Stand der Technik bekannten ODS FeCrAl-Vergleichslegierungen PM 2000 und Kanthal APM (Zusammensetzung siehe Tabelle 1), sowie die in Tabelle 2 aufgeführten erfindungsgemässen Legierungen im Hinblick auf das Oxidationsverhalten sowie im Hinblick auf die mechanischen Eigenschaften bei Raumtemperatur (RT) bis zu 1000°C untersucht. Die Legierungsbestandteile sind in Gew.- % angegeben:
Die erfindungsgemässen Legierungen wurden durch Lichtbogenschmelzen der angegebenen Elemente hergestellt und dann bei Temperaturen von 900-800°C gewalzt, bevor u.a. die Zugproben hergestellt wurden.The novel alloys were prepared by arc melting the specified elements and then rolled at temperatures of 900-800 ° C before, inter alia, the tensile specimens were prepared.
In
In
In den
Bis ca. 400°C bleiben die Zugfestigkeitswerte in Abhängigkeit von der Temperatur annährend konstant, danach sinken sie erwartungsgemäss markant ab. Im Temperaturbereich von 900 bis 1000°C weisen die untersuchten erfindungsgemässen Legierungen ausnahmslos höhere Zugfestigkeiten auf als Kanthal APM und etwas niedrigere Zugfestigkeiten als PM 2000. Bringt man das aber in Verbindung mit dem hervorragenden Oxidationsverhalten dieser Legierungen bei 1000°C (siehe
In
Während bei Raumtemperatur die Bruchdehnungen der erfindungsgemässen Legierungen unterhalb der Werte für PM 2000 liegen, sind sie ab ca. 600°C ausnahmslos höher. Dieser positive Effekt ist auf das Zusammenwirken der Materialbestandteile in den vorgegebenen Bereichen zurückzuführen.While at room temperature the elongations at break of the alloys according to the invention are below the values for
Die erfindungsgemässen Materialien lassen sich ausserdem gut warmwalzen, sie weisen eine gute plastische Verformbarkeit auf.The novel materials can also be hot rolled well, they have a good plastic deformability.
Sie sind sehr gut einsetzbar als Schutzrohr für Thermoelemente, wobei letztere beispielsweise in Gasturbinen mit sequentieller Verbrennung zur Temperaturkontrolle verwendet werden und dort oxidierenden Atmosphären ausgesetzt sind.They are very useful as a thermocouple thermowell, the latter being used, for example, in gas turbines with sequential combustion for temperature control where they are exposed to oxidizing atmospheres.
Zusammenfassend ist festzustellen, dass die erfindungsgemässen Legierungen einen sehr hohen Oxidationswiderstand bei 1000°C aufweisen. Sie haben bessere mechanische Eigenschaften als die aus dem Stand der Technik bekannte Legierung Kanthal APM. Die Festigkeitswerte der erfindungsgemässen Legierungen sind zwar bei hohen Temperaturen etwas geringer als diejenigen der Legierung PM 2000, aber dafür ist die Duktilität wesentlich besser. Bei 1000°C ist ausserdem der Oxidationswiderstand mehr als doppelt so hoch als bei PM 2000. Da die erfindungsgemässen Legierungen zudem billiger als PM 2000 sind (billigere Bestandteile, einfachere Herstellung) sind diese für die oben beschriebenen Einsatzgebiete hervorragend als Ersatz für PM 2000 geeignet.In summary, it should be noted that the alloys according to the invention have a very high oxidation resistance at 1000 ° C. They have better mechanical properties than the Kanthal APM alloy known from the prior art. Although the strength values of the alloys according to the invention are somewhat lower at high temperatures than those of the
Claims (13)
Applications Claiming Priority (1)
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CH13552007 | 2007-08-30 |
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EP2031080A1 true EP2031080A1 (en) | 2009-03-04 |
EP2031080B1 EP2031080B1 (en) | 2012-06-27 |
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EP08163031A Active EP2031080B1 (en) | 2007-08-30 | 2008-08-27 | High temperature alloy |
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US (1) | US8435443B2 (en) |
EP (1) | EP2031080B1 (en) |
JP (1) | JP5574588B2 (en) |
CN (1) | CN101476084B (en) |
CA (1) | CA2639255C (en) |
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JP6909806B2 (en) | 2016-04-22 | 2021-07-28 | サンドビック インテレクチュアル プロパティー アクティエボラーグ | Tubes and methods for making tubes |
IT201900003507A1 (en) | 2019-03-11 | 2020-09-11 | Polidoro S P A | PERFECTED TEMPERATURE SENSOR FOR GAS BURNER AND ASSEMBLY OF SUCH SENSOR AND BURNER |
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- 2008-08-29 JP JP2008220844A patent/JP5574588B2/en not_active Expired - Fee Related
- 2008-08-29 CN CN2008101911374A patent/CN101476084B/en not_active Expired - Fee Related
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Also Published As
Publication number | Publication date |
---|---|
EP2031080B1 (en) | 2012-06-27 |
CA2639255C (en) | 2016-08-16 |
US8435443B2 (en) | 2013-05-07 |
JP5574588B2 (en) | 2014-08-20 |
JP2009057633A (en) | 2009-03-19 |
US20090060774A1 (en) | 2009-03-05 |
CN101476084B (en) | 2013-10-23 |
CN101476084A (en) | 2009-07-08 |
CA2639255A1 (en) | 2009-02-28 |
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