EP0774526B1 - Eisen-Nickel-Superlegierung vom Typ IN 706 - Google Patents
Eisen-Nickel-Superlegierung vom Typ IN 706 Download PDFInfo
- Publication number
- EP0774526B1 EP0774526B1 EP96810754A EP96810754A EP0774526B1 EP 0774526 B1 EP0774526 B1 EP 0774526B1 EP 96810754 A EP96810754 A EP 96810754A EP 96810754 A EP96810754 A EP 96810754A EP 0774526 B1 EP0774526 B1 EP 0774526B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- max
- temperatures
- solution
- iron
- alloy
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
Definitions
- the invention relates to a prior art of Iron-nickel superalloys of type IN 706 such as that from J.H. Moll et al. "The Microstructure of 706, a New Fe-Ni Base Superalloy "Met. Trans. 1971, vol.2, pp.2143-2151, and” Heat Treatment of 706 Alloy for Optimum 1200 ° F stress rupture Properties "Met. Trans. 1971, vol. 2, pp.2153-2160, is described.
- the task is an iron-nickel superalloy of type IN 706, which can be found in high heat resistance characterized by great ductility, and at the same time specify a method by which ductility a material body formed from this alloy can also be improved.
- the alloy according to the invention stands out above all in that they are compared to an additive-free iron-nickel superalloy of type IN 706 at only marginally reduced heat resistance practically a double has great long-term ductility.
- Additions to boron and / or hafnium are caused by tension forces supported oxidation of the grain boundaries of the alloy structure reduced. Undesirable material fatigue phenomena, like notch embrittlement and stress crack growth, become so whole significantly reduced.
- This alloy is therefore suitable especially as a material for rotors of large gas turbines.
- the Alloy has a sufficiently high heat resistance. When local temperature gradients occur work because of the high ductility of the alloy undesirable tensile forces only very low in the structure out.
- suitable heat treatment steps that Solution annealing, cooling and precipitation hardening, can additionally the ductility of the alloy according to the invention be further improved.
- alloy A B C carbon 0.01 0.01 0.01 silicon 0.04 0.04 0.04 manganese 0.12 0.12 0.12 sulfur ⁇ 0.001 ⁇ 0.001 ⁇ 0.001 phosphorus 0.005 0.005 0.005 chrome 16.03 16.03 16.03 nickel 41.9 41.9 41.9 aluminum 0.19 0.19 0.19 cobalt 0.01 0.01 0.01 titanium 1.67 1.67 1.67 copper ⁇ 0.01 ⁇ 0.01 ⁇ 0.01 niobium 2.95 2.95 2.95 boron - 0.2 - hafnium - - 1.0 iron rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest rest
- the material With the slow expansion rate, the material has sufficient Time to relax. Therefore these are determined Strength values not as significant as that of the faster strain rate.
- the slow Expansion rate has the oxygen contained in the environment on the other hand, sufficient time to make grain boundary effects appear brittle to cause. Therefore, they are slow Elongation rate determined more meaningful elongation at break than that determined at the fast strain rate.
- the of the alloy body formed according to the invention B 'and C' therefore outperform at 705 ° C Ductility of the alloy according to the prior art manufactured material body A 'by far and are him at least equal to its heat resistance.
- the alloys according to the invention can with great advantage as rotors of large gas turbines be used because they have a sufficiently high Heat resistance and because of the high ductility local temperature gradients that cannot be avoided can only build up low local voltages.
- the ductility of the Alloy improved according to the invention become. Between 0.5 and 20 is preferred [° C / min] lying cooling rate with which the material of the in the solution annealing provided annealing temperature to the the precipitation hardening provided temperature is performed.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Heat Treatment Of Articles (AREA)
Description
Legierung | A | B | C |
Kohlenstoff | 0,01 | 0,01 | 0,01 |
Silicium | 0,04 | 0,04 | 0,04 |
Mangan | 0,12 | 0,12 | 0,12 |
Schwefel | <0,001 | <0,001 | <0,001 |
Phosphor | 0,005 | 0,005 | 0,005 |
Chrom | 16,03 | 16,03 | 16,03 |
Nickel | 41,9 | 41,9 | 41,9 |
Aluminium | 0,19 | 0,19 | 0,19 |
Kobalt | 0,01 | 0,01 | 0,01 |
Titan | 1,67 | 1,67 | 1,67 |
Kupfer | <0,01 | <0,01 | <0,01 |
Niob | 2,95 | 2,95 | 2,95 |
Bor | - | 0,2 | - |
Hafnium | - | - | 1,0 |
Eisen | Rest | Rest | Rest |
Werkstoffkörper | Dehnungsrate [s-1] | Zugfestigkeit [MPa] bei 705°C | Bruchdehnung [%] bei 705°C | |
7,09·10-5 | 7,09·10-7 | |||
A' | x | 705 | 16,4 | |
A' | x | 597 | 6,7 | |
B' | x | 765 | 13,6 | |
B' | x | 752 | 11,1 | |
B' | x | 541 | 12,0 | |
C' | x | 708 | 14,4 | |
C' | x | 570 | 10,6 |
Claims (7)
- Eisen-Nickel-Superlegierung mit folgender chemischer Zusammensetzung in Gewichts-% :max. 0,02 Kohlenstoffmax. 0,10 Siliciummax. 0,20 Manganmax. 0,002 Schwefelmax. 0,015 Phosphor15 bis 18 Chrom40 bis 43 Nickel0,1 bis 0,3 Aluminiummax. 0,30 Kobalt1,5 bis 1,8 Titanmax. 0,30 Kupfer2,8 bis 3,2 Niob0,02 bis 0,3 Bor und/oder 0,05 bis 1,5 HafniumRest Eisen.
- Legierung nach Anspruch 1, dadurch gekennzeichnet, dass der Borgehalt ca. 0,2 Gewichtsprozent beträgt.
- Legierung nach Anspruch 1, dadurch gekennzeichnet, dass der Hafniumgehalt ca. 1 Gewichtsprozent beträgt.
- Verfahren zur Herstellung eines hochtemperaturbeständigen Werkstoffkörpers aus einem von der Legierung gemäss Patentanspruch 1 gebildeten Ausgangskörper, dadurch gekennzeichnet, dass der Ausgangskörper in einem Ofen bei Temperaturen zwischen 900°C und 1000°C lösungsgeglüht und anschliessend in einer ersten Stufe bei Temperaturen zwischen 700°C und 760°C und in einer zweiten Stufe bei Temperaturen zwischen 600°C und 650°C ausscheidungsgehärtet wird.
- Verfahren nach Anspruch 4, dadurch gekennzeichnet, dass der lösungsgeglühte Ausgangskörper vor dem Ausscheidungshärten mit Luft auf Raumtemperatur abgekühlt wird.
- Verfahren nach Anspruch 4, dadurch gekennzeichnet, dass der lösungsgeglühte Ausgangskörper mit einer zwischen 0,5 und 20 [°C/min] liegenden Abkühlrate von der beim Lösungsglühen vorgesehenen Glühtemperatur auf die bei der Ausscheidungshärtung vorgesehene Temperatur geführt wird.
- Verfahren nach einem der Ansprüche 4 bis 6, dadurch gekennzeichnet, dass der Übergang von der ersten auf die zweiten Stufe durch Abkühlen im Ofen ausgeführt wird.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE19542920 | 1995-11-17 | ||
DE19542920A DE19542920A1 (de) | 1995-11-17 | 1995-11-17 | Eisen-Nickel-Superlegierung vom Typ IN 706 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0774526A1 EP0774526A1 (de) | 1997-05-21 |
EP0774526B1 true EP0774526B1 (de) | 2002-01-16 |
Family
ID=7777737
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP96810754A Expired - Lifetime EP0774526B1 (de) | 1995-11-17 | 1996-11-07 | Eisen-Nickel-Superlegierung vom Typ IN 706 |
Country Status (8)
Country | Link |
---|---|
US (1) | US5863494A (de) |
EP (1) | EP0774526B1 (de) |
JP (1) | JP3781494B2 (de) |
KR (1) | KR970027351A (de) |
CN (1) | CN1079840C (de) |
CA (1) | CA2184960C (de) |
DE (2) | DE19542920A1 (de) |
RU (1) | RU2173349C2 (de) |
Families Citing this family (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4123064B2 (ja) * | 2003-06-13 | 2008-07-23 | 株式会社日立製作所 | 蒸気タービンロータおよび蒸気タービンプラント |
US7156932B2 (en) * | 2003-10-06 | 2007-01-02 | Ati Properties, Inc. | Nickel-base alloys and methods of heat treating nickel-base alloys |
US7316057B2 (en) * | 2004-10-08 | 2008-01-08 | Siemens Power Generation, Inc. | Method of manufacturing a rotating apparatus disk |
US7531054B2 (en) * | 2005-08-24 | 2009-05-12 | Ati Properties, Inc. | Nickel alloy and method including direct aging |
US8663404B2 (en) * | 2007-01-08 | 2014-03-04 | General Electric Company | Heat treatment method and components treated according to the method |
US8668790B2 (en) * | 2007-01-08 | 2014-03-11 | General Electric Company | Heat treatment method and components treated according to the method |
US7985304B2 (en) * | 2007-04-19 | 2011-07-26 | Ati Properties, Inc. | Nickel-base alloys and articles made therefrom |
US8313593B2 (en) * | 2009-09-15 | 2012-11-20 | General Electric Company | Method of heat treating a Ni-based superalloy article and article made thereby |
US8512485B2 (en) | 2011-01-03 | 2013-08-20 | General Electric Company | Alloy |
US10266926B2 (en) | 2013-04-23 | 2019-04-23 | General Electric Company | Cast nickel-base alloys including iron |
DE102015206323A1 (de) * | 2015-04-09 | 2016-10-13 | Siemens Aktiengesellschaft | Bauteil mit Festigkeitsgradienten, Verfahren und Turbine |
CN106480445B (zh) * | 2015-09-02 | 2019-02-26 | 沈阳大陆激光工程技术有限公司 | 在卷取机夹送辊表面制备耐磨抗热复合涂层的合金材料 |
US10563293B2 (en) | 2015-12-07 | 2020-02-18 | Ati Properties Llc | Methods for processing nickel-base alloys |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE1082739B (de) * | 1953-05-29 | 1960-06-02 | Nyby Bruk Ab | Verwendung nicht ausscheidungshaertender, ueberhitzungsunempfindlicher Legierungen |
GB999439A (en) * | 1962-05-10 | 1965-07-28 | Allegheny Ludlum Steel | Improvements in or relating to an austenitic alloy |
CA920842A (en) * | 1970-02-09 | 1973-02-13 | The International Nickel Company Of Canada | Nickel-chromium-iron alloys |
US3705827A (en) * | 1971-05-12 | 1972-12-12 | Carpenter Technology Corp | Nickel-iron base alloys and heat treatment therefor |
US3785876A (en) * | 1972-09-25 | 1974-01-15 | Special Metals Corp | Treating nickel base alloys |
US4225363A (en) * | 1978-06-22 | 1980-09-30 | The United States Of America As Represented By The United States Department Of Energy | Method for heat treating iron-nickel-chromium alloy |
US5415712A (en) * | 1993-12-03 | 1995-05-16 | General Electric Company | Method of forging in 706 components |
-
1995
- 1995-11-17 DE DE19542920A patent/DE19542920A1/de not_active Withdrawn
-
1996
- 1996-09-05 US US08/707,610 patent/US5863494A/en not_active Expired - Lifetime
- 1996-09-06 CA CA002184960A patent/CA2184960C/en not_active Expired - Lifetime
- 1996-10-17 KR KR1019960046582A patent/KR970027351A/ko not_active Application Discontinuation
- 1996-11-07 EP EP96810754A patent/EP0774526B1/de not_active Expired - Lifetime
- 1996-11-07 DE DE59608591T patent/DE59608591D1/de not_active Expired - Lifetime
- 1996-11-15 JP JP30515796A patent/JP3781494B2/ja not_active Expired - Fee Related
- 1996-11-15 RU RU96121981/02A patent/RU2173349C2/ru not_active IP Right Cessation
- 1996-11-16 CN CN96114573A patent/CN1079840C/zh not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
US5863494A (en) | 1999-01-26 |
JP3781494B2 (ja) | 2006-05-31 |
CA2184960A1 (en) | 1997-05-18 |
DE19542920A1 (de) | 1997-05-22 |
RU2173349C2 (ru) | 2001-09-10 |
DE59608591D1 (de) | 2002-02-21 |
EP0774526A1 (de) | 1997-05-21 |
KR970027351A (ko) | 1997-06-24 |
CN1079840C (zh) | 2002-02-27 |
CA2184960C (en) | 2008-01-08 |
JPH09170054A (ja) | 1997-06-30 |
CN1157332A (zh) | 1997-08-20 |
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