EP2163656B1 - Support d'enregistrement d'informations optiques, substrat et procédé de fabrication pour le support d'enregistrement d'informations optiques - Google Patents

Support d'enregistrement d'informations optiques, substrat et procédé de fabrication pour le support d'enregistrement d'informations optiques Download PDF

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Publication number
EP2163656B1
EP2163656B1 EP09168496A EP09168496A EP2163656B1 EP 2163656 B1 EP2163656 B1 EP 2163656B1 EP 09168496 A EP09168496 A EP 09168496A EP 09168496 A EP09168496 A EP 09168496A EP 2163656 B1 EP2163656 B1 EP 2163656B1
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Prior art keywords
cobalt
weight
base superalloy
temperature
alloy
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EP09168496A
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German (de)
English (en)
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EP2163656A1 (fr
Inventor
Mohamed Nazmy
Andreas KÜNZLER
Markus Staubli
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General Electric Technology GmbH
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Alstom Technology AG
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    • 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
    • C22C19/07—Alloys based on nickel or cobalt based on cobalt

Definitions

  • the invention relates to the field of materials technology. It relates to a cobalt-based superalloy with a y / y microstructure, which has very good mechanical properties and good oxidation resistance at high operating temperatures up to about 1000 ° C.
  • Cobalt or nickel based superalloys are known in the art.
  • components of nickel-base superalloys in which a ⁇ / ⁇ precipitation hardening mechanism is usually used to improve the high-temperature mechanical properties, have very good material strength at high temperatures, but also very good corrosion and oxidation resistance and creep properties. Due to these properties, when using such materials z.
  • the inlet temperature of the gas turbine can be increased, whereby the efficiency of the gas turbine plant increases.
  • cobalt base superalloys are solidified by carbide precipitates and / or solid solution hardening due to alloying of refractory elements, resulting in lower high temperature strength compared to the ⁇ / ⁇ nickel base superalloys.
  • secondary carbide precipitations in the temperature range of about 650 - 927 ° C, the ductility is also severely degraded.
  • cobalt-base superalloys often have an advantage over nickel-base superalloys, improved hot corrosion resistance, and higher resistance to oxidation and wear.
  • cobalt-based superalloys having a predominantly ⁇ / ⁇ 'microstructure have also become known which exhibit improved high-temperature strength compared with the abovementioned commercial cobalt-base superalloys.
  • this alloy also contains titanium.
  • the structure of this alloy consists mainly of the typical ⁇ / ⁇ structure with a hexagonal (Co, Ni) 3 Ti compound with plate-like morphology, the latter having a negative influence on the high temperature properties and therefore the use of such alloys at temperatures below 800 ° C is limited.
  • Co-Al-W-based ⁇ / ⁇ superalloys have become known ( Akane Suzuki, Garret C. De Nolf, and Tresa M. Pollock: High Temperature Strength of Co-based ⁇ / ⁇ '-Superalloys, Mater. Res. Soc. Symp. Proc. Vol. 980, 2007, Materials Research Society ).
  • the alloys studied there have 9 At. -% Al and 9-11 at. -% W, where optionally 2 At. -% Ta or 2 At. -% Re were added.
  • 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 cobalt-based superalloy, which has improved mechanical properties and good oxidation resistance especially at high temperatures up to about 1000 ° C.
  • the alloy should also be advantageous for the production of monocrystalline components.
  • the alloy consists of a cubic face-centered ⁇ -Co matrix phase and a high volume fraction of ⁇ '-phase Co 3 (Al, W), which is stabilized by Ta.
  • the ⁇ '-precipitates are very stable and lead to a material consolidation, which has a positive effect on the properties (creep properties, oxidation behavior), especially at high temperatures.
  • This Co-superalloy has neither Cr nor Ni, but a relatively high proportion of W.
  • This high proportion of tungsten (25-28% by weight) causes the ⁇ '-phase to be further strengthened, thus improving the creep properties become.
  • W adjusts the grid offset between the ⁇ matrix and the ⁇ 'phase, with a small lattice offset allowing the formation of a coherent microstructure.
  • Ta also acts as a precipitation hardener. 0.5 to 6% by weight of Ta, preferably 5.0-5.4% by weight of Ta, should be added. Ta increases the high-temperature strength. If more than 6% by weight of Ta is adjusted, the adverse oxidation resistance will be lowered.
  • the alloy contains 3-8% by weight of Al, preferably 3.1-3.4% by weight of Al.
  • an Al 2 O 3 protective film is formed on the material surface, which enhances the high-temperature oxidation resistance.
  • B is an element which is available in small amounts from 0.001 to max. 0.05 wt.% Solidifies the grain boundaries of the cobalt base superalloy. Higher boron contents are critical, as they can lead to undesirable boron precipitations, which have an embrittling effect. In addition, B lowers the melting temperature of the Co alloy, so B contents above 0.05 wt% are not meaningful. The interaction of boron in the specified range with the other constituents, in particular with Ta, leads to good strength values.
  • Mo is a solid solution in the cobalt matrix. Mo affects the lattice offset between the ⁇ -matrix and the ⁇ '-phase and thus also the morphology of ⁇ 'under creep stress.
  • C is in the specified range from 0.01 to max. 0.2% by weight is useful for carbide formation, which in turn increases the strength of the alloy. C also acts as a grain boundary consolidator. If more than 0.2% by weight of carbon is present, this disadvantageously leads to embrittlement.
  • Hf in the specified range of 0.01-0.1% by weight mainly solidifies the ⁇ matrix and thus contributes to increasing the strength.
  • Hf in combination with 0.01-0.1% by weight of Si has a favorable effect on the oxidation resistance. If the mentioned ranges are exceeded, this disadvantageously leads to embrittlement of the material.
  • the cobalt-base superalloy according to the invention owing to its chemical composition (combination of the specified elements in the ranges indicated), has excellent properties at high temperatures up to about 1000 ° C., in particular good creep rupture strength, ie. H. good creep properties, and extremely high oxidation resistance.
  • Table 2 Compositions of the investigated alloys according to the invention Co W al Ta C Hf Si B Not a word Co-1 rest 26 3.4 5.1 0.2 0.1 0.1 12:05 - Co-2 rest 27.25 8th 5.2 0.2 0.1 0.1 12:05 - Co-3 rest 26 3.4 0.5 0.2 0.1 12:05 12:05 2.8 Co-4 rest 25.5 3.1 5 0.2 0.1 12:05 12:05 - Co-5 rest 25.5 3.1 5.2 0.2 0.1 12:05 12:05 -
  • Fig. 1 For the alloy Co-1 according to the invention, the microstructure obtained in this way is shown. The fine distribution of the precipitated ⁇ '-phase in the ⁇ -matrix can be seen very well. These ⁇ '-precipitates are very similar to the ⁇ '-phase, which is typical of nickel-base superalloys. It can be expected that the ⁇ 'precipitates in this cobalt base superalloy are more stable than those in the nickel base superalloys. This is due to the presence of tungsten in the form of Co 3 (Al, W), which has a low diffusion coefficient.
  • Fig. 2 shows the curve of the yield strength ⁇ 02 for the inventive alloy Co-1 as a function of the temperature in the range of room temperature to about 1000 ° C.
  • Table 1 The results for the in Table 1
  • the commercial comparative alloys listed and the known from the literature Co-Al-W-Ta alloy are also in Fig. 2 shown
  • the yield strength ⁇ 0.2 of the alloy Co-1 is higher than the yield strength ⁇ 0.2 of the three comparative commercial alloys over the entire temperature range studied, the difference being particularly pronounced at temperatures> 600 ° C. In the range of about 700-900 ° C, the yield strength of the cobalt-base superalloy Co-1 is about twice as large as the yield strength of the best known commercial alloy M302 investigated here. Although the known from the literature Co-Al-W-Ta alloy in the higher temperature range from about 650 ° C in relation to the yield strength ⁇ 0.2 is superior to the commercial comparative alloys, so significantly improved values can be achieved with the present inventive alloy.
  • Fig. 3 the dependence of the tensile strength ⁇ US of the alloy Co-1 and the known comparative alloys described in Table 1 from the temperature in the range from room temperature to about 1000 ° C is shown.
  • the known superalloy M302 has the highest tensile strength values, from about 600 ° C, the inventive cobalt-based superalloy Co-1 is significantly better.
  • the tensile strength of Co-1 is about twice as high as the tensile strength of M302 and even about 2.5 times as high as the tensile strength of M509 and X-40, respectively.
  • Fig. 4 is the dependence of the elongation at break ⁇ of the alloy Co-1 and known comparative alloys of the temperature in the range of room temperature to about 1000 ° C shown. While at RT the elongation at break for alloy Co-1 is still above the values for the commercial alloys M509 and X-40, it is much lower at higher temperatures. The best elongation at break shows the alloy M302 in almost the entire temperature range investigated.
  • the alloys Co-1, Co-4 and Co-5 according to the invention endure consistently higher stresses than the comparative alloy, ie they have improved creep properties, due to the precipitation of the ⁇ '-phase and the associated solidification and the additional above-mentioned solidification mechanisms is due.
  • cobalt-base superalloys according to the invention can advantageously be high-temperature components for gas turbines, such as blades, z. As guide vanes, or produce heat shields. Due to the good creep properties of the material, these components are particularly suitable for use at very high temperatures.
  • the invention is not limited to the embodiments described above.
  • it is also advantageous to produce single-crystal components from the cobalt-base superalloys, specifically when the C and B contents (B and C are grain boundary strengtheners), but also the Hf and Si contents in comparison to those described above Examples are reduced and selected weight proportions, which are rather at the lower limit of the ranges given in claim 1 for these elements.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Catalysts (AREA)

Claims (17)

  1. Superalliage à base de cobalt, caractérisé par la composition chimique suivante (indications en % en poids) :
    - 25-28 de W,
    - 3-8 d'Al,
    - 0,5-6 de Ta,
    - 0-3 de Mo,
    - 0,01-0,2 de C,
    - 0,01-0,1 d'Hf,
    - 0,001-0,05 de B,
    - 0,01-0,1 de Si,
    le reste étant formé de Co et d'impuretés liées à la fabrication.
  2. Superalliage à base de cobalt selon la revendication 1, caractérisé par 25,5-27,25, de préférence 25,5-26% en poids de W.
  3. Superalliage à base de cobalt selon la revendication 1, caractérisé par 3,1-3,4% en poids d'Al.
  4. Superalliage à base de cobalt selon la revendication 1, caractérisé par 5-6, de préférence 5,0-5,3% en poids de Ta.
  5. Superalliage à base de cobalt selon la revendication 1, caractérisé par 2,8% en poids de Mo.
  6. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,2% en poids de C.
  7. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,01-0,03, de préférence 0,02% en poids de C.
  8. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,1% en poids d'Hf.
  9. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,01-0,02, de préférence 0,02% en poids d'Hf.
  10. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,05% en poids de B.
  11. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,001-0,003, de préférence 0,002% en poids de B.
  12. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,1% en poids de Si.
  13. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,05% en poids de Si.
  14. Superalliage à base de cobalt selon la revendication 1, caractérisé par 0,01-0,02, de préférence 0,01% en poids de Si.
  15. Superalliage à base de cobalt selon la revendication 1, caractérisé par la composition chimique suivante (indications en % en poids) :
    - 26 de W,
    - 3, 4 d'Al,
    - 5,1 de Ta,
    - 0,2 de C,
    - 0, 1 d'Hf,
    - 0,05 de B,
    - 0,1 de Si,
    le reste étant formé de Co et d'impuretés liées à la fabrication.
  16. Superalliage à base de cobalt sous forme d'un alliage monocristallin selon la revendication 1, caractérisé par la composition chimique suivante (indications en % en poids) :
    - 26 de W,
    - 3,4 d'Al,
    - 5,1 de Ta,
    - 0,02 de C,
    - 0,02 d'Hf,
    - 0,002 de B,
    - 0,01 de Si,
    le reste étant formé de Co et d'impuretés liées à la fabrication.
  17. Utilisation du superalliage à base de cobalt selon l'une quelconque des revendications 1-16 pour la fabrication d'un composant de turbine à gaz, de préférence une pale ou un bouclier thermique.
EP09168496A 2008-09-08 2009-08-24 Support d'enregistrement d'informations optiques, substrat et procédé de fabrication pour le support d'enregistrement d'informations optiques Not-in-force EP2163656B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CH01433/08A CH699456A1 (de) 2008-09-08 2008-09-08 Hochtemperaturbeständige Kobaltbasis-Superlegierung.

Publications (2)

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EP2163656A1 EP2163656A1 (fr) 2010-03-17
EP2163656B1 true EP2163656B1 (fr) 2011-12-28

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US (1) US8764919B2 (fr)
EP (1) EP2163656B1 (fr)
JP (1) JP2010065319A (fr)
CN (1) CN101671785B (fr)
AT (1) ATE539174T1 (fr)
CA (1) CA2677574C (fr)
CH (1) CH699456A1 (fr)

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US9034247B2 (en) 2011-06-09 2015-05-19 General Electric Company Alumina-forming cobalt-nickel base alloy and method of making an article therefrom
US10227678B2 (en) 2011-06-09 2019-03-12 General Electric Company Cobalt-nickel base alloy and method of making an article therefrom
CN102390920A (zh) * 2011-08-09 2012-03-28 苏州卡波尔模具科技有限公司 一种模压玻璃模具
CN103045910B (zh) * 2013-01-16 2015-01-28 北京科技大学 一种高温稳定γ’相强化的钴基高温合金及其制备方法
DE102013224989A1 (de) * 2013-12-05 2015-06-11 Siemens Aktiengesellschaft Gamma/Gamma gehärtete Kobaltbasis-Superlegierung, Pulver und Bauteil
WO2015159166A1 (fr) 2014-04-16 2015-10-22 Indian Institute Of Science Superalliage à base de cobalt sans tungstène à renforcement des phases gamma/gamma prime
CN104630569B (zh) * 2015-01-21 2017-12-22 厦门大学 一种含高温有序γ`强化相的Co‑V基高温合金及其制备方法
US10287824B2 (en) 2016-03-04 2019-05-14 Baker Hughes Incorporated Methods of forming polycrystalline diamond
US11292750B2 (en) * 2017-05-12 2022-04-05 Baker Hughes Holdings Llc Cutting elements and structures
US11396688B2 (en) 2017-05-12 2022-07-26 Baker Hughes Holdings Llc Cutting elements, and related structures and earth-boring tools
US11536091B2 (en) 2018-05-30 2022-12-27 Baker Hughes Holding LLC Cutting elements, and related earth-boring tools and methods
JP6952237B2 (ja) * 2020-03-02 2021-10-20 三菱パワー株式会社 Ｃｏ基合金構造体およびその製造方法
CN113699414B (zh) * 2021-07-21 2022-05-10 东北大学 一种优异高温拉伸性能的γ′相强化钴基高温合金
CN115198372B (zh) * 2022-05-13 2024-01-05 广东省诺法材料科技有限公司 一种具有分层微观结构的钴基单晶高温合金及其制备方法

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Publication number Publication date
US20100061883A1 (en) 2010-03-11
CN101671785B (zh) 2017-04-12
CA2677574A1 (fr) 2010-03-08
JP2010065319A (ja) 2010-03-25
ATE539174T1 (de) 2012-01-15
CA2677574C (fr) 2016-10-25
EP2163656A1 (fr) 2010-03-17
CN101671785A (zh) 2010-03-17
US8764919B2 (en) 2014-07-01
CH699456A1 (de) 2010-03-15

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