US3552953A - Cobalt-chromium base alloy and articles produced therefrom - Google Patents
Cobalt-chromium base alloy and articles produced therefrom Download PDFInfo
- Publication number
- US3552953A US3552953A US790369A US3552953DA US3552953A US 3552953 A US3552953 A US 3552953A US 790369 A US790369 A US 790369A US 3552953D A US3552953D A US 3552953DA US 3552953 A US3552953 A US 3552953A
- Authority
- US
- United States
- Prior art keywords
- cobalt
- percent
- chromium
- phase
- 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
- 229910045601 alloy Inorganic materials 0.000 title abstract description 57
- 239000000956 alloy Substances 0.000 title abstract description 57
- 229910000684 Cobalt-chrome Inorganic materials 0.000 title description 5
- 239000010952 cobalt-chrome Substances 0.000 title description 5
- WAIPAZQMEIHHTJ-UHFFFAOYSA-N [Cr].[Co] Chemical compound [Cr].[Co] WAIPAZQMEIHHTJ-UHFFFAOYSA-N 0.000 title description 4
- 239000011651 chromium Substances 0.000 abstract description 35
- 229910052804 chromium Inorganic materials 0.000 abstract description 33
- 239000000203 mixture Substances 0.000 abstract description 31
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract description 27
- 229910017052 cobalt Inorganic materials 0.000 abstract description 22
- 239000010941 cobalt Substances 0.000 abstract description 22
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 abstract description 22
- 239000011159 matrix material Substances 0.000 abstract description 22
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 16
- 229910052799 carbon Inorganic materials 0.000 abstract description 15
- 239000000155 melt Substances 0.000 abstract description 8
- 230000003647 oxidation Effects 0.000 abstract description 5
- 238000007254 oxidation reaction Methods 0.000 abstract description 5
- 238000005486 sulfidation Methods 0.000 abstract description 4
- 239000012071 phase Substances 0.000 description 47
- 238000006243 chemical reaction Methods 0.000 description 22
- 230000005496 eutectics Effects 0.000 description 19
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 16
- 238000007711 solidification Methods 0.000 description 15
- 230000008023 solidification Effects 0.000 description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 12
- 229910002058 ternary alloy Inorganic materials 0.000 description 11
- 229910052759 nickel Inorganic materials 0.000 description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 7
- 229910052727 yttrium Inorganic materials 0.000 description 7
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 7
- 229910052742 iron Inorganic materials 0.000 description 6
- 239000007788 liquid Substances 0.000 description 6
- 229910052761 rare earth metal Inorganic materials 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 238000007792 addition Methods 0.000 description 4
- 230000008014 freezing Effects 0.000 description 4
- 238000007710 freezing Methods 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 238000010587 phase diagram Methods 0.000 description 4
- 229910000601 superalloy Inorganic materials 0.000 description 4
- ULORNNZYVOQJFU-UHFFFAOYSA-N [C].[Cr].[Co] Chemical compound [C].[Cr].[Co] ULORNNZYVOQJFU-UHFFFAOYSA-N 0.000 description 3
- 239000006185 dispersion Substances 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000007246 mechanism Effects 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 230000003068 static effect Effects 0.000 description 3
- 238000006467 substitution reaction Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 238000005266 casting Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000009472 formulation Methods 0.000 description 2
- 239000002655 kraft paper Substances 0.000 description 2
- 239000007790 solid phase Substances 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 229910000531 Co alloy Inorganic materials 0.000 description 1
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 102220467129 Runt-related transcription factor 1_L13V_mutation Human genes 0.000 description 1
- RZJQYRCNDBMIAG-UHFFFAOYSA-N [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] Chemical class [Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Cu].[Zn].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Ag].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn].[Sn] RZJQYRCNDBMIAG-UHFFFAOYSA-N 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000002860 competitive effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000012937 correction Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 239000006023 eutectic alloy Substances 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000003607 modifier Substances 0.000 description 1
- 238000005191 phase separation Methods 0.000 description 1
- 239000008247 solid mixture Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B21/00—Unidirectional solidification of eutectic materials
- C30B21/02—Unidirectional solidification of eutectic materials by normal casting or gradient freezing
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/06—Alloys based on chromium
Definitions
- alloys like certain eutectics as indicated in the patent to Kraft 3,124,- 452, may be solidified to produce articles of pronounced anisotropy.
- a dispersed carbide phase (Cr, Co)-;C aligns in a cobalt-base solid solution matrix.
- the alloys of the cobalt-chromium-carbon system offer great potential utility in the advanced gas turbine engines.
- the particular applications and the particular needs in a given application will, of course, vary.
- the strength characteristics of such articles are usually preferential as to direction and, in those articles where increased omnidirectional strength is of more fundamental importance, the anisotropic articles may often be less preferred than components exhibiting a lesser degree of directional orientation.
- the present invention generally contemplates alloys nominally of the cobalt-chromium-carbon type which substantially solidify according to the eutectic-type reaction wherein two primary phases freeze simultaneously from a multi-component system to form a matrix phase consisting of a cobalt base alloy and a dispersed phase consisting of a mixed carbide of the M C type.
- the alloys of this invention solidify such that the carbide is randomly dispersed throughout the matrix or, upon unidirectional solidification, is dispersed in a skeletal distribution in the matrix. As such, these alloys display substantial omnidirectional strength.
- the unmodified ternary alloys of this invention in terms of the basic cobalt, chromium, carbon relationship, occupy a limited segment on the eutectic trough which exists in the ternary phase diagram of this system. Accordingly, the ternary alloys lie below the liquidus trough and within the two phase field, solidifying, in fundamental terms, according to the monovariant eutectic reaction:
- the ternary alloy composition by weight, solidifying by this reaction consists essentially of, 45.2-49.2 percent cobalt, 49-53 percent chromium and about 1.8 percent carbon.
- the particularly preferred ternary alloy is formulated at the composition, by weight, 49.2 percent cobalt, 49 percent chromium, and 1.8 percent carbon.
- the present basic alloy is tolerant toward the addition or substitution of certain materials, and, in certain applications some change from the basic ternary composition is desirable.
- alloys in terms of the melt composition, may be generated from a formulation comprising by weight, 45-55 percent chromium, 1.7-2.2 percent carbon, up to 10 percent nickel, up to 5 percent iron, up to 2 percent aluminum, yttrium and the rare earth elements, balance essentially cobalt.
- FIG. 1 is a photomicrograph of a unidirectionally solidified specimen of the ternary alloy at the preferred composition taken transverse to the direction of growth X 500).
- FIG. 2 is a photomicrograph of the same specimen taken in longitudinal section (X500). 5
- FIG. 3A is a space model phase diagram illustrating a eutectic trough, e-e in a ternary system.
- FIG. 3B is an isopleth taken along the dotted lines of FIG. 3A.
- FIG. 3C is a projection of the eutectic trough and the solubility curves on the basal triangle.
- FIG. 4 is the liquidus diagram for the cobalt-chromiumcarbon system.
- FIG. 5 is a graph demonstrating the tensile strength of the ternary alloy as a function of temperature.
- FIG. 6 is a graph depicting the stress-rupture life of the alloys of this invention as compared to a number of competitive alloys.
- FIG. 7 is a chart demonstrating the results of vane cyclic sulfidation-erosion testing of these alloys as a function of time.
- FIG. 8 is a graph illustrating the extent of specimen bowing in thermal fatigue testing of various alloys, the arrows indicating the onset of surface cracking.
- the present approach contemplates the solidification of a melt whose composition substantially corresponds to that at the eutectic trough of some phase diagrams, such a trough being illustrated by way of example by the line e-e of the model ternary diagram of FIG. 3A, which shows a three phase region passing continuously from one binary eutectic horizontal to the other along the line 2-2
- the vertical section or isopleth indicated by the dotted lines of FIG. 3A is reproduced as FIG. 3B.
- a liquid of composition X will solidify over the temperature range T to T2-
- the equilibrium solidification of composition X may be conveniently described by referring to FIG.
- 3C which is a projection of the eutectic trough and the solubility curves on the basal triangle. Also shown are the tie triangles whose vertices indicate the composition of the liquid and two solid phases in equilibrium. At each temperature level there is a tie triangle. These triangles reduce to the eutectic horizontal in the terminal binary phase diagrams. For the solidification of composition X only the tie triangles corresponding to the beginning of freezing, T and the termination of freezing, T have been shown in FIG. 3C. There are in fact a continuous series of tie triangles between these temperatures.
- the term monovariant eutectic reaction may conveniently be utilized to describe the above-mentioned solidification reaction in the ternary system including the basic ternary alloys of this invention, the term is not always applicable to the higher order systems.
- the present formulation does not result in the aligned fibrous carbide phase of the prior compositions but rather in a randomly dispersed mixed carbide phase or, in the case of the unidirectionally solidified structure, in a skeletal distribution of the carbide.
- the present castings exhibit a greater degree of isotropy and omnidirectional strength than the aligned structures including the M- C carbide.
- the fundamental premise of the present invention therefore, resides in the formation and random dispersion of the M C -type carbides in a cobalt base alloy matrix of high chromium content. In directionally solidified form these carbides will normally be distributed in a skeletal structure.
- the basic alloy system from which these structures are formed is the ternary alloy of cobalt, chromium and carbon solidifying accordinging to the monovariant eutectic reaction, particularly in the compositional range, by weight, of 45.2-49.2 percent cobalt, 49-53 percent chromium, and about 1.8 percent carbon.
- Its elastic modulus at room temperature is 40x10 p.s.i. which compares favorably with the reported elastic moduli of the commercial cobalt-base superalloys in the range of 3.0-36 10 p.s.i. In terms of density, the present alloy density of 7.91 g./cc.
- the basic ternary composition exhibits a reasonable tolerance insofar as modifications to the basic alloy chemlstry are concerned.
- modifications to the basic alloy chemlstry are concerned.
- articles formed of the basic ternary composition unidirectionally solidified at about 10 cm./hr. have displayed unacceptable creep-rupture properties in the intermediate temperature range of 1500-1600 F. While the reasons for this behavior are not fully understood, the behavior is believed to be associated with the allotropic transformation of the cobaltchromium solid solution.
- modification of the alloy is suggested. Accordingly, the basic alloy was modified, in some instances, to include nickel, a face-centered cubic stabilizer. Nickel substitutions of up to about 10 weight percent are readily tolerated and serve to reduce the transformation temperature and thus to shift it out of the critical range.
- transformation temperature is similarly and more efiiciently reduced by substituting iron for a portion of the cobalt in these alloys.
- additions of aluminum, yttrium and therare earth'elements may advantageously be added to these alloys. Such additions are primarily included as modifiers of the solid solution matrix, aluminum, yttrium and the rare earth elements, such as lanthanum frequently being added to the superalloys to promote their oxidation/erosion resistance.
- An alloy substantially solidifying according to the reaction L a+;8 where on comprises an alloy consisting essentially of, by weight, 25-35 percent chromium, up to about 10 percent nickel, up to about 5 percent iron and up to about 2 percent aluminum, yttrium and the rare earth elements and where [3 consists of a dispersed carbide of the M C type where M includes cobalt, chromium and the other stable carbide-forming elements of the a phase.
- a unidirectionally solidified metallic article having a substantially two phase microstructure consisting of a. matrix phase and a dispersed phase, the matrix phase consisting essentially of a cobalt-chromium-base alloy, the dispersed phase consisting essentially of a mixed carbide of the generic type (Cr, Co) C in a substantially skeletal distribution.
- a unidirectionally solidified metallic article having a substantially two phase microstructure consisting of a matrix phase and a dispersed phase, the matrix phase consisting essentially of a cobalt-base alloy containing, by weight, 25-35 percent chromium, up to about 10 percent nickel, up to about 5 percent iron, and up to about 2 percent aluminum, yttrium and the rare earth elements, the dispersed phase consisting of a mixed carbide of the C C type Where M includes cobalt, chromium and the other stable carbide forming elements of the matrix phase alloy.
- An alloy consisting essentially of, by weight, 45-55 percent chromium, 1.7-2.2 percent carbon, up to 10 percent nickel, up to 5 percent iron and up to 2 percent aluminum, yttrium and the rare earth elements, balance essentially cobalt, said alloy having a microstructure of a dispersion of the M C type carbides in a cobalt base alloy matrix of high chromium content.
- I References Cited 9.
- Analloy according to claim wherein the chromium UNITED STATES PATENTS content is about 49 percent by Weight and the carbon cony 5 tent is about 1.8 percent by weight. 3124452 3/1964 Kraft 75"134 10.
- An alloy consisting of, by weight, 49-53 percent 3434827 3/1969 'Lemkey 75' 134 romium, 1.8-2 percent carbon, balance essentially 5 3,434,892 3/ 19 69 Heimke 7 5 134 balt, said alloy having a microstructure of a dispersion of the M C type carbides in a cobalt base alloy matrix of RICHARD N Pnmary Exammer high chromium content. v y Y 11. A eutectic alloy consisting essentially of, by Weight, 10 X- about 49.2 percent cobalt, 49 percent chromium, and 1.8 135, percent carbon.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US79036969A | 1969-01-10 | 1969-01-10 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3552953A true US3552953A (en) | 1971-01-05 |
Family
ID=25150485
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US790369A Expired - Lifetime US3552953A (en) | 1969-01-10 | 1969-01-10 | Cobalt-chromium base alloy and articles produced therefrom |
Country Status (10)
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3649225A (en) * | 1969-11-17 | 1972-03-14 | United Aircraft Corp | Composite coating for the superalloys |
| US3844845A (en) * | 1973-11-15 | 1974-10-29 | Gen Electric | Directional composites by solid-state up-transformation |
| US3847679A (en) * | 1973-11-15 | 1974-11-12 | Gen Electric | Directional eutectoid composites by solid-state up-transformation |
| US3891431A (en) * | 1971-05-10 | 1975-06-24 | Bbc Brown Boveri & Cie | Method of, and apparatus for, controlling the crystalline structure of alloys, and alloys so produced |
| US3976516A (en) * | 1973-10-17 | 1976-08-24 | Bbc Brown Boveri & Company Limited | High temperature alloy |
| US4016014A (en) * | 1974-02-11 | 1977-04-05 | Bbc Brown Boveri & Company Limited | High temperature alloy |
| US4088606A (en) * | 1974-05-06 | 1978-05-09 | Gould Inc. | Cobalt base nox reducing catalytic structure |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS51108228U (enrdf_load_stackoverflow) * | 1975-02-28 | 1976-08-30 | ||
| RU2257421C1 (ru) * | 2004-04-02 | 2005-07-27 | Закрытое акционерное общество "Уральский научно-технический инновационный центр им. Ф.П. Литке" | Способ получения сплавов тугоплавких металлов |
-
1969
- 1969-01-10 US US790369A patent/US3552953A/en not_active Expired - Lifetime
- 1969-12-23 SE SE17860/69A patent/SE365556B/xx unknown
-
1970
- 1970-01-05 DE DE19702000325 patent/DE2000325B2/de active Granted
- 1970-01-08 CA CA071734A patent/CA924128A/en not_active Expired
- 1970-01-09 CH CH23070A patent/CH573983A5/xx not_active IP Right Cessation
- 1970-01-09 FR FR7000822A patent/FR2033230A1/fr not_active Withdrawn
- 1970-01-09 BE BE744234D patent/BE744234A/xx unknown
- 1970-01-09 GB GB0225/70A patent/GB1294293A/en not_active Expired
- 1970-01-09 NL NL707000254A patent/NL150516B/xx unknown
- 1970-01-10 JP JP45002721A patent/JPS5013215B1/ja active Pending
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3649225A (en) * | 1969-11-17 | 1972-03-14 | United Aircraft Corp | Composite coating for the superalloys |
| US3891431A (en) * | 1971-05-10 | 1975-06-24 | Bbc Brown Boveri & Cie | Method of, and apparatus for, controlling the crystalline structure of alloys, and alloys so produced |
| US3976516A (en) * | 1973-10-17 | 1976-08-24 | Bbc Brown Boveri & Company Limited | High temperature alloy |
| US3844845A (en) * | 1973-11-15 | 1974-10-29 | Gen Electric | Directional composites by solid-state up-transformation |
| US3847679A (en) * | 1973-11-15 | 1974-11-12 | Gen Electric | Directional eutectoid composites by solid-state up-transformation |
| US4016014A (en) * | 1974-02-11 | 1977-04-05 | Bbc Brown Boveri & Company Limited | High temperature alloy |
| US4088606A (en) * | 1974-05-06 | 1978-05-09 | Gould Inc. | Cobalt base nox reducing catalytic structure |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5013215B1 (enrdf_load_stackoverflow) | 1975-05-17 |
| CH573983A5 (enrdf_load_stackoverflow) | 1976-03-31 |
| DE2000325A1 (de) | 1970-09-10 |
| DE2000325B2 (de) | 1972-06-29 |
| CA924128A (en) | 1973-04-10 |
| SE365556B (enrdf_load_stackoverflow) | 1974-03-25 |
| NL7000254A (enrdf_load_stackoverflow) | 1970-07-14 |
| GB1294293A (en) | 1972-10-25 |
| NL150516B (nl) | 1976-08-16 |
| FR2033230A1 (enrdf_load_stackoverflow) | 1970-12-04 |
| BE744234A (fr) | 1970-06-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109207799B (zh) | 一种稳定γ′相强化的Co-Ni-V-Al基高温合金 | |
| CN102803528B (zh) | Ni基单晶超合金及使用其的涡轮叶片 | |
| US3552953A (en) | Cobalt-chromium base alloy and articles produced therefrom | |
| JP5252348B2 (ja) | Ｎｉ基超合金とその製造方法およびタービンブレードまたはタービンベーン部品 | |
| JPWO2007122931A1 (ja) | Ｎｉ基超合金とその製造方法 | |
| US3155501A (en) | Nickel base alloy | |
| Guo et al. | Tensile deformation and fracture behavior of nickel-based superalloy DZ951G | |
| US3793012A (en) | Nickel-base tantalum carbide eutectic alloys | |
| Jithin S et al. | Comparative analysis between 5th and 6th generation superalloys and previous generation superalloys | |
| CN114032421B (zh) | 一种增材制造用镍基高温合金、镍基高温合金粉末材料和制品 | |
| US3793010A (en) | Directionally solidified eutectic type alloys with aligned delta phase | |
| JP2002235135A (ja) | 産業用タービンの単結晶ブレードのための非常に高い耐高温腐食性をもつニッケル系超合金 | |
| US2751668A (en) | Method of producing titanium carbide and article thereof | |
| US2981620A (en) | Cobalt-nickel base alloy | |
| US4055447A (en) | Directionally solidified eutectic γ-γ' nickel-base superalloys | |
| US3635769A (en) | Nickel-chromium eutectic alloy | |
| US3793013A (en) | Cobalt-base tantalum carbide eutectic alloys | |
| US4961905A (en) | Nickel aluminide materials having toughness and ductility at low temperatures | |
| US2805154A (en) | Nickel-base alloy | |
| US3304177A (en) | Method of producing la containing alloys | |
| US5023050A (en) | Superalloy for high-temperature hydrogen environmental applications | |
| JPS62109943A (ja) | 炭素を含有するホウ素添加アルミニウム化三ニツケルとその製法 | |
| US3617397A (en) | Cast nickel-base alloy | |
| US3667939A (en) | High temperature cobalt-base sheet alloy | |
| US4045255A (en) | Directionally solidified eutectic γ+β nickel-base superalloys |