GB2517653A - Fabrication of gamma titanuim (TiAl) alloy articles by powder metallurgy - Google Patents
Fabrication of gamma titanuim (TiAl) alloy articles by powder metallurgy Download PDFInfo
- Publication number
- GB2517653A GB2517653A GB8900043.4A GB8900043A GB2517653A GB 2517653 A GB2517653 A GB 2517653A GB 8900043 A GB8900043 A GB 8900043A GB 2517653 A GB2517653 A GB 2517653A
- Authority
- GB
- United Kingdom
- Prior art keywords
- tia1
- tial
- powders
- alloy articles
- preform
- 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.)
- Granted
Links
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 25
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 229910045601 alloy Inorganic materials 0.000 title abstract description 16
- 239000000956 alloy Substances 0.000 title abstract description 16
- 238000004663 powder metallurgy Methods 0.000 title abstract description 5
- 239000000203 mixture Substances 0.000 claims abstract description 29
- 239000000843 powder Substances 0.000 claims abstract description 25
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 8
- 238000000034 method Methods 0.000 claims abstract description 7
- 239000000463 material Substances 0.000 claims description 24
- 229910021330 Ti3Al Inorganic materials 0.000 claims description 10
- 230000015572 biosynthetic process Effects 0.000 claims description 5
- 239000002243 precursor Substances 0.000 claims description 3
- 102100032620 Cytotoxic granule associated RNA binding protein TIA1 Human genes 0.000 claims 2
- 101000654853 Homo sapiens Cytotoxic granule associated RNA binding protein TIA1 Proteins 0.000 claims 2
- 229910006281 γ-TiAl Inorganic materials 0.000 abstract 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 12
- 239000010936 titanium Substances 0.000 description 12
- 229910052719 titanium Inorganic materials 0.000 description 12
- 238000005096 rolling process Methods 0.000 description 8
- 238000007792 addition Methods 0.000 description 7
- 238000005275 alloying Methods 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 238000009792 diffusion process Methods 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 239000010955 niobium Substances 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 3
- 235000012771 pancakes Nutrition 0.000 description 3
- 238000013459 approach Methods 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- RUDFQVOCFDJEEF-UHFFFAOYSA-N yttrium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Y+3].[Y+3] RUDFQVOCFDJEEF-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 229910010039 TiAl3 Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical class [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000009924 canning Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000013067 intermediate product Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F5/006—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of flat products, e.g. sheets
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/047—Making non-ferrous alloys by powder metallurgy comprising intermetallic compounds
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Forging (AREA)
- Powder Metallurgy (AREA)
Abstract
Powder metallurgy techniques are disclosed for fabricating gamma titanium alloy articles (TiAl type alloys) from mixture of powder wherein one species is based on A13Ti and the other Ti3A1. Mixtures of these powders in the proper ratio can be compacted, worked and heat treated to form the desired gamma TiAl alloy.
Description
Description
Fabrication of Gamma Titanium (TiAl) Alloy Articles By Powder Metallurgy
Technical Field
This invention relates to the powder metallurgy fabrication of gamma titanium alloy articles.
Background Art
Titanium and its alloys have unique combinations of low densities and high melting points which lead to their widespread application in high technology applications, particularly in gas turbine engines.
A large number of titanium alloys have been proposed. These generally comprise at least about 80% tItanium with balance being other additions including aluminum, vanadium, chromium, zirconium, etc. The widely used commercial alloys of this type have either an alpha or beta structure, both of which are essentially titanium splid solutions.
Research has also been conducted aimed at utilizing various titanium intermetallic compounds based on titanium. These include Al3Ti, Ti3Al, and TiAl. The TiAl composition is the one of interest with respect to this invention. It has a high melting point, approximately 2600'F, and a low density, even lower of that of titanium because of the large amount of aluminum present. One draw back of TiAl is its lack of useful ductility. Various alloying approaches have been taken to overcome this problem with a certain degree of. success. U.S. Patent Nb. 4,294,615 which shares a common assignee with the present application, discloses that the addition of a small amount of vanadium increases the ductility of TiAl type compositions and that the addition of a small amount of carbon increases the creep rupture strength of such materials. This patent also describes some of the earlier work in the TiAl system. The patent is incorporated herein by reference.
Being an intermetallic material with high strength, low to moderate ductility, and high melting point, TiAl type alloys have in the past been formable only with the greatest of difficulty. Invariably, forming is conducted at a high temperature, generally in excess of about 2400F for reasons of ductility.
This requirement poses a problem for the production of certain thin section alloy shapes, particularly sheet material. Sheet material is formed by rolling, but when thin sheet is being formed, the heat extraction capability of the rolls is such that the material between the rolls rapidly loses its heat and then cracks as it becomes too cold. The obvious approach would be to heat the rolls to the hot rolling temperature, but this is impractical given the temperatures involved. To my knowledge crack free TiA1 sheet having a thickness of 0.1 inch and below has never been produced.
Similar difficulties can be envisioned in forming TiA1 type materials in different thin section shapes by other processes such as by forging.
Other titanium-aluminum compounds do not suffer from this great lack of ductility. In particular, Al3Ti and Ti3Al display useful ductilities.
As used herein, the terms Ti3Al, TiAl3 and TiAl include minor alloying elements which do not significantly change the crystal structure of the phases. These tens are also intended to denote materials which contain up to about 10% by volume of other phases in the case of Ti3Al and A13Ti and up to about 20% by volume of other phases in the case of TiAl. That is to say, a structure comprised of volume % TiAl, 5 volume % Al3Ti and 10 volume % Ti3A1 is considered to be TiAl.
Disclosure of Invention
It is an object of the present invention to provide a practical method for forming complex shapes and especially shapes with thin sections pf TiA1 type compositions.
The prior aart has disclosed the broad ranges for the TiA1 type compositions and has discussed at some length various alloying additions which may be made to this type of alloy for different purposes, mainly for improved ductility. To the best of my knowledge, however, the prior art has always contemplated forming and fabricating TiAl compositions from a homogeneous preform, a preform which has its origins as *a cast product of essentially a TiA1 composition.
My inventjon is the use of powder metallurgy to form TiAl compositions from a mixture of starting powders, one based on Al3Ti and the other based on Ti3A1. One skilled in the art can readily visualize that such a mixture of powders can be fabricated which will have an overall net composition lying within the TiAl gamma phase region.
According to my invention such a mixture of powders is formed and is compacted to form a preform, a homogeneous mass of essentially full density.
The resultant preform will have useful S ductilities especially if its exposure time at elevated temperature is kept at a minimum. The preform can be heated to an elevated temperature and formed into a useful shape, for example by rolling despite losing heat to the rolls: The formed article, having essentially a final shape is then heated at an elevated temperature for a time sufficient to allow diffusion between the A].3Ti and Ti3A1 constituents and thereby the formation of the desired TiA1 compositions. The resultant article contain a predominate amount of TiAl and can have useful ductilities by virtue of alloying additions added to the precursor powders.
The foregoing and other features and advantages of the present invention will become more apparent
from the following description and accompanying
drawings.
Brief Description of Drawings
Figure 1 shows a photomicrograph of as forged material.
Figure 2 shows a photomicrograph of as rolled material.
Figure 3 shows a photomicrograph of homogenized material.
Best Mode for Carrying Out the Invention
According to the present invention shapes of the difficult to form TiAl material are formed from a preform consisting of A13Ti and Ti3A1 powders in a ratio such that TiA1 can be formed by subsequent diffusional heat treatment.
I have used powder produced by rotary atomization which also provides an extremely rapid cooling rate from the liquid. However, the cooling rate is not essential to the success of the invention and nor for that matter is the highly spherical powder geometry.
It is my belief that powders formed by other techniques have equal utility in my invention.
I believe that a useful range of powder particle sizes for application to the present process is from about -40 to -120 U.S. standard sieve size. Powders falling within this size range should be formed from an A13Ti type composition and a Ti3Al composition.
Alloying additions which may be desired to enhance ductility or other alloy properties may be made to either or both of the alloy species.
The ratio of the powders to arrive at the desired TiA1 composition will depend in part upon the alloying additions which may have been made. The gamma type alloys, although based on an intermetallic compound, have a fairly wide composition range of from about 35 wt.% to about 45 wt.% aluminum (in the absence of other alloying elements). The skilled practitioner will have no difficulty in determining the ratio of TI3A1 and TiA13 materials necessary to arrive at the desired composition within the gamma range. The appropriate mixture of powders can be placed in a sheet metal container, a cart, which may for example. be made of stainless steel, and may be consolidated at a temperature in the range of 1600°? -2000°F i.e. 1800°F at a pressure ranging from 20-40 ksi i.e. 30 ksi for a time period from about one-half to about ten hours. This will produce a powder compact having a density at least 95% of theoretical density.
The can then be removed by either mechanical or chemical means. The compact can then be forged or extruded to an intermediate shape. Forging or extrusion can be conducted at a temperature of from about 1700°F to about 2100°F. A typical strain rate It should again be pointed out that while both the starting powders are of materials which have reasonable ductility, they will react by diffusion after compaction to form a much stronger much less ductile TiAl structure. Accordingly processing should be conducted in a timely fashion and at as low a temperature as possible consistent with achieving the desired results. This will minimize the formation of TiA1 during processing and thereby inhibit its possible interference with deformation processing.
A major product at which this invention is aimed is thin sheet material which might be used for example in the fabrication of honeycomb. The intermediate product produced by forging or extrusion is again canned but this time in a stronger alloy such as columbium. The choice of canning alloy in this instance is dictated by the desire to have a can which has a similar resistance to deformation at the selected temperature as the preform. Yttria can be used between the preform and the can to minimize diffusion and/or bonding between the can and preform.
The canned material can then be hot rolled in an elevated temperature between 2000°F and 2400°? tà the desired thickness and the can can then be removed.
The hot rolled material is then heat treated to encourage total diffusional interaction between Ti3Al and A.l3Ti constituents to form the TiA1 gamma structure. The time and temperature of this diffusional heat treatment will depend to some extent on the initial powder sizes employed. Larger powder sizes will provide a material having longer diffusional distances and less interface area and will need more time and/or higher temperature. Times from about 2-20 hours at 220OF-2500°F will be typical with the useful range of powder sizes.
The invention may be better understood by reference to the following specific illustrative
example.
EXANPLE
grams of -100 mesh Al-25 atomic % titanium was mixed with 194 grams of -50 mesh Ti-24 atomic % aluminum -11 atomic % niobium. Mixing was conducted in a V blender for about 2 hours. The blended powder was then placed in a stainless steel canister and vacuumed hot pressed in a vacuum in the range of 0.0001 torr. The powder is first soaked at 1700°F temperature for one hour and then consolidated at a pressure of 30 ksi for two hours at l700'F. The resultant compact 1.5 inches in diameter and 4 inches in length.
The can was removed by mechanical means. The compact was then forged in a 500 ton vacuum press.
The. compact was soaked at lB5OF for one hour before forging at 1850°F at a strain rate of 0.1 Inch per inch per minute using molybdenum dies. The resultant pancake was about 0.25 inch thick and had a microstructure shown in Figure 1.
A rolling preform was made by cutting a rectangular shape from this pancake and placing it on a flat picture frame can made from columbium alloy C103. Prior to placing the pancake into the can cavity all internal surfaces were coated with yttria to inhibit reaction between the titanium materials and the coluinbium can. The can assembly was TIC welded along the seams and was beveled at the leading edge to assist in the initial rolling step.
Rolling was performed on a conventional rolling mill at a temperature of 2200'F, a relatively low temperature which was selected to inhibit further transformation of the starting material to be stronger TiAl material. The material was first soaked for twenty minutes and then rolled using a pass schedule shown in Table 1 with intermediate reheats as shown.
It will be appreciate that this is an aggressive rolling schedule which was selected based on a desire to inhibit the TiAl formation to the extent possible.
Following this step x-ray diffraction analysis of the rolled material showed that it had not yet totally transferred to the gamma structure. Rolling was completely successful despite the large pass reduction taken. Final thickness achieve was about 0.07 inch.
It is to my knowledge the thinnest sheet ever successfully produced having an overall TiA1 composition. Figure 2 shows the as rolled microstructure.
This rolled sheet was then given a diffusion treatment in vacuum at 2400F for ten hours in an effort to completely transform the starting materials to the TiAl material. Commercially pure titanium sheet was used to surround the rolled stock to protect it from absorbing oxygen. After homogenization x-ray diffraction analysis was done to confirm that the -5 majority material had transformed to gamma. The microstructure of the homogenized sheet is shown in Figure 3. The lamellar structure is typical of that seen in gamma microstructures. The alpha two phase, Ti3A1, was also found by x-ray analysis. This is not surprising since the overall nominal composition selected is slightly rich in titanium which permits some alpha two phase to exist at equilibrium. Such as a titanium rich gamma alloy is generally considered to be even more difficult to fabricate than a completely pure TiAl structure would be.
Although this invention has been shown and described with respect to detailed embodiments thereof, it will be understood by those skilled in the art that various changes in form and detail thereof may be made without departing from the spirit and scope of the claimed invention.
Claims (5)
- Claims 1. A method for producing gamma (TIA1) titanium alloy articles including the steps of: a) compacting a mixture of Al3Ti and Ti3Al powders, whose overall composition lieswithin the TIA1 phase field, into a preform;b) -hot working the preform into a final shape; and c) homogEnizing the hot worked article under conditions which promote interdiffusion and TiA1 formation.
- 2. A compacted precursor whose overall composition, is that of TiA1 consisting essentially of a compact formed of Ti3Al and TiA13 powders.
- 3. A crack free sheet material whose thickness is less than about 0.1 inch and whose overall composition is TiA1.c Amendments to the claims have been filed as followsCLAIMS1. A method for producing gamma (TiAl) titanium alloy articles including the steps of: (a) compacting a mixture of Al3Ti and Ti3Al powders, whose overall composition lies within the TiAl phase field, into a preform; (b) hot working the preform into a final shape; and (C) homogenizing the hot worked article under conditions which1, promote intardiffusion and TiA1 formation.2. A compacted precursor whose overall cOmposition is that of TiM consisting essentially of a compact formed of Ti3Al and TiA13 powders.3. A method for producing gamma (TiA1) titanium alloy articles substantially as herein particularly described with reference to the accompanying figures.
- 4. Titanium alloy articles when produced by the method of claimi.
- 5. Titanium alloy articles when produced by the method of claim 3.-F-1 I-.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB8900043.4A GB2517653B (en) | 1989-01-03 | 1989-01-03 | Fabrication of gamma titanuim (TiAl) alloy articles by powder metallurgy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB8900043.4A GB2517653B (en) | 1989-01-03 | 1989-01-03 | Fabrication of gamma titanuim (TiAl) alloy articles by powder metallurgy |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| GB8900043D0 GB8900043D0 (en) | 2013-11-13 |
| GB2517653A true GB2517653A (en) | 2015-03-04 |
| GB2517653B GB2517653B (en) | 2017-08-30 |
Family
ID=49584979
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| GB8900043.4A Expired - Lifetime GB2517653B (en) | 1989-01-03 | 1989-01-03 | Fabrication of gamma titanuim (TiAl) alloy articles by powder metallurgy |
Country Status (1)
| Country | Link |
|---|---|
| GB (1) | GB2517653B (en) |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1218295A (en) * | 1967-12-14 | 1971-01-06 | Gen Electric | Improved metallic coating material |
| US4294615A (en) * | 1979-07-25 | 1981-10-13 | United Technologies Corporation | Titanium alloys of the TiAl type |
| JPS62278240A (en) * | 1986-05-23 | 1987-12-03 | Agency Of Ind Science & Technol | Compacting method for ti-al intermetallic compound member |
| JPS63114930A (en) * | 1986-10-31 | 1988-05-19 | Daido Steel Co Ltd | Ti-al powder metallurgical alloy |
| JPS63255331A (en) * | 1987-04-10 | 1988-10-21 | Sumitomo Light Metal Ind Ltd | Formation of ti-al intermetallic-compound member |
-
1989
- 1989-01-03 GB GB8900043.4A patent/GB2517653B/en not_active Expired - Lifetime
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1218295A (en) * | 1967-12-14 | 1971-01-06 | Gen Electric | Improved metallic coating material |
| US4294615A (en) * | 1979-07-25 | 1981-10-13 | United Technologies Corporation | Titanium alloys of the TiAl type |
| JPS62278240A (en) * | 1986-05-23 | 1987-12-03 | Agency Of Ind Science & Technol | Compacting method for ti-al intermetallic compound member |
| JPS63114930A (en) * | 1986-10-31 | 1988-05-19 | Daido Steel Co Ltd | Ti-al powder metallurgical alloy |
| JPS63255331A (en) * | 1987-04-10 | 1988-10-21 | Sumitomo Light Metal Ind Ltd | Formation of ti-al intermetallic-compound member |
Also Published As
| Publication number | Publication date |
|---|---|
| GB8900043D0 (en) | 2013-11-13 |
| GB2517653B (en) | 2017-08-30 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PE20 | Patent expired after termination of 20 years |
Expiry date: 20090102 |