GB2259309A - Ceramic particles - Google Patents
Ceramic particles Download PDFInfo
- Publication number
- GB2259309A GB2259309A GB9119239A GB9119239A GB2259309A GB 2259309 A GB2259309 A GB 2259309A GB 9119239 A GB9119239 A GB 9119239A GB 9119239 A GB9119239 A GB 9119239A GB 2259309 A GB2259309 A GB 2259309A
- Authority
- GB
- United Kingdom
- Prior art keywords
- melt
- ceramic particles
- aluminium
- metal
- dispersion
- 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.)
- Withdrawn
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B13/00—Oxygen; Ozone; Oxides or hydroxides in general
- C01B13/14—Methods for preparing oxides or hydroxides in general
- C01B13/145—After-treatment of oxides or hydroxides, e.g. pulverising, drying, decreasing the acidity
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/06—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B35/00—Boron; Compounds thereof
- C01B35/02—Boron; Borides
- C01B35/04—Metal borides
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/01—Particle morphology depicted by an image
- C01P2004/03—Particle morphology depicted by an image obtained by SEM
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/60—Particles characterised by their size
- C01P2004/62—Submicrometer sized, i.e. from 0.1-1 micrometer
Landscapes
- Chemical & Material Sciences (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Ceramic Products (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention provides a method of making a concentrated supply of ceramic particles which are readily wettable when added to an aluminium-based melt. The method companies forming a dispersion of ceramic particles (preferably titanium diboride) in a metal melt (preferably aliuminium) such that the ceramic particles are thoroughly wetted by the melt, solidifying the melt, and extracting metal from the solidified dispersion (preferably by caustic soda treatment where the melt comprises aluminium). The resulting supply of ceramic particles can then be dispersed in an aluminium-based melt under easily producible conditions (generally under ambient atmosphere, and at less than 1000 degrees C), with full wetting of the particles. The preferred method of producing the initial dispersion is by an in situ reaction of titanium and boron, which are preferably formed by reaction of aluminium in the melt with salts containing boron (preferably KBF4) and titanium (preferably K2TiF6).
Description
Ceramic Particles
This invention relates to making a concentrated supply of ceramic particles which are readily wettable when added to an aluminium-based melt, such as a melt of aluminium or of an aluminium alloy.
A considerable amount of work has been carried out on incorporating ceramic particles into metals to improve their mechanical properties such as stiffness, and to improve their performance at elevated temperatures. It is important that in the resulting metal matrix composite material the ceramic particles are fully wetted by the matrix metal, since otherwise the mechanical properties such as strength will be impaired.
U.S. Patent Specification No. 3037857 (assigned to Union Carbide) teaches making an aluminium-based metal matrix composite by adding pre-formed particles of a boride such as titanium diboride to aluminium or an aluminium alloy. For relatively low boride particle loadings this may be accomplished by adding them to an aluminium melt. However, U.S. 3037857 teaches making the addition at 1200 degrees C in a vacuum or under an argon atmosphere. The preferred method taught in U.S. 3037857, to obtain higher particle loadings, is to dry-blend powders of the boride and of the aluminium-based metal matrix cold, compact the blend at high pressure, and then heat to between 1000 and 1150 degrees C. For both techniques taught in U.S. 3037857, having to provide the conditions required considerably increases the cost of operating the process.Further, the surfaces of pre-formed ceramic particles formed by known techniques are contaminated, especially when the particles have been subjected to a comminution process, and neither technique taught in U.S. 3037857 can be relied upon to achieve full ceramic particle wetting regardless of the contaminants on the particle surfaces. U.S. 3037857 illustrates the difficulties which are experienced when trying to achieve adequate wetting of the ceramic particles when incorporating pre-formed ceramic particles into a matrix metal melt.
An alternative way of incorporating ceramic particles into a metal matrix melt is to form the ceramic particles by an in situ chemical reaction within the melt; see, for example, European Patent Specification No.
EP 0113249 A (Alcan International), and the specification of our U.K.
patent application No , filed on 9th September, 1991 and entitled "Metal Matrix Alloys". However, for some purposes it is desirable to achieve a level of ceramic particle loading which is greater than is achievable by such means.
According to the present invention, there is provided a method of making a concentrated supply of ceramic particles which are wettable when added to an aluminium-based melt, the method comprising forming a dispersion of ceramic particles in a metal melt such that the ceramic particles are thoroughly wetted by the melt, solidifying the melt, and extracting metal from the solidified dispersion, whereby to increase the concentration of ceramic particles in the dispersion.
We prefer that the metal melt in which the dispersion of ceramic particles is formed is an aluminium-based melt, such as a melt of an aluminium alloy or, preferably, aluminium. In such cases, the preferred method of performing the step of extracting metal from the solidified dispersion comprises alkali-leaching it to extract aluminium, preferably with an aqueous solution comprising caustic soda.
We have found that, as soon as sufficient metal is extracted from the solidified dispersion that the remaining product is of particulate form, then that product can be highly concentrated in ceramic particles. For example, where the matrix metal is aluminium and the ceramic particles are of titanium diboride, the resulting product at that stage contains only about 10% by weight aluminium. However, we generally prefer that substantially all of the metal should be extracted from the solidified dispersion.
For most applications, it is preferable that the ceramic particles should be sufficiently fine that the majority of the ceramic particles are of mass equivalent to spheres which are less than 1 micron in diameter; that is readily achievable using the following teachings. However, in some applications, e.g. where the particles are to provide abrasion resistance, the ceramic particles may usefully be coarser.
Although generally not the best method, formation of the initial dispersion of ceramic particles in a metal melt may be carried out by introducing pre-formed ceramic particles into the metal melt. As will be appreciated from the prior art discussion above, care will be needed in sourcing the ceramic particles, and considerable care will have to be taken to provide conditions to ensure that the ceramic particles are fully wetted by the metal melt. Nevertheless, in some circumstances it may worthwhile for a bulk producer to make the necessary arrangements, so that customers producing final metal matrix composites are relieved of individually having to make such arrangements.
In general, we greatly prefer that the dispersion of ceramic particles in the metal melt should be formed by reacting, within the metal melt, precursors for the ceramic particles.
The ceramic particles used in the method of the present invention may be any suitable ceramic particles such as one or more of the refractory oxides, silicides, borides, nitrides or carbides, for example. We generally prefer that the ceramic particles should be substantially insoluble in, and unreactive with, the metal melt in which they are dispersed in the method of the invention. It is not necessary for the ceramic particles to be of the same chemical composition; mixtures of different types of ceramic particles may be used. Nor is it necessary for them to be chemically pure; their metal constituents may be mixed (tungsten titanium carbide, for example) and/or their non-metal constituents may be mixed (titanium carbonitride, for example). The ceramic particles may be of any suitable shape, such as granular, tabular, acicular or fibrous, for example.
In accordance with a preferred embodiment of the invention, the ceramic particles comprise titanium boride, preferably titanium diboride. In practising this embodiment we prefer that the metal melt is an aluminium-based melt; and:
(a) a boron-containing salt (preferably potassium borofluoride, KBF4)
is reacted with aluminium within the melt to produce boron, which
then reacts with titanium within the melt; and/or
(b) a titanium-containing salt (e.g. potassium fluorotitanate,
preferably potassium hexafluorotitanate, K2TiF6) is reacted with
aluminium within the melt to produce titanium, which then reacts with
boron within the melt.
These procedures are generally as employed in the grain refiner art for making titanium-boron-aluminium grain refiners. Preferably, both (a) and (b) apply; in such cases the boron-containing and titanium-containing salts are preferably added as a mixture (generally in stoichiometric proportions) at a controlled rate. However, (a) may apply without (b) (e.g. where the metal melt is an aluminium-titanium alloy); and (b) may apply without (a) (e.g. where the metal melt is an aluminium-boron alloy). We recommend that the reaction temperature be kept below 1000 degrees C, and that the reaction should be carried in an electric induction furnace.
We have found that a concentrated supply of ceramic particles made in accordance with the teachings of the invention can surprisingly easily be incorporated into an aluminium-based melt with full wetting of the ceramic particles. In particular we have found it possible to achieve such incorporation with aluminium-based melts which are at substantially less than 1000 degrees C, and also when the incorporation is carried out in air.
We expect that it will be possible to incorporate a concentrated supply of ceramic particles made in accordance with the invention with similar ease into other melts (e.g. magnesium-based melts), also with full wetting of the ceramic particles.
A concentrated supply of ceramic particles made in accordance with the invention may also be used to make a metal matrix composite, by forming a mixture comprising a supply of suitable matrix metal (such as aluminium or an aluminium alloy, for example, or any other metal which when molten will wet the ceramic particles) and the concentrated supply of ceramic particles, and subjecting the mixture to a suitable powder metallurgical process. Use of such a procedure can attain relatively high ceramic particle loadings, in the resulting metal matrix composite, such as from 15 up to about 60 weight percent. Because of the good wettability of the ceramic particles, the resulting metal matrix composite can be expected to have good mechanical properties such as strength.
In order that the invention may be more fully understood, an embodiment in the accordance therewith will now be described in the following Example, with reference to the single Figure of the accompanying drawing, which shows a micrograph formed by a scanning electron microscope, at a magnification of 7000, of the titanium diboride particles produced in the Example.
Example
Approximately 20 kg of aluminium was melted in a carbon bonded silicon carbide crucible by induction heating. At a starting temperature of 660 degrees C an intimate mixture of K2TiF6 and KBF4 was fed into the aluminium while stirring the aluminium by induction. The K2TiF6 and KBF4 salts were in the stoichiometric ratio required to produce titanium diboride,
TiB2, ceramic particles. The exothermic heat of reaction caused the temperature of the melt to rise but was kept below 1000 degrees C.
Sufficient salt was reacted to produce a melt of aluminium with approximately 8 wt.% TiB2. Potassium aluminium fluoride produced as a by-product of the reaction was removed from the surface of the melt. The resulting dispersion of titanium diboride particles in aluminium was then cast to billet. Most of these TiB2 particles are below one micron in diameter, as seen under an optical microscope.
A 100 g piece taken from the billet was placed in a glass beaker, and about 1 1 of 17 percent aqueous caustic soda solution at about 20 degrees C was added to it. The resulting mixture was heated to about 60 degrees C and maintained under agitation until substantially all of the aluminium had been extracted, after about one hour. The residue was allowed to settle, washed by decantation in distilled water and dried.
A sample of the resulting TiB2 particles is shown in the Figure, from which it can be seen that the particles are of generally tabular (i.e. plate-like) shape, typically having a diameter of about 2.5 microns or less and a thickness of about 0.1 micron. Thus, the majority are equivalent in mass to spherical particles of less than 1 micron in diameter; this accords with what was observed under the optical microscope prior to extraction of the aluminium.
1 g of the extracted TiB2 particles was then added to the surface of a melt of 100 g of aluminium held at 730 degrees C in a alumina crucible.
The surface of the aluminium melt was cleaned, by skimming it, immediately prior to adding the TiB2 particles, and the melt was gently stirred during the addition. As soon as they were added to the melt surface, the TiB2 particles were seen to be wetted by the melt, and they then sank into it.
When the same quantity of TiB2 particles supplied by Rhone-Poulenc Chemicals Limited and having an average particle size of 11.8 microns was added in the same manner to an aluminium melt which had been heated and skimmed in the same way and was similarly stirred during the addition, the majority of the particles remained on the melt surface and were pushed to the side of the crucible. Thus, they were clearly not wetted by the melt.
Claims (22)
1. A method of making a concentrated supply of ceramic particles which are wettable when added to an aluminium-based melt, the method comprising forming a dispersion of ceramic particles in a metal melt such that the ceramic particles are thoroughly wetted by the melt, solidifying the melt, and extracting metal from the solidified dispersion, whereby to increase the concentration of ceramic particles in the dispersion.
2. A method according to claim 1, wherein the metal melt in which the dispersion of ceramic particles is formed is an aluminium-based melt.
3. A method according to claim 2, wherein the metal melt in which the dispersion of ceramic particles is formed is a melt of aluminium metal.
4. A method according to claim 2 or claim 3, wherein the solidified dispersion is alkali-leached to extract aluminium, preferably with an aqueous solution comprising caustic soda.
5. A method according to any one of claims 1 to 4, wherein sufficient metal is extracted from the solidified dispersion that the remaining material is of particulate form.
6. A method according to claim 5, wherein substantially all of the metal is extracted from the solidified dispersion.
7. A method according to any one of claims 1 to 6, wherein the majority of the ceramic particles in the product are of mass equivalent to spheres which are less than 1 micron in diameter.
8. A method according to any one of claims 1 to 7, wherein the dispersion of ceramic particles in the metal melt is formed by reacting, within the metal melt, precursors for the ceramic particles.
9. A method according to any one of claims 1 to 8 wherein the ceramic particles comprise titanium diboride.
10. A method according to claim 9, wherein the metal melt is an aluminium-based metal, and a boron-containing salt is reacted with aluminium within the melt to produce boron, which then reacts with titanium within the melt.
11. A method according to claim 10, wherein the boron-containing salt is potassium borofluoride, KBF4.
12. A method according to any one of claims 9 to 11, wherein the metal melt is an aluminium-based melt, and a titanium-containing salt is reacted with aluminium within the melt to produce titanium, which then reacts with boron within the melt.
13. A method according to claim 12, wherein the titanium-containing salt is potassium fluorotitanate.
14. A method according to claim 13, wherein the titanium-containing salt is potassium hexafluorotitanate, K2TiF6.
15. A method according to any one of claims 9 to 14, wherein the ratio of titanium to boron is substantially stoichiometric.
16. A method of making a concentrated supply of ceramic particles, substantially as described in the foregoing Example.
17. A method according to any one of claims 1 to 16, including the additional step of dispersing the product concentrated supply of ceramic particles into an aluminium-based melt.
18. A method according to claim 17, wherein the temperature of the melt into which the product concentrated supply of ceramic particles is dispersed is less than 1000 degrees C.
19. A method according to claim 17 or claim 18, wherein the step of dispersing the product concentrated supply of ceramic particles into the aluminium-based melt is carried out in air.
20. A method according to any one of claim 1 to 16, including the additional step of forming a mixture comprising a supply of matrix metal and the product concentrated supply of ceramic particles, and subjecting the mixture to a powder metallurgical process to form a metal matrix composite.
21. A method according to claim 20, wherein the resulting metal matrix composite contains from 15 to 60 weight percent of the ceramic particles.
22. The product of any one of claims 1 to 21.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB9119239A GB2259309A (en) | 1991-09-09 | 1991-09-09 | Ceramic particles |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB9119239A GB2259309A (en) | 1991-09-09 | 1991-09-09 | Ceramic particles |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| GB9119239D0 GB9119239D0 (en) | 1991-10-23 |
| GB2259309A true GB2259309A (en) | 1993-03-10 |
Family
ID=10701126
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| GB9119239A Withdrawn GB2259309A (en) | 1991-09-09 | 1991-09-09 | Ceramic particles |
Country Status (1)
| Country | Link |
|---|---|
| GB (1) | GB2259309A (en) |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2274467A (en) * | 1993-01-26 | 1994-07-27 | London Scandinavian Metall | Metal matrix alloys |
| GB2288189A (en) * | 1994-03-31 | 1995-10-11 | Brunel University Of West Lond | Ceramic reinforced metal-matrix composites. |
| GB2316092A (en) * | 1996-08-08 | 1998-02-18 | London Scandinavian Metall | Metal matrix composite alloys |
| CN1059710C (en) * | 1997-11-27 | 2000-12-20 | 宝山钢铁(集团)公司 | Preparation of ceramic grain reinforced aluminium-based composite material |
| WO2007052174A1 (en) | 2005-11-02 | 2007-05-10 | Tubitak | Process for producing a grain refining master alloy |
| CN100357468C (en) * | 2005-04-05 | 2007-12-26 | 江苏大学 | Preparation method of endogenous particle reinforced aluminium-based composite material |
| CN102168214A (en) * | 2011-04-15 | 2011-08-31 | 江苏大学 | Preparation method for light high-strength and high-tenacity aluminum-matrix composite material |
| US20130115370A1 (en) * | 2012-05-23 | 2013-05-09 | Shenzhen Sunxing Light Alloys Materials Co.,Ltd | Process for preparing inert anode material or inert cathode coating material for aluminium electrolysis |
| EP2666752A1 (en) * | 2012-05-23 | 2013-11-27 | Shenzhen Sunxing Light Alloys Materials Co., Ltd | Potassium cryolite for aluminum electrolysis industry and preparation method thereof |
| EP2669250A1 (en) * | 2012-05-30 | 2013-12-04 | Shenzhen Sunxing Light Alloys Materials Co., Ltd | Preparation process of transition metal boride and uses thereof |
| CN106591618A (en) * | 2016-12-06 | 2017-04-26 | 昆明理工大学 | Preparation method of endogenous double-phase particle enhanced aluminum-based composite material |
| CN111020343A (en) * | 2019-11-26 | 2020-04-17 | 纽维科精密制造江苏有限公司 | Method for preparing high-mass-fraction particle-reinforced aluminum-based composite material by using in-situ self-generation method |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1103396A (en) * | 1966-02-07 | 1968-02-14 | Int Nickel Ltd | Manufacture of precious metal spheres and spheroids |
| GB1354873A (en) * | 1970-03-07 | 1974-06-05 | Dannohl W | Magnesium-containing alloys and fibre materials |
| EP0113249A1 (en) * | 1982-12-30 | 1984-07-11 | Alcan International Limited | Metallic materials reinforced by a continuous network of a ceramic phase |
| WO1988007593A2 (en) * | 1987-04-03 | 1988-10-06 | Martin Marietta Corporation | Process for forming metal-second phase composites utilizing compound starting materials, and products thereof |
-
1991
- 1991-09-09 GB GB9119239A patent/GB2259309A/en not_active Withdrawn
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1103396A (en) * | 1966-02-07 | 1968-02-14 | Int Nickel Ltd | Manufacture of precious metal spheres and spheroids |
| GB1354873A (en) * | 1970-03-07 | 1974-06-05 | Dannohl W | Magnesium-containing alloys and fibre materials |
| EP0113249A1 (en) * | 1982-12-30 | 1984-07-11 | Alcan International Limited | Metallic materials reinforced by a continuous network of a ceramic phase |
| WO1988007593A2 (en) * | 1987-04-03 | 1988-10-06 | Martin Marietta Corporation | Process for forming metal-second phase composites utilizing compound starting materials, and products thereof |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2274467A (en) * | 1993-01-26 | 1994-07-27 | London Scandinavian Metall | Metal matrix alloys |
| US6099664A (en) * | 1993-01-26 | 2000-08-08 | London & Scandinavian Metallurgical Co., Ltd. | Metal matrix alloys |
| GB2288189A (en) * | 1994-03-31 | 1995-10-11 | Brunel University Of West Lond | Ceramic reinforced metal-matrix composites. |
| GB2316092A (en) * | 1996-08-08 | 1998-02-18 | London Scandinavian Metall | Metal matrix composite alloys |
| CN1059710C (en) * | 1997-11-27 | 2000-12-20 | 宝山钢铁(集团)公司 | Preparation of ceramic grain reinforced aluminium-based composite material |
| CN100357468C (en) * | 2005-04-05 | 2007-12-26 | 江苏大学 | Preparation method of endogenous particle reinforced aluminium-based composite material |
| WO2007052174A1 (en) | 2005-11-02 | 2007-05-10 | Tubitak | Process for producing a grain refining master alloy |
| CN102168214A (en) * | 2011-04-15 | 2011-08-31 | 江苏大学 | Preparation method for light high-strength and high-tenacity aluminum-matrix composite material |
| CN102168214B (en) * | 2011-04-15 | 2013-07-17 | 江苏大学 | Preparation method for light high-strength and high-tenacity aluminum-matrix composite material |
| US20130115370A1 (en) * | 2012-05-23 | 2013-05-09 | Shenzhen Sunxing Light Alloys Materials Co.,Ltd | Process for preparing inert anode material or inert cathode coating material for aluminium electrolysis |
| EP2666752A1 (en) * | 2012-05-23 | 2013-11-27 | Shenzhen Sunxing Light Alloys Materials Co., Ltd | Potassium cryolite for aluminum electrolysis industry and preparation method thereof |
| EP2669250A1 (en) * | 2012-05-30 | 2013-12-04 | Shenzhen Sunxing Light Alloys Materials Co., Ltd | Preparation process of transition metal boride and uses thereof |
| CN106591618A (en) * | 2016-12-06 | 2017-04-26 | 昆明理工大学 | Preparation method of endogenous double-phase particle enhanced aluminum-based composite material |
| CN111020343A (en) * | 2019-11-26 | 2020-04-17 | 纽维科精密制造江苏有限公司 | Method for preparing high-mass-fraction particle-reinforced aluminum-based composite material by using in-situ self-generation method |
Also Published As
| Publication number | Publication date |
|---|---|
| GB9119239D0 (en) | 1991-10-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US6723282B1 (en) | Metal product containing ceramic dispersoids form in-situ | |
| CA1329023C (en) | Process for forming metal-second phase composites and product thereof | |
| CA1289748C (en) | Producing titanium carbide | |
| US4753690A (en) | Method for producing composite material having an aluminum alloy matrix with a silicon carbide reinforcement | |
| US4662429A (en) | Composite material having matrix of aluminum or aluminum alloy with dispersed fibrous or particulate reinforcement | |
| Tjong et al. | Microstructural and mechanical characteristics of in situ metal matrix composites | |
| US6290748B1 (en) | TiB2 particulate ceramic reinforced Al-alloy metal-matrix composites | |
| Chrysanthou et al. | Production of copper-matrix composites by in situ processing | |
| US6036792A (en) | Liquid-state-in-situ-formed ceramic particles in metals and alloys | |
| EP0556367B1 (en) | Process for making a castable aluminium-based composite alloy | |
| JPS6383239A (en) | Production of metal-ceramic composite | |
| WO1992013978A1 (en) | High strength, high stiffness magnesium base metal alloy composites | |
| GB2259309A (en) | Ceramic particles | |
| EP0113249A1 (en) | Metallic materials reinforced by a continuous network of a ceramic phase | |
| US5573607A (en) | Metal matrix composites of aluminum, magnesium and titanium using silicon borides | |
| JP2743720B2 (en) | Method for producing TiB2 dispersed TiAl-based composite material | |
| CN101148721B (en) | Aluminum-base composite material and preparation method thereof | |
| US6843865B2 (en) | Aluminum alloy product refinement and applications of aluminum alloy product refinement | |
| Gobalakrishnan et al. | Mechanical properties of Al 6061/TiB2 in-situ formed metal matrix composites | |
| Ehrström et al. | Production of rapidly solidified Al/SiC composites | |
| US6398882B1 (en) | Uniformly dispersed, finely sized ceramic particles in metals and alloys | |
| GB2171723A (en) | Producing an alloy containing titanium carbide | |
| Abdelkareem | Thermodynamic analysis of Al alloy reinforced with zirconia particles | |
| WO1998006880A1 (en) | Metal matrix composite alloys | |
| JPS5839757A (en) | Manufacture of composite body |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| WAP | Application withdrawn, taken to be withdrawn or refused ** after publication under section 16(1) |