AU600030B2

AU600030B2 - Particulate metal composites

Info

Publication number: AU600030B2
Application number: AU78868/87A
Authority: AU
Inventors: Ian Robert Hughes; Richard Michael Jordan; Treve Courtney Willis
Original assignee: Alcan International Ltd Canada
Current assignee: Rio Tinto Alcan International Ltd
Priority date: 1986-09-24
Filing date: 1987-09-23
Publication date: 1990-08-02
Anticipated expiration: 2007-09-23
Also published as: EP0262869A1; ZA877089B; KR880003688A; BR8704882A; JPS63140001A; CN1012803B; AU7886887A; CN87106831A; GB8622949D0

Description

s 3 COMMONWEALTH OF AUSTRALIA PATENTS ACT 1952.69 COMPLETE SPECIFICATION

(ORIGINAL)

Class Application Number: Lodged: Int. Class Complhte Specification Lodged: Accepted: Published: Priority Related Art: Name of Applicant: Address of Applicant: Actual Inventor: Address for Service ALCAN INTERNATIONAL LILMITED 1188 Sherbrooke Street West, Montreal, Quebec, Canada RICHARD MICHAEL JORDAN, IAN ROBERT HUGHES and TREVE COURTNEY WILLIS EDWD. WATERS SONS, 50 QUEEN STREET, MELBOURNE, AUSTRALIA, 3000.

Complete Specification for the invention entitled: PARTICULATE METAL COMPOSITES The following statement is a full description of this invention, including the best method of performing it known to US 1i.

I

~I rrrrr~-~ I PARTICULATE METAL COMPOSITES This invention relates to particulate composites in which the particles have a continuous phase of a metal eg an Al alloy.

EPA 105595 describes Al alloys containing substantial proportions of Cr, Zr and Mn. Rapid cooling of the molten alloy e.g. by spraying or splatcasting, result's in a particulate solid in which the bulk of the alloying additions are retained in solid solution. This material can be consolidated by powder 4Qo metallurgy techniques to a product which can be ageo~hardened at a temperature of 3000 to 500°C and which t Iretains its strength for long periods at temperatures SaIof 150 C to 450 C.

I It 15 EPA 128260 describes a technique employing metal vapour to make composite particles below 10 microns.

GB 2115014 describes a method of making a massive not particulate) product by combining molten metal droplets with fine refractory material.

DE 2124199 describes an atomisation method of making metal powders whose particle surfaces are coated with fine refractory material.

EPA 147769 describes a method of making particulate composites of Al alloys with fine refractory material, by mechanical alloying.

GB 1548616 is one of a family of patents relating Sto the manufacture of spray deposited preforms from which articles of precise shape can be produced e.g. by forging, pressing or machining. A stream of molten metal alloy is atomised by means of high velocity jets of gas and the resultant spray of hot metal particles is directed onto a shaped collecting surface to form a coherent deposit. The patent describes how a proportion of the particles may miss the target and collect as a powder or aggregate of overspray material which is not convenient for re-cycling and, it is -2 implied, not useful for other purposes.

EPA 198607 describes a method of making a metal matrix composite comprising the steps of atomising a stream of molten metal to form a spray of hot metal particles by subjecting the stream to relatively cold gas directed at the stream, applying to the stream or spray fine solid particles of a material of different composition from the metal, and depositing the metal, having said fine particles incorporated therein, in coherent form on a collecting surface. The fine particulate material enhances physical and mechanical properties of the metal matrix. The metal may be Al and the particulate material may be SiC.

When the method of EPA 198607 is operated, a S 15 proportion of the metal particles is generally not o o* deposited on the collecting surface, and is collected downstream as a powder or aggregate. The present invention is based on the following observation .o regarding the overspray. When a finely divided 20 refractory material has been applied to the stream or 0 0 o spray of molten metal, the refractory material is found, not only in the coherent deposit formed on the collecting surface, but also associated with the metal in the overspray. The refractory material is present in the overspray, not only on the surface of the solidified particles of metal, but also rather uniformly distributed within the interior of the particles. This observation was unexpected. It hiad not previously been realized that the refractory material became associated with the molten metal spray prior to deposition on a collecting surface. Indeed, the prior art noted above indicates that such association would not take place.

The present invention provides a particu!ate composite, made by combining molten metal droplets with fine refractory material, in which the particles have a 3 continuous phase of the metal and a disperse phase, incorporated in the continuous phase, of the refractory material.

The invention is of particular interest when the metal is an Al alloy, as the technique of atomising molten Al alloys is quite well developed. But the invention is applicable to other materials that can be sprayed in the form of molten droplets, such as for example, steel, nickel, cobalt, copper, titanium and magnesium.

The particulate composite has been made by 0 combining molten metal droplets with fine refractory material. Even when spray casting is carried out in an oinert atmosphere, so far as Al alloys are concerned, the resulting particles necessarily have at least a °o0 thin oxide coating on their surface. The particles do not normally contain any internal oxide inclusions unless this is deliberately added in (or as) the fine 00 ",refractory material. By contrast, a particulate o 20 composite of an Al alloy made by mechanical alloying would necessarily contain internal oxide inclusions.

The particles of the composite generally have a size in the range from 10 to 500 microns, preferably CI O* with an average diameter of from 20 to 80 microns.

o 25 When the particles are formed by spray casting, their 04 diameter can be controlled by controlling the atomising conditions, as is known in the art. Although they may be flattened, e.g. as a result of splat-casting, the composite particles are preferably spherical.

The refractory material may be another me~al of higher melting point than the metal, but is preferably an oxide, boride, carbide or nitride.

Ceramic materials of this kind, some of which are known as refractory hard metals, are well known, and preferred examples include SiC, Al 0 MgO, TiC and boron carbide. These refractory materials are 4 preferably used in the form of particles having average diameters, below 50 microns and down to sub-micron size. Particles of 5 to 20 microns are often convenient to use.

in the composite particles, the disperse phase and the continuous phase are preferably present in volume concentrations of 0.5 to 50% and 99.5 to respectively. Particularly when used in a volume concentration of 10 to 30%, high strength high modulus refractory powders can impart substantial strengthening and modulus properties to the composite.

The matrix metal may be an Al alloy containing on or more conventional age- and solution-hardening ingredients such as Zn, Mg, An, Si, Li, and optionally also one or more transition metal elements for grain refining purposes.

Or the Al alloy may contain at least one transition metal alloying ingredient having agehardening, or solution strengthening properties, such 20 as for example Cr, Zr, Mn, Fe, Co and Ce. Preferred are alloys containing 0.5% to 7% by weight Cr, 0.5% to 4 2.5% by weight Zr and 0.1% to 4.0% by weight Mn.

These alloying ingredients are difficult to get into solid solution in Al by conventional means, but this problem is solved by the spray-casting technique described below. These transition metal alloying elements have the advantage of providing age-hardening properties at elevated temperatures typically in the range 300 0 C-500 0

C.

The tranvition metal alloying ingredients are preferably prespit at least partly, and preferably totally, in solid (supersaturated) solution in the metal. When not in solid solution, the alloying ingredients should be present as a fine dispersion.

To achieve this, it is necessary to cool the molten metal rapidly at about 100C sec for a fine dispersion, and at about 10 0 C sec for solid solution. Depending on particle size, these are cooling rates which can be achieved by spray-casting.

In another aspect, the invention provides a method of making the particulate composite herein described, which method comprises atomising a stream of the molten metal to form a spray of metil particles by subjecting the stream to relatively cold inert gas directed at the stream, applying to the stream or spray fine solid particles of a refractory material, allowing the metal particles to solidify, and collecting the resulting I9 particulate composite.

Preferably, the solid particles of refractory material are applied to the stream of molten metal just before this is broken up into spray. In order to obtain spherical particles it is, of course, necessary that the metal particles solidify before impact with any solid surface. For Al alloys the inert gas may conveniently be argon or preferably nitrogen.

Providing the oxygen partial pressure is sufficiently low, the composite particles come out spherical with no more than a thin coating of aluminium oxide. The spray of molten metal particles may be directed at a collecting surface, in which case a particulate composite is recovered as a by-product. Alternatively, the spray conditions may be chosen such that the metal particles solidify before impact with any solid surface.

The nature of the Al alloy is not critical to the invention. The method has been employed to make particulate composites using SiC as the refractory material with the following: commercially pure aluminium, AA 2014, 2024, 2618, 6061, 7075, 7475, 8090, LM 13, A 3210, Al-12% Si, Al-20% Si and Al-6% Sn.

The particulate composite is amenable to further processing via known powder metallurgy routes 6such as canning, degassing, compacting and extruding to solid eg semi-fabricated or fully fabricated products.

Possible applications include extruding directly to form air-frame structures; extruding bar and forging to give gas-turbine compressor blades or pistons for internal combustion engines; or extruding plate and rolling to sheet for the skins of aircraft.

Reference is directed to accompanying drawing which is a diagram of an atomisation system suitable for making particulate composites of the invention.

The system comprises a molten metal nozzle 10 from o00 which is passing by gravity a stream 12 of molten o0.6 %metal. Surrounding the molten metal nozzle is a primary gas nozzle 14, with apertures to direct a o o 15 primary support gas flow 16, parallel to and OVID surrounding the metal stream, to shroud and contain the O0 omolten metal. Surrounding the primary gas nozzle is a secondary gas nozzle 18 provided with jets 19 which Sdirect a secondary atomising gas stream 20 towards the o 20 molten metal stream. The secondary gas stream contacts 0 Q 0€ the molten metal stream a distance h downstream of the molten metal nozzle and atomises it into a spray 22 of metal particles.

The secondary atomising gas flow 20 defines a cone 25 of height h and radius equal to the distance of the *o C motjets 19 from the metal stream 12. The refractory material 24, entrained in a carrier gas, is introduced into this cone via a pipe 26. The carrier gas flow rate is typically several orders of magnitude less than the flow rate of the secondary atomising gas The position at which the carrier material is introduced within the cone is not critical; it could for example be inside, rather than outside, the primary gas nozzle 14. If the distance h is sufficiently small, it is possible to dispense with the primary gas nozzle altogether.

The refractory material loading in the carrier gas, and the carrier gas flow rate relative to the metal flow rate and the secondary (atomising) gas flow rate determine the concentrations of refractory material in the particulate composite produced. The temperature and flow rate of the atomising gas determine the rate at which the atomised metal i particles solidify.

SThe following examples illustrate the invention.

iat Example 1 iA typical experiment resulting in the formation of composite powder (18% of 13 microns SiC powder into AA 2014 alloy) was carried out using the following parameters in a system as shown in the figure:- S(a) Temp. of molten metal 705 0

C

i(b) Primary gas pressure 0.25 MPa 3 -1 1 ii flow rate 0.4m 3 min I approx velocity 240 m sec Secondary gas pressure 0. 55 MPa flow rate 6.0 m 3 min i *-I approx velocity 300 m sec -3 Carrier gas SiC loading 30 kg m Carrier gas flow rates 0.03 m 3 min 1 The product collected consisted of some SiC that did not get incorporated, along with the desired product, which was characterised as follows:- Composite powder size range 10-500 microns Mean size of composite 80 microns SiC size range in composite 6-45 microns Mean size of SiC in composite 13 microns Vol SiC in the composite powder 18% The SiC and Al-SiC composite powders can be separated either by sieving or by gas separation/ classification techniques. An optical section through the composite particles shows comminuted SiC uniformly distributed through the metal matrix.

j i'i 1 i T 8 Example 2 The amount of SiC (or other refractory material) incorporated is dependent on the composition of the Al alloy used and on the atomising conditions. The following table reports the SiC incorporated in a series of experimental runs performed under the same general conditions as Example 1. The SiC was determined by sieving the particulate composite to -150 to +38 microns (thereby excluding SiC particles not associated with Al metal), followed by chemical dissolution of the matrix and weighing.

SiC Secondary Atomising Pressure and Mean Diameter Alloy Weight Volume Secondary Composite 15 SiC SiC Pressure Mean Diam 4 41 4i 4 4 o 4 4 4

IP

2014 6061 2014 20 2014 2014 8090 2014 21.3 28.4 14.5 12.0 17.3 5.5 12.2 18.6 8.0 24.8 F .0 12.6 '.0 10.5 5.3 15.1 6.3 4.4 5.8 10.6 4.7 67.4 68.6 68.8 78.0 70.8 69.2 71.5 Example 3 Two experiments have been conducted both using 2014 alloy and the same powder production conditions as in Example 1. They differ in their processing after the powder production phase.

Experiment

A

The as produced powder was sieved to <1501m and then air classified to 4 5m producing a composite powder in the size range 45-150m. The powder was placed in a can (170 mm diameter by 647 mm length) made of 6082 alloy and degassed at 325 C for 4 hours under 4- -9 vacuum. The can and powder were then hot compacted at 3500C in a commercial press. After cooling the can was machined away.

The hot compacted billet was extruded using an indirect press to a rectangular section 63 mm x 14 mm corresponding to an extrusion ratio of 26:1.

The as-extruded bar was solution heat treated for 1 hr at 505 0 C, water quenched, and artificially aged for 8 hr at 175 0 C. Tensile test data was obtained using round bar tensiles machined parallel to the extrusion direction.

Experiment

B

0 The as-produced powder was sieved to <150 m and 0 Ir 0 o aO then air classified to >25 m producing a composite o0on 15 powder in the size range 25-150 m. The powder was 0° 0placed in a can (74 mm diameter by 200 mm length) made of 2024 alloy. Two degassing conditions were used; 4 hrs at 3250C and 1 hr at 530 0 C under vacuum. The cans 000 o were sealed and then put into a furnace at 300 C for min and then extruded. The extrusion conditions were; container temperature 300 0 C, billet temperature 3000C, P000 S4: breakthrough pressures <1000 N/mm ram speed 12 mm/sec. The extruded cross section was 19 mm round bar corresponding to an extrusion ratio of 15:1.

The as-extruded bar was solution heat treated for 1 hr at 5050C, water quenched, and artificially aged for 8 hr at 1750C. Tensile test data was obtained S~Iusing round bar tensiles machined parallel to the extrusion direction.

The test results are reported in the following table, together with comparative data on the unreinforced 2014 alloy. The composites of the invention show higher modulus with no loss of tensile strength.

10 Property Experiment

A

Experiment B Degassing Temperature 325 00 53000C 2014 0.2% PS (MPa) TS (MPa) Ef E (GPa) 430 474 3.7 87 414.2 462.7 2.3 96.0 442.4 491 .7 1 .5 90.4 429 476 7. 73 a no 0~ 0 000 0 00 .0 0 a 4.

proof strength tensile strength elongation to failure elastic modulus

II

I

00 0' a 0

Claims

1. A particulate composite, made by combining molten metal droplets with fine refractory material, in which the particles have a continuous phase of the metal and a disperse phase, incorporated in the continuous phase, of the refractory material.

2. A particulate composite as clained in claim 1, wherein the metal is an Al alloy.

3. A particulate composite as claimed in claim 2, wherein the Al alloy includes at least one transition metal element at least partly in solid solution.

4. A particulate composite as claimed in any one of o claims 1 to 3, wherein the particles are spherical. o 15

5. A particulate composite as claimed in any one of claims 1 to 4, wherein the refractory material is an oxide, boride, carbide or nitride.

6. A particulate composite as claimed in any one of a' claims 1 to 4, wherein the particles have a size in the range 10-500 microns.

7. A particulate composite as claimed in any one of claims 1 to 6, wherein the refractory material is in the form of particles having an average diameter of up to 50 microns.

8. A particulate composite as claimed in any one of claims 1 to 7, wherein the refractory material is uniformly distributed within the particles. 7

9. A particulate composite as claimed in any one of ;claims 1 to 8, wherein the continuous phase is of an Al alloy containing a transition metal element selected from 0.5% to 7.0% by weight Cr, 0.5% to 2.5% weight Zr, and 0.1% to 4.0% by weight Mn.

A method of making the particulate composite claimed in any one of claims 1 to 9, which method comprises atomising a stream of a molten metal to form a spray of metal particles by 21jbjecting the stream to I 12 relatively cold inert gas directed at the stream, applying to the stream or spray fine solid particles of a refractory material, allowing the metal particles to solidify, and collecting the resulting particulate composite.

11. A method as claimed in claim 10, wherein the solid particles of refractory material are applied to the stream of molten metal.

12. A solid body formed by compacting the partizulate composite of any one of claims 1 to 9. DATED this 23rd day of September 1987. ALCAN INTERNATIONAL LIMITED EDWD. WATERS SONS PATENT ATTORNEYS QUEEN STREET MELBOURNE. VIC. 3000. t 4