CN1675388A

CN1675388A - Metal matrix composites, and methods for making the same

Info

Publication number: CN1675388A
Application number: CNA038197588A
Authority: CN
Inventors: 卡玛尔·E·阿明; 迈克尔·F·格雷瑟; 阿兰·R·霍尔茨; 小威廉·J·赛特泽尔; 约瑟夫·J·施米特; 保罗·S·沃纳
Original assignee: 3M Innovative Properties Co
Current assignee: 3M Innovative Properties Co
Priority date: 2002-08-20
Filing date: 2003-07-08
Publication date: 2005-09-28
Also published as: WO2004018718A1; JP2005536641A; KR20050058350A; EP1570095A1; AU2003251789A1

Abstract

Metal comprising inserts for reinforcing a metal matrix composite article and methods of making the same. In another aspect, the present invention provides metal matrix composite articles reinforced with an insert(s) and methods of making the same. Useful metal matrix composite articles comprising the inserts include brake calipers.

Description

Metal-matrix composite and preparation method thereof

Invention field

The present invention relates to be used to strengthen the inset that contains metal of metal-matrix composite goods and with inset enhanced metal-matrix composite goods.

Description of Related Art

With ceramic reinforced metal matrix is knownly (to see also for example United States Patent (USP) 4,705,093 (Ogino) in the art, 4,852,630 (people such as Hamajima), 4,932,099 (people such as Corwin), 5,199,481 (people such as Corwin), 5,234,080 (Pantale) and 5,394,930 (Kennerknecht); Be disclosed in English Patent 2,182,970 A on May 28th, 1987 and on September 14th, 1988 and B number respectively; Announcement WO 02/26658, WO 02/27048 that on April 4th, 2002 announced and the PCT of WO 02/27049 application.The example that is used for the enhanced stupalith comprises particle, discontinuous fiber (comprising filament) and successive fiber and ceramic preform.

Usually, stupalith is added in the metal, and so that metal-matrix composite (MMC) to be provided, it is compared with the goods that the metal that does not add stupalith makes, and mechanical property increases.For example the conventional brake of Motor vehicles pincers (for example car and truck) are made by cast iron usually.For reducing the gross weight of vehicle, especially be non-spring-load weight such as caliper, need to use the element and/or the material of weight.A kind of method that is used to design MMC is finite element analysis, is included as the aequum that application-specific is placed ceramic oxide material and minimized ceramic oxide material.

The caliper of being made by cast aluminium compares by the gently about 50wt.% of castiron identical (being same size and structure) caliper.The mechanical property of cast aluminium and cast iron is inequality, and (for example the Young's modulus of cast iron is about 100-170GPa, and the Young's modulus of cast aluminium is about 70-75GPa; The yield strength of cast iron is 300-700MPa, and the yield strength of cast aluminium is 200-3000MPa).Therefore, for intended size and shape, its mechanical property of caliper made by cast aluminium such as bending hardness and yield strength are starkly lower than cast-iron caliper.Usually, the mechanical property of this aluminium caliper is compared with cast-iron caliper and is low to moderate unacceptable degree.Need be identical with the cast-iron caliper structure compared by the caliper that aluminum metal-matrix composite material (for example using ceramic fiber enhanced aluminium) makes, and mechanical property such as bending hardness identical at least with yield strength (or better).

A kind of consideration for some MMC goods is to need to form post-treatment (for example add hole or screw thread, or cutting material being to provide needed shape) or other processing (for example two MMC goods being welded together, to make the part of complicated shape).Many conventional MMC contain the ceramic reinforcing material of capacity usually, thus make processing or the welding be unpractiaca or or even impossible.Yet need preparation " net form " goods, and require to become processing or processing after the less shape.The method of preparation " net form " goods is known (for example seeing also United States Patent (USP) 5,234,045 (Cisko) and 5,887,684 people such as () Doll) in the art.In addition or selectively, on certain practical level, can reduce pottery and strengthen, or be not placed on can influence processing or other handle as zones of welding.

Another kind at design and preparation MMC considers it is the cost of ceramic reinforcing material.Continuously the mechanical property of polycrystalline Alpha-alumina fiber (as by 3M Company, those that St.Paul, MN sell with trade(brand)name " NEXTEL610 ") is higher than low density metals such as aluminium.In addition, be higher than metal such as aluminium basically on the cost of ceramic oxide material such as polycrystalline Alpha-alumina fiber.Therefore, need minimize institute's consumption of ceramic oxide material, and the placement of optimization ceramic oxide material, with the performance of maximization ceramic oxide material generation.

In addition, ceramic reinforcing material need be in packing, provided, or the metal-matrix composite goods can be relatively easily prepared from ceramic reinforcing material.

Although announcement WO 02/26658, WO 02/27048 that on April 4th, 2002 announced and the PCT of WO 02/27049 application comprise the explanation that ceramic reinforcing material need be provided or can relatively easily prepare the embodiment of metal-matrix composite goods from ceramic reinforcing material solving in packing, but also need to provide extra scheme and/or selectable other novel methods of metal-matrix composite goods, preferably it has more superior performance than common metal groundmass composite material goods.

Summary of the invention

In one aspect, the invention provides and be used to inset that strengthens in the metal-matrix composite goods and preparation method thereof.In one aspect of the method, the invention provides with inset (for example, two, three, four, five, six or more a plurality of inset) enhanced metal-matrix composite goods and preparation method thereof.

The embodiment of metal-matrix composite goods of the present invention that is used for strengthening the inset of metal-matrix composite goods of the present invention comprises and is at least 8 microns (in certain embodiments, preferably be at least 10 microns, be at least 12 microns or even be at least 15 microns; More preferably 12～15 microns) be the metal (for example silver, gold, its alloy and combination thereof) of positive Gibbs oxidation free energy when being higher than at least 200 ℃.This embodiment can provide the metal-matrix composite goods usually, the combination that has utmost point needs at the inset and the intermetallic of the metal-matrix composite goods that comprise inset (for example in certain embodiments, the preferred combination interface does not contain aerobic and/or the bonding strength peak value is at least 100MPa (in certain embodiments, preferably be at least 125MPa, be at least 150MPa, be at least 175 or even be at least 180MPa)).Although without wishing to be held to theory, can think when being higher than at least 200 ℃ be positive Gibbs oxidation free energy metal have inset and a melts combine that helps make the metal-matrix composite goods that comprise inset.In addition, although without wishing to be held to theory, can think when being higher than 200 ℃ to be that the have inset and the intermetallic interface that help make the metal-matrix composite goods that comprise inset of metal of positive Gibbs oxidation free energy do not contain aerobic at least.

In one embodiment, the invention provides first kind of metal-matrix composite goods (for example being used to strengthen the inset of metal-matrix composite goods) comprising:

Basically the successive ceramic oxide fibers and be selected from aluminium, (for example 200,300,400,700 and/or 6000 series (in certain embodiments for its alloy, preferred 200 series) aluminium alloy) and the combination first kind of metal, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this first kind of metal is along this at least a portion extension of the length of successive ceramic oxide fibers basically, and this first kind of metal comprises outside surface; And

Second kind of metal on this first kind of outer metallic surface, this second kind of metal is positive Gibbs oxidation free energy (for example silver, gold, its alloy and combination thereof) when being higher than at least 200 ℃, this second kind of its thickness of metal is at least 8 microns (in certain embodiments, preferably be at least 10 microns, be at least 12 microns or even be at least 15 microns; More preferably 12～15 microns; In one aspect of the method, usually less than 20 microns).

Selectively, these first kind of metal-matrix composite goods also is included in the third metal (for example Ni) between the outside surface of this second kind of metal and this first kind of metal.

In one aspect of the method, the invention provides the method for preparation first kind of metal-matrix composite goods of the present invention, this method comprises:

Be selected from aluminium, (for example 200,300,400,700 and/or 6000 series (in certain embodiments for its alloy, preferred 200 series) fixing successive ceramic oxide fibers basically aluminium alloy) and in first kind of metal of combination, make this first kind of metal along this at least a portion extension of the length of successive ceramic oxide fibers basically, this first kind of metal comprises outside surface; And

Provide second kind of metal so that this metal-matrix composite goods to be provided on the outside surface of this first kind of metal, this second kind of metal is positive Gibbs oxidation free energy (for example silver, gold, its alloy and combination thereof) when being higher than at least 200 ℃.

In an embodiment preferred of first kind of metal matrix goods of the present invention, the invention provides second kind of metal-matrix composite goods (for example being used to strengthen the inset of metal-matrix composite goods) and comprising:

Basically the successive ceramic oxide fibers and be selected from aluminium, (for example 200,300,400,700 and/or 6000 series (in certain embodiments for its alloy, preferred 200 series) aluminium alloy) and the combination metal, wherein this metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this metal is along this at least a portion extension of the length of successive ceramic oxide fibers basically, and this metal comprises outside surface;

Ni is on the outside surface of this metal, and Ni comprises outside surface; And

Ag on the outside surface of Ni, Ag thickness be at least 8 microns (in certain embodiments, be preferably 10 microns, 12 microns or even 15 microns; More preferably 12～15 microns; In one aspect of the method, usually less than 20 microns).

In one aspect of the method, the invention provides the method for preparation second kind of metal-matrix composite goods of the present invention, this method comprises:

Fixing successive ceramic oxide fibers basically in the metal that is selected from aluminium, its alloy and combination thereof makes this metal along this at least a portion extension of the length of successive ceramic oxide fibers basically, and this metal comprises outside surface; And

Provide Ni on the outside surface of this metal, Ni comprises outside surface; And

On the outside surface of Ni, provide Ag,

So that this metal-matrix composite goods to be provided.

In one embodiment, the invention provides the third metal-matrix composite goods, the inset that it comprises first kind of metal and strengthens this first kind of metal, wherein this first kind of metal is selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (in certain embodiments, preferred 300 or 400 series) aluminium alloy) and the combination, wherein this inset comprises basically the successive ceramic oxide fibers and is selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (in certain embodiments, preferred 200 series) aluminium alloy) and the combination second kind of metal, wherein this second kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, wherein this second kind of metal is along this at least a portion extension of the length of successive ceramic oxide fibers basically, wherein between this first kind of metal and this inset, interfacial layer is arranged, and wherein the interfacial layer bonding strength peak value between this first kind of metal and this inset is at least 100MPa (in certain embodiments, preferably be at least 125MPa, be at least 150MPa, be at least 175 or even be at least 180MPa).In certain embodiments, preferably this interfacial layer does not contain aerobic.In one aspect of the method, this interfacial layer can comprise mean vol is the metal (for example silver, gold, its alloy and combination thereof) of positive Gibbs oxidation free energy when being higher than at least 200 ℃, and the mean vol of this metal height (for example be at least 15,20,25,30,35,40,45 or even 50wt.%) in this interfacial layer than in this first kind of metal wherein.In one aspect of the method, this interfacial layer can comprise the Ag that is higher than the mean vol in this first kind of metal and Ni (for example among Ag and the Ni each be at least 15,20,25,30,35,40,45 or even 50wt.%).In one aspect of the method, each all has fusing point this first kind and this second kind of metal, and wherein the fusing point of this second kind of metal is at least 10 ℃, 15 ℃, 20 ℃, 25 ℃, 30 ℃, 35 ℃, 40 ℃, 45 ℃ or even 50 ℃ and be higher than the fusing point of this first kind of metal.In one aspect of the method, this first kind of metal and second kind of metal can different (for example aluminium and aluminium alloy or different aluminium alloys).

Selectively, these the third metal-matrix composite goods comprise two, three, four, five, six or more a plurality of inset.Selectively, this inset has identical or different composition, or some inset has same composition, and other have different the composition.

In one aspect of the method, the invention provides the method for preparation the third metal-matrix composite goods of the present invention, this method comprises:

Inset is put into mould, this inset comprises basically the successive ceramic oxide fibers and is selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (in certain embodiments, preferred 200 series) aluminium alloy) and the combination first kind of metal, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this first kind of metal along this basically at least a portion of the length of successive ceramic oxide fibers extend, this first kind of metal comprises outside surface, and second kind of metal on this first kind of outer metallic surface, this second kind of metal is that positive Gibbs oxidation free energy is (for example silver-colored when being higher than at least 200 ℃, gold, its alloy and combination thereof);

The third metal of fusion that will be selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (preferred 300 or 400 series in certain embodiments) aluminium alloy) and combination thereof is put into mould; And

Cool off the third metal of this fusion so that the metal-matrix composite goods to be provided.

In one aspect of the method, the invention provides the method for the third metal-matrix composite goods of the preparation preferred embodiment of the invention, this method comprises:

Inset is put into mould, this inset comprises basically the successive ceramic oxide fibers and is selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (in certain embodiments, preferred 200 series) aluminium alloy) and the combination first kind of metal, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this first kind of metal along this basically at least a portion of the length of successive ceramic oxide fibers extend, this first kind of metal comprises outside surface, Ni is on this first kind of outer metallic surface, Ni comprises outside surface, and Ag is on the outside surface of Ni;

Second kind of metal of fusion that will be selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (preferred 300 or 400 series in certain embodiments) aluminium alloy) and combination thereof put into mould; And

Cool off second kind of metal of this fusion so that this metal-matrix composite goods to be provided.

In one aspect of the method, the invention provides the method for preparing the metal-matrix composite inset, this inset is used to prepare the metal-matrix composite goods, and this method comprises:

Design metal-matrix composite goods strengthen inset to comprise metal-matrix composite, and this inset comprises:

Basically the successive ceramic oxide fibers and be selected from aluminium, (for example 200,300,400,700 and/or 6000 series (in certain embodiments for its alloy, preferred 200 series) aluminium alloy) and the combination first kind of metal, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this first kind of metal along this basically at least a portion of the length of successive ceramic oxide fibers extend; And

Prepare metal-matrix composite by the design that obtains and strengthen inset, it comprises:

Successive ceramic oxide fibers and this are selected from first kind of metal of aluminium, its alloy and combination thereof basically for these, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this first kind of metal is along this at least a portion extension of the length of successive ceramic oxide fibers basically, and this first kind of metal comprises outside surface; And also comprise:

Second kind of metal on this first kind of outer metallic surface, this second kind of metal is positive Gibbs oxidation free energy (for example silver, gold, its alloy and combination thereof) when being higher than at least 200 ℃, this second kind of its thickness of metal be at least 8 microns (in certain embodiments, be preferably 10 microns, 12 microns or even 15 microns; More preferably 12～15 microns; In one aspect of the method, usually less than 20 microns).

Basically the successive ceramic oxide fibers and be selected from aluminium, (for example 200,300,400,700 and/or 6000 series (in certain embodiments for its alloy, preferred 200 series) aluminium alloy) and the combination metal, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this metal along this basically at least a portion of the length of successive ceramic oxide fibers extend; And

Successive ceramic oxide fibers and this are selected from the metal of aluminium, its alloy and combination thereof basically for these, wherein this first kind of metal with this basically the successive ceramic oxide fibers be fixed on the appropriate location, and wherein this metal is along this at least a portion extension of the length of successive ceramic oxide fibers basically, and this first kind of metal comprises outside surface; And also comprise:

Ag on the outside surface of Ni, Ni thickness be at least 8 microns (in certain embodiments, be preferably 10 microns, 12 microns or even 15 microns; More preferably 12～15 microns; In one aspect of the method, usually less than 20 microns).

Be surprisingly, the embodiment of the inventive method can be used to prepare the metal-matrix composite goods, and wherein molten metal is in molten state less than 75 seconds (in certain embodiments, preferably less than 60 seconds) in mould.Comparatively speaking, ordinary method requires molten metal to be in molten state 200 seconds or bigger in mould.Although without wishing to be held to theory, but can think when being higher than 200 ℃ to be that the existence of metal of positive Gibbs oxidation free energy can make the inset of metal-matrix composite goods and metal (in certain embodiments at least, preferably do not having oxide skin at the interface) combination, therefore need not form melts combine to attempt disruptive oxidation thing layer by fusion aluminum or aluminum alloy warming interface for a long time.

In this application:

" positive Gibbs oxidation free energy be higher than at least 200 ℃ " refer to temperature still keep during greater than 200 ℃ (473K) on the occasion of G ° of amount Δ _Rxn=Δ H ° _RxnS ° of-T Δ _Rxn, wherein Δ H ° _RxnBe the enthalpy (kJ/mol) of oxidizing reaction, T is temperature (degree Kelvin), Δ S ° _RxnIt is the entropy (kJ/mol ° of K) of oxidizing reaction;

" bonding strength peak value " refers to by the definite bonding strength peak value of " bonding strength peak value " described below test;

" do not contain aerobic " and refer in embodiment 3, observe with the 250X enlargement ratio, at the continuous oxide skin that does not have to estimate differentiation at the interface with opticmicroscope; And

" successive ceramic oxide fibers basically " refers to that length is at least the ceramic oxide fibers of 5cm.

First kind and second kind of metal-matrix composite goods of the present invention for example are used in the metal-matrix composite goods strongthener are provided.The advantage of one aspect of the invention is that the existing goods made by (original) metal (for example cast iron) can redesign with the fibre-reinforced another kind of metal of successive (for example aluminium) basically, make latter's (being the metal-matrix composite form of goods) have some needed performance (for example Young's modulus, yield strength and ductility), its performance equals to use the needed performance of being made by this original metal of original goods at least.Selectively, these goods can be redesigned and become to have the physical size identical with original goods.

The third metal matrix examples of articles of the present invention comprises caliper, high speed rotating ring and the loaded and high speed mechanical arm of using in the industrial equipments.

Brief Description Of Drawings

Fig. 1 is the stereographic map of illustrative metal groundmass composite material goods of the present invention.

Fig. 2 is the stereographic map of another kind of illustrative metal groundmass composite material goods of the present invention.

Fig. 3 A and Fig. 3 B are the stereographic maps of another kind of illustrative metal groundmass composite material goods of the present invention.

Fig. 4 A and Fig. 4 B are the stereographic maps of caliper of the present invention.

Fig. 4 C and Fig. 4 D are the sectional views of the caliper among Fig. 4 A and Fig. 4 B.

Fig. 5 is the stereographic map of another kind of illustrative metal groundmass composite material goods of the present invention.

Fig. 6 is the stereographic map of the metal-matrix composite goods made with metal-matrix composite goods shown in Figure 5.

Fig. 7 is the stereographic map that utilizes the another kind of illustrative metal groundmass composite material of the present invention goods of multilayer ceramic oxide fibre, wherein the longitudinal axis of each layer toward each other angle greater than 0 degree.

Fig. 8 is around another group of organizing that successive ceramic oxide fibers spiral basically twines stereographic map of successive ceramic oxide fibers basically.

Fig. 9 is the stereographic map of another kind of illustrative metal groundmass composite material goods of the present invention.

Figure 10 A and Figure 10 B are the orthographic plans of another kind of caliper of the present invention.

Figure 11 is the stereographic map of another kind of caliper of the present invention.

Figure 12 is the light micrograph of polished cross-sections of the inset of embodiment 1.

Figure 13 is the synoptic diagram of die cavity, and it is used for using embodiment 1 described inset to prepare the metal-matrix composite goods of embodiment 1.

Fig. 9 is the synoptic diagram of compression shear test set, and it is used for determine using the inset and the intermetallic bonding strength peak value of the metal-matrix composite goods of the present invention that inset of the present invention makes.

Figure 15 is the graphic representation of inset displacement under the load effect of embodiment 3 and embodiment 7.

Figure 16 is the light micrograph of polished cross-sections of the metal-matrix composite goods of embodiment 3.

Figure 17 is the light micrograph of polished cross-sections of the metal-matrix composite goods of Comparative Example H.

Figure 18 is the Photomicrograph of embodiment 1 described specimen.

Figure 19 is the stereographic map of exemplary inset holder.

Figure 19 A is the sectional view of Figure 19 part.

Describe in detail

The invention provides the metal-matrix composite goods, it comprises at least a metal and successive ceramic oxide fibers basically.Usually, metal-matrix composite goods of the present invention are designed to be suitable for application-specific, so that reach optimization or acceptable at least balance between needed performance, low cost and easy the manufacturing.

Usually, metal-matrix composite goods of the present invention such as inset are designed to be suitable for application-specific and/or some performance and/or feature.For example, the existing goods that selection is made by a kind of metal (for example cast iron) are used and are comprised that the another kind of metal of material enhanced (for example aluminium) of successive ceramic oxide fibers redesigns basically, make latter's (being the metal-matrix composite form of goods) have some needed performance (for example Young's modulus, yield strength and ductility), its performance equals to use by this first kind needed performance of metal original goods at least.Selectively, these goods can be redesigned and become to have the physical size identical with original goods.

The structure of comprehensive needed metal-matrix composite goods, needed performance, possible metal and the correlated performance of ceramic oxide material (preferably being suitable for making) and those materials, and be used to provide possible suitable structure.In certain embodiments, the preferred method that produces possible structure is to use finite element analysis (FEA), comprises utilizing conventional computer system (comprise and use central processing unit (CPU), input and output device) to use FEA software.Commercial the obtaining of FEA software that is fit to comprises by Ansys, Inc., Canonsburg, the FEA software that PA sells with trade(brand)name " ANSYS ".FEA helps accurately to simulate goods, and can determine to provide the successive ceramic oxide fibers, metal of desired properties level and the put area of possible other materials.Usually need move FEA repeatedly several times, to obtain preferred design.

With reference to Fig. 1, exemplary first kind of metal-matrix composite goods of the present invention (it also is exemplary second kind of metal-matrix composite goods of the present invention in certain embodiments) 10 comprise basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 12, aluminium or its alloy 14, outside surface 15, when being higher than at least 200 ℃ the metal 16 of positive Gibbs oxidation free energy, the outside surface 17 of selectable additional metal (for example Ni) 18 and selectable metal 18.Metal-matrix composite goods 10 are used to prepare metal-matrix composite goods of the present invention, and wherein the additional metal of goods and aluminium or its alloy 14 can be identical or different.

With reference to Fig. 2, exemplary first kind of metal-matrix composite goods of the present invention (it also is exemplary second kind of metal-matrix composite goods of the present invention in certain embodiments) 20 comprise basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 22, aluminium or its alloy 24, outside surface 25, when being higher than at least 200 ℃ the metal 26 of positive Gibbs oxidation free energy, the outside surface 27 of selectable additional metal (for example Ni) 28 and selectable metal 28.Metal-matrix composite goods 20 are used to prepare metal-matrix composite goods of the present invention, and wherein the additional metal of goods and aluminium or its alloy 24 can be identical or different.

In some exemplary of the present invention, the successive ceramic oxide fibers is vertically arranged basically, thereby they are parallel to each other usually.Although ceramic oxide fibers can be as single fiber in first kind of metal-matrix composite goods of the present invention (or being second kind of metal-matrix composite goods in certain embodiments), they are more typically in first kind of metal-matrix composite goods (or being second kind of metal-matrix composite goods in certain embodiments) form with bundle or bundle as one group of fiber.Bundle or intrafascicular fiber can remain on the relation (promptly normally parallel) of vertically arranging each other.When using many bundles or multi beam, fiber bundle or bundle also remain on the relation (promptly normally parallel) of vertically arranging each other.In certain embodiments, preferably all successive ceramic oxide fibers remain on basically vertically structure arranged, wherein the arrangement of single fiber remain on its average longitudinal axis ± 10 °, more preferably ± 5 °, most preferably be ± 3 ° within.

For some metal-matrix composite goods of the present invention, preferred or need ceramic oxide fibers bending, relative with straight ceramic oxide fibers (i.e. planar extension).Therefore, for example ceramic oxide fibers can be a planar in whole staple lengths, can be nonplanar (promptly crooked) in whole staple lengths, or they can be planar in some part, is nonplanar (i.e. bendings) in other parts.In certain embodiments, the successive ceramic oxide fibers remains on Uncrossed basically curvilinear structures (promptly vertically arranging) in the part of all metal-matrix composite goods bendings basically.In certain embodiments, the successive ceramic oxide fibers remains on equidistant each other basically relation in the curved part of whole metal-matrix composite goods basically.

For example Fig. 3 A and Fig. 3 B are another kind of first kind of illustrative metal groundmass composite material goods of the present invention (it also is exemplary second kind of metal-matrix composite goods of the present invention in certain embodiments) (insets) 30, wherein metal-matrix composite goods (inset) 30 comprise basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 32, aluminium or its alloy 34, outside surface 35, when being higher than at least 200 ℃ the metal 36 of positive Gibbs oxidation free energy, the outside surface 37 of selectable additional metal (for example Ni) 38 and selectable metal 38.Basically successive ceramic oxide fibers 32 is a planar reaching between section line DD and EE between section line BB and CC basically, is crooked between section line CC and DD.Selectively, the ceramic oxide fibers of vertically arranging of successive basically can be nonplanar in its whole length.

For example with reference to Fig. 5, another kind of first kind of illustrative metal groundmass composite material goods of the present invention (it also is exemplary second kind of metal-matrix composite goods of the present invention in certain embodiments) (inset) 50 comprises basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 52, aluminium or its alloy 54, outside surface 55, it when being higher than at least 200 ℃ the metal 56 of positive Gibbs oxidation free energy, the outside surface 57 of selectable additional metal (for example Ni) 58 and selectable metal 58, wherein successive ceramic oxide fibers 52 is crooked in its whole length basically.The example of the metal-matrix composite goods that can be made by latter's inset is metal-matrix composite rings as shown in Figure 6.Ring 60 comprises aluminium or its alloy 54 and ceramic oxide fibers 52 (seeing also Fig. 5).This ring for example is used for high speed rotating and produces the equipment of big centrifugal force.

In one aspect of the method, for some metal-matrix composite goods of the present invention, preferably maybe need to have two-layer, three layers, four layers or multiwalled successive ceramic oxide fibers (be one deck be one deck successive ceramic oxide fibers (in certain embodiments, preferably one deck fibrous bundle comprise successive ceramic oxide fibers basically) at least basically) at least basically.Each layer can be directed each other by any way.The example that each layer concerns each other shows in Fig. 7 and Fig. 8.With reference to Fig. 7, exemplary first kind of metal-matrix composite goods of the present invention (it also is exemplary second kind of metal-matrix composite goods of the present invention in certain embodiments) (inset) 70 comprises that the first layer and the second layer are basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 71 and 72, aluminium or its alloy 74, outside surface 75, when being higher than at least 200 ℃ the metal 76 of positive Gibbs oxidation free energy, the outside surface 77 of selectable additional metal (for example Ni) 78 and selectable metal 78.The first layer basically successive ceramic oxide fibers 71 with respect to the second layer basically successive ceramic oxide fibers 72 be 45 °, although depend on specific application, the potential difference of one deck and another layer can be for greater than 0 ° to 90 °.In certain embodiments, for some application preferably one deck be about 30 °～60 ° with respect to another layer, or even for example be about 40 °～50 °.Selectively, metal-matrix composite goods of the present invention can comprise two-layer or multilayer.

Be wound with successive ceramic oxide fibers basically as shown in Figure 8 and benefit one group of fiber, wherein metal-matrix composite goods (inset) 80 comprise around basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 81 spirals twine basically continuously (as shown in the figure, vertically arrange) ceramic oxide fibers 82, aluminium or its alloy 84, outside surface 85, when being higher than at least 200 ℃ the metal 86 of positive Gibbs oxidation free energy, the outside surface 87 of selectable additional metal (for example Ni) 88 and selectable metal 88.The example that is of value to the metal-matrix composite goods of performance by successive ceramic oxide fibers layer basically comprises the goods that are subjected to the power of bending in use around two Z-axises.

Usually, its length of successive ceramic oxide fibers is at least 10cm (often being at least 15cm, 20cm, 25cm or bigger) basically.In in certain embodiments of the invention, the successive ceramic oxide fibers is the form (being that fibrous bundle comprises successive ceramic oxide fibers basically) of fibrous bundle basically.Usually, its length of successive ceramic oxide fibers bundle is at least 10cm (often being at least 15cm, 20cm, 25cm or bigger) basically.

Ceramic oxide fibers can comprise ceramic oxide fibers that successive is basically vertically arranged or even form by it basically, wherein " vertically arrange " and refer to the arrangement that fiber is normally parallel with respect to staple length.

In certain embodiments, strengthen ceramic oxide fibers basically continuously and be used to prepare metal-matrix composite goods of the present invention, preferably its mean diameter is at least about 5 microns.In certain embodiments, fiber diameter is not more than about 200 microns, more preferably no more than about 100 microns.For fibrous bundle, in certain embodiments, fiber diameter preferably is not more than about 50 microns, more preferably no more than about 25 microns.

In certain embodiments, its Young's modulus of successive ceramic oxide fibers more preferably is at least 100GPa greater than about 70GPa basically, is at least 150GPa, is at least 200GPa, is at least 250GPa, is at least 300Gpa, or even is at least 350GPa.

In certain embodiments, can use fiber although depend on specific application than the harmonic(-)mean tensile strength, but its average tensile strength of successive ceramic oxide fibers preferably is at least about 1.4GPa basically, more preferably be at least about 1.7GPa, even more preferably be at least about 2.1Gpa, most preferably be at least about 2.8GPa.

The successive ceramic oxide fibers commercial can single fiber or in groups fiber (for example strand or bundle) obtain.Strand or bundle can comprise and for example be at least 420 single fiber/bundles, be at least 760 single fiber/bundles, be at least 2600 single fiber/bundles, or bigger.Bundle is known in fiber art, refer to untiing many (single) fibers (be at least 1 00 fibers usually, more generally be at least 400 fibers) that form is collected, and stock index is twined or rope-like constructed to a certain degree.Can obtain the ceramic oxide fibers that comprises the ceramic oxide fibers bundle that all lengths is crossed.The transversal section form of fiber can be circular or oval.

Useful ceramic oxide fibers example comprises the αYang Hualv fiber, aluminosilicate fibre and aluminoborosilicate fiber.After reading specification sheets, other useful ceramic oxide fibers are clearly for those skilled in the art.

The method of making sapphire whisker is known in the art, comprises United States Patent (USP) 4,954, the method described in 462 people such as () Wood.In certain embodiments, preferred sapphire whisker is the alpha alumina-based fiber of polycrystalline, comprises by theoretical oxide compound accounting for the Al of sapphire whisker gross weight greater than about 99wt.% ₂O ₃SiO with about 0.2-0.5wt.% ₂In one aspect of the method, in certain embodiments, preferred polycrystalline, alpha alumina-based fiber comprises the αYang Hualv of mean particle size less than 1 micron (being more preferably less than 0.5 micron).In one aspect of the method, in certain embodiments, preferred its average tensile strength of the alpha alumina-based fiber of polycrystalline is at least 1.6GPa (preferably be at least 2.1GPa, more preferably be at least 2.8GPa).The αYang Hualv fiber is commercial for example can be from 3M Company of St.Paul, and MN obtains with trade(brand)name " NEXTEL 610 ".Another kind of αYang Hualv fiber comprises the Al of about 89wt.% by total weight of fibers ₂O ₃, 10wt.% ZrO ₂With about 1wt.% Y ₂O ₃, commercial can obtaining with trade(brand)name " NEXTEL 650 " from 3M Company.

The method for preparing aluminosilicate fibre is known in the art, comprises United States Patent (USP) 4,047, the method described in 965 (people such as Karst).In certain embodiments, preferred aluminosilicate fibre comprises the Al that accounts for the about 67～85wt.% of aluminosilicate fibre gross weight by theoretical oxide compound ₂O ₃SiO with about 33～15wt.% ₂In certain embodiments, preferred aluminosilicate fibre comprises the Al that accounts for the about 67～77wt.% of aluminosilicate fibre gross weight by theoretical oxide compound ₂O ₃SiO with about 33～23wt.% ₂In certain embodiments, preferred aluminosilicate fibre comprises the Al that accounts for the about 85wt.% of aluminosilicate fibre gross weight by theoretical oxide compound ₂O ₃SiO with about 15wt.% ₂In certain embodiments, preferred aluminosilicate fibre comprises the Al that accounts for the about 73wt.% of aluminosilicate fibre gross weight by theoretical oxide compound ₂O ₃SiO with about 27wt.% ₂Aluminosilicate fibre is commercial for example can be obtained with trade(brand)name " NEXTEL 440 ", " NEXTEL 720 " and " NEXTEL 550 " from 3M Company.

The method for preparing the aluminoborosilicate fiber is known in the art, comprises United States Patent (USP) 3,795, the method described in 524 (Sowman).In certain embodiments, preferred aluminoborosilicate fiber comprises by theoretical oxide compound and accounts for the aluminoborosilicate total weight of fibers: about 35wt.%～75wt.% (Al of even for example about 55wt.%～75wt.%) ₂O ₃Greater than 0wt.% (even for example being at least about 15wt.%) and less than the SiO of about 50wt.% (or for example less than about 45% or even less than about 44%) ₂Greater than about 5wt.% (or for example less than about 25wt.%, less than about 1wt.%～5wt.% or even less than the B of about 2wt.%～20wt.%) ₂O ₃The aluminoborosilicate fiber is commercial for example can be obtained with trade(brand)name " NEXTEL 312 " from 3M Company.

The commercial available ceramic oxide fibers of successive basically often is included in the organic sizing material that is added in its manufacturing in the fiber, oilness to be provided in processing and to protect fiber rope.Can think that sizing material for example is easy to reduce the breakage of fiber in changing into the fabric process, reduce static, reduce amount of dust.For example can or make its burning remove sizing material by dissolving.

Coating also within the scope of the present invention on ceramic oxide fibers.Coating for example can be used for the wetting properties of fortifying fibre, reduces or prevents reaction between fiber and the molten metal sill.This coating is known with the technology of this coating is provided in fiber and metal-matrix composite field.

For the third metal-matrix composite goods of the present invention, the aluminum or aluminum alloy of the aluminum or aluminum alloy of inset and the third metal-matrix composite goods is normally different, but also can be identical.Comprise that the aluminium of metal-matrix composite goods of the present invention (comprising inset) and aluminium alloy can contain impurity although be used for making, preferably to use purer relatively metal (being that metal comprises less than 0.1wt.% or even less than the impurity of 0.05wt.% (be among Fe, Si and/or the Mg each less than 0.25wt.%, 0.1wt.% or even less than 0.05wt.%)) in certain embodiments.Although the higher degree metal is preferred for the material of making than high-tensile, also can use the lower metal of purity.

The aluminium and the aluminium alloy that are fit to obtain commercial.For example aluminium can be from Pittsburgh, and the Alcoa of PA is with trade(brand)name " SUPER PURE ALUMINUM; 99.99% Al " obtains.Aluminium alloy (for example the Cu of Al-2wt.% (0.03wt.% impurity) can be from Belmont Metals, NewYork, and NY obtains.In certain embodiments, preferred aluminium alloy example comprises and contains the alloy of the Al of 98wt.% at least, contain at least the aluminium alloy of the Cu of 1.5wt.% and (for example press the total restatement of alloy, the weight percent of Cu is 1.5～2.5, be preferably 1.8～2.2 aluminium alloy), 200 (A201.1 aluminium alloys for example, 201.2 aluminium alloy, A206.0 aluminium alloy and 224.2 aluminium alloys), 300 (A319.1 aluminium alloys for example, 354.1 aluminium alloy, 355.2 aluminium alloy and A356.1 aluminium alloy), and/or 400 (for example 443.2 aluminium alloys and 444.2 aluminium alloys), 700 (for example 713 aluminium alloys), 6000 (for example 6061 aluminium alloys) series alloys.

Although its thickness of metal that is positive Gibbs oxidation free energy when being higher than at least 200 ℃ also is available outside preset value, if but thickness is low excessively, when inset is preheated so, the coating diffusion, thereby can not prevent that the interface is oxidized or help to reduce at the interface oxidation, and excessive thickness is easy to influence required cohesive strength between the metal of the metal of inset and metal-matrix composite goods.Being used to be deposited on when being higher than at least 200 ℃ is that the method for the metal of positive Gibbs oxidation free energy is known in the art, comprises plating.

Usually, the thickness of selectable Ni is greater than about 1 micron, more generally greater than 2 microns, or even greater than 3 microns.In one aspect of the method, the thickness of common this metal is less than about 10 microns, more generally less than about 5 microns.Although thickness also is available outside these values, if but thickness is low excessively, can not to help when being higher than at least 200 ℃ be that the metal and the inset of positive Gibbs oxidation free energy is bonding to coating so, and excessive thickness is easy to influence required cohesive strength between the metal of the metal of inset and metal-matrix composite.In certain embodiments, by electroless deposition deposition Ni.

First kind or second kind of metal-matrix composite goods (inset) of the present invention for example can by will many successive ceramic oxide fibers (in certain embodiments, preferably fiber (for example strand or bundle)) in groups be wrapped in and be used for the metal inset and design and have on the axle of needed size and dimension and make.In certain embodiments, the fiber that preferably is wound is handled through sizing material.Exemplary sizing material comprises water (in certain embodiments, preferred deionized water), wax (for example paraffin), polyvinyl alcohol (PVA).If sizing material is a water, fiber is wrapped on the axle usually so.After winding is finished, take off axle, place water cooler then, freeze up to the fiber that twines from wrapping machine.Can cut the winding fiber that freezes as required.For example wind the axle of forming by four adjacent panels and twine, can take off rectangular plate so, thereby the fibre preforms that freezes is provided as fruit fiber.Preform can be cut into pieces, so that less preform to be provided.Usually remove sizing material before at formation metal-matrix composite goods (inset).Can be by for example the fiber that forms being placed mould (in certain embodiments, preferably graphite), heating mould is removed sizing material then.Mould is used to make metal-matrix composite goods (for example inset).

For forming metal-matrix composite goods (for example inset), if sizing material is arranged, after removing sizing material, mould is placed jar so, normally stainless cylinder of steel preferably only has an end opening.In certain embodiments, jar inside preferably with boron nitride or similar coated materials, with in casting cycle subsequently, minimize aluminium/aluminium alloy and jar between reaction, and/or accelerate the metal-matrix composite goods and discharge from mould.Jar and mould place in the pressurized vessel of pressure pouring machine.Subsequently, aluminium and/or aluminium alloy (for example multi-disc aluminium and/or the aluminium alloy that scales off from ingot casting) place the top of jar.Evacuation pressure container then, and be heated to above the fusing point (usually above about 80 ℃～120 ℃ of liquidus temperature) of aluminium/aluminium alloy.In case reach needed temperature, just turn off well heater, use argon gas (or similar rare gas element) that pressurized vessel is pressurized to pressure then usually and be about 8.5～9.5MPa, thereby make molten aluminum/aluminium alloy infiltrate preform.Along with temperature descends, the pressure in the pressurized vessel also slowly descends.When goods solidify (its temperature drops to and is lower than about 500 ℃), by gas, from mould, take out the metal-matrix composite goods (for example inset) of casting, further cooling in air then.

Also can make metal-matrix composite goods (for example inset) by the other technologies that for example are known in the art, comprise casting-forging method.For casting-forging method, for example the ceramic oxide fibers of Xing Chenging can place mould (for example punching block), burns the sizing material of any existence, and molten aluminum/aluminium alloy is added in the die cavity, exerts pressure, and solidifies up to casted article and finishes.After the cooling, from mould, take out the metal-matrix composite goods (for example inset) that make.

The inset of making can further be handled (for example sandblast and/or surface grinding (for example using the Z-axis diamond lapping machine), for example elimination or the lip-deep oxidation of reduction inset.But also cutting insert as required is to provide needed shape (comprise with sprinkler and cutting).Next, preferably being used in when being higher than at least 200 ℃ is the washing metal-matrix composite goods (for example inset) of positive Gibbs oxidation free energy.Selectively, be coated in be the metal of positive Gibbs oxidation free energy when being higher than at least 200 ℃ before, metal such as Ni are coated on the metal-matrix composite goods (for example inset).Use Ni to help the bonding of metal such as Ag and inset.

Select the method steps of the specific ceramic oxide fibers of successive basically, substrate material, holder etc. and preparation metal-matrix composite goods, so that the goods of the metal-matrix composite with needed performance to be provided.For example be the needed goods of preparation, select to reach each other and abundant compatible ceramic oxide fibers of successive basically and the metal_based material of article fabrication methods.In certain embodiments; the preferred metal of selecting to comprise metal-matrix composite of the present invention zone; make metal matrix not have tangible chemical reaction (being relative chemically inert promptly), thereby for example need not provide protective coating in the fiber outside with respect to melting material with successive ceramic oxide fibers basically.

Can use inset of the present invention to prepare the third metal-matrix composite goods of the present invention (for example casting-forging method and permanent instrument gravity casting) according to method as known in the art.Can use finite element analysis (FEA) model, for example determine the optimum position and the amount of ceramic oxide fibers, to satisfy needed specification.This analysis also can be used to size, quantity and the position of for example selecting inset used.Usually, preheating inset and/or mould before casting.Although without wishing to be held to theory, can think that the preheating inset helps to form metal bonding between the aluminium of inset and the third metal-matrix composite goods and/or aluminium alloy.In certain embodiments, preferably inset is preheating to 500 ℃-600 ℃.In certain embodiments, preferably mould is preheating to 200 ℃-500 ℃.Although casting is carried out in air usually, (for example argon gas) casts also within the scope of the present invention in other atmosphere.

Also can use FEA, with casting process, casting condition and/or the die design of for example be used to select to cast inset of the present invention and/or metal-matrix composite goods.The FEA software that is fit to can obtain in commerce, comprises by UES Annapolis, the software that MD sells with trade(brand)name " PROCAST ".

As mentioned above, should be used for designing metal-matrix composite goods (comprising inset) according to some usually, thereby it need have some performance, have some structure and made etc. by some material.Usually, select mould or mfg. moulding die, so that the metal-matrix composite goods of required shape to be provided, thus the net form of providing or near the net form goods.Net form or for example can minimize or cancel the metal-matrix composite goods of casting needs with post-treatment or other casting aftertreatments near the net form goods.Usually, mfg. moulding die or be used for making inset to be in needed position makes that the successive ceramic oxide fibers is in the appropriate location in the metal-matrix composite goods that make basically.Method and material that preparation is fit to cavity are known to those skilled in the art.The material that is used to prepare particular mold depends on the metal that for example is used to prepare the metal-matrix composite goods.Usually used moulding stock comprises graphite or steel.

Selectively, the inset holder is used for fixing inset of the present invention.This inset holder helps to place inset in mould, thereby helps to place inset in the metal-matrix composite goods that make.An exemplary, this inset holder comprises that at least one is used for fixing the part of at least one inset, wherein this inset holder comprises the first kind of metal that is selected from aluminium, its alloy (for example 200,300,400,700 and/or 6000 series (preferred 6000 series in certain embodiments) aluminium alloy) and combination thereof.In certain embodiments, this inset holder comprises outside surface and is second kind of metal on the outside surface of first kind of metal of positive Gibbs oxidation free energy when being higher than at least 200 ℃, wherein this second kind of its thickness of metal be at least 8 microns (in certain embodiments, be preferably 10 microns, 12 microns or even 15 microns; More preferably 12～15 microns; In one aspect of the method, usually less than 20 microns).

The exemplary holder that wherein has inset is shown in Figure 19 and Figure 19 A.With reference to Figure 19, goods 10 comprise holder 191 and are used for fixing

part

192A, 192B, 192C and the 192D of inset 193A of the present invention, 193B and 193C.With reference to Figure 19 A, holder 191 comprises aluminium and/or its alloy 194, outside surface 195, is the outside surface 198 of the selectable metal 197 of positive Gibbs oxidation free energy, selectable additional metal (for example Ni) 196 and selectable metal 196 when being higher than at least 200 ℃.

For the additional detail of exemplary inset holder, see also the common pending application U.S.60/404 that submitted on August 20th, 2002,729.

In addition, surprisingly, the embodiment of first kind or second kind of metal-matrix composite goods (inset) of the present invention can be used for preparing the metal-matrix composite goods, wherein the molten metal in the mould in molten state less than 75 seconds (in certain embodiments, preferably less than 60 seconds).Although keeping molten metal in mould also is available in the molten state long period, the preferred short period (promptly less than 75 seconds),, can think that the long period can make the inset distortion although without wishing to be held to theory.In certain embodiments, preferably the unobvious distortion of inset (is that inset has first kind of outside dimension structure (being size and dimension) before casting in casting the third metal-matrix composite goods process of the present invention, have second kind of outside dimension shape after the casting, wherein first kind identical with second kind of outside dimension structure, and wherein be understandable that when being higher than 200 ℃ to be that the metal of positive Gibbs oxidation free energy and selectable metal such as Ni are easy to diffuse in the metal of casting metals (and in metal of possible inset) at least).

For the metal-matrix composite goods that the metal founding oxidation at the interface around inset and inset is higher than desired level, can use further treatment articles of hot isostatic pressing (HIPing), to reduce or to avoid unwanted oxidation.HIPing also can be used for reducing the porousness in the metal-matrix composite goods.The HIPing technology is known in the art.The example that can be used for HIPing temperature, pressure and the time of embodiment of the present invention comprises 500 ℃～600 ℃ respectively, 25Mpa～50Mpa, 4～6 hours.Also can use temperature, pressure and time outside these scopes.Lesser temps is easy to the compactibility that for example provides less and/or improves the HIPing time, and comparatively high temps makes the metal-matrix composite product deformation.The compactibility that lower pressure is easy to for example to provide less and/or improve the HIPing time, and elevated pressures may be unwanted, or in some cases even can damage the metal matrix goods.Short period is easy to the compactibility that for example provides less, and the long period may be unwanted.

For the exemplary inset of preparation metal-matrix composite goods and other details of method, see also the common pending application U.S.60/404 that submitted on August 20th, 2002,704.

After reading specification sheets, the additive method of preparation metal-matrix composite goods is clearly to those skilled in the art.

Metal-matrix composite goods of the present invention can comprise the ceramic oxide fibers of successive basically more than a group (for example two groups, three groups etc.), wherein one group basically successive ceramic oxide fibers and another group with therebetween basically the successive ceramic oxide fibers metal that is fixed on the appropriate location separate.For example with reference to Fig. 9, first kind of metal-matrix composite goods of the present invention (it also is exemplary second kind of metal-matrix composite goods of the present invention in certain embodiments) (inset) 90 comprises that successive (as shown in the figure basically, vertically arrange) the group 93A of ceramic oxide fibers 92,93B and 93C, aluminium or its alloy 94, outside surface 95, when being higher than at least 200 ℃ the metal 96 of positive Gibbs oxidation free energy, the outside surface 97 of selectable additional metal (for example Ni) 98 and selectable metal 98.

Be at least 100MPa (in certain embodiments according to following, preferably be at least 125MPa, be at least 150MPa, be at least 175 or even be at least 180MPa) " test of bonding strength peak value ", the embodiment of some metal-matrix composite goods of the present invention has " bonding strength peak value " between the inset that uses or holder (depending on that promptly test is any) and inset aluminum or aluminum alloy foundry goods on every side.The synoptic diagram of compression shear test set as shown in Figure 9, wherein compression shear test set 140 comprises the compressive load element 147 of release instrument 141, specimen 142, back-up block 143 and 100,000 newton (22,482 pounds).Its cross section of metal-matrix composite to be tested is perpendicular to the longitudinal axis of employed inset or holder; The tranverse sectional thickness of inset is 1.16cm (0.46 inch), and the tranverse sectional thickness of holder is 0.4cm, and diameter is 2.5cm (1 inch).

Release instrument 141 comprises the respective cross section of the used inset of contact or holder 144 and specimen 142, but the cross-sectional area of release instrument 141 little by 10% (it is identical with the shape of cross section of used inset or holder 144 promptly to release instrument 141, and the cross-sectional dimension of release instrument 144 is littler).Release instrument 141 is clipped in the upper gripper jaw 145 of oild chuck, and hydraulic pressure is 10.34MPa (1500 pounds/square inch).Back-up block 143 diameters are 2.54cm (1.0 inches), the dark 0.15cm of counterbore (0.06 inch).1.1cm the through hole of (0.435 inch) diameter is located at the top of opening jaw 145 of oild chuck 146 bottoms.

Sample 142 to be tested is placed on the back-up block 143, and is enclosed within counterbore, used inset or holder, through hole center.The bottom 148 of rising oild chuck 146 is 0.025cm (0.01 inch) up to the space of releasing between instrument 141 and used inset or holder on top to be promoted (being sample 144 to be tested).Utilize the gentle sliding support rotatably of the most advanced and sophisticated manual water of the coupling piece 143 of release instrument 141 then, be positioned at used inset or the holder that exposes in the specimen with range estimation, up to the cross section coupling of two elements.

Then by release towards fixed instrument 141 with 0.05cm (0.020 inch)/minute the speed lower oild chuck that moves up test monitoring load and deflection simultaneously.Thereby used inset or holder are released tool surfaces with fixed and are contacted, and contact force therebetween are recorded as the function of displacement.Stop test after arriving peak force immediately, total deflection is about 0.05cm (0.020 inch).

After test is finished,,, make that its cross section is overlapping to verify the most advanced and sophisticated complete matching of used test inset or holder and release with the enlargement ratio test sample of opticmicroscope with 100X.

Use following formula to calculate average shear stress:

Average shear stress=(load during first slippage, N lbs.)/(contact area between inset and aluminium alloy, m ²(in ²)).

Load is drawn into the function of inset displacement.The load of releasing the discontinuous place of curve be the bonding strength peak value (promptly inset or holder and used inset or holder aluminum or aluminum alloy foundry goods on every side at the interface be original slippage).

Use finite element analysis (FEA) calculations incorporated intensity peak.Finite element analysis (FEA) software (from Ansys Inc., Canonsburg, PA obtains with trade(brand)name " ANSYS ") and be used to simulate used inset or holder, show that bonding strength peak value and the average shear stress axis that records are about 3.0.

FEA is calculated as follows.Create the finite element geometric model of specimen.Used inset or holder and the cube component that is of a size of 0.02cm * 0.02cm * 0.05cm (0.01 inch * 0.01 inch * 0.02 inch) are formed net, and except the top of used inset or holder, sizing grid is 0.02cm on all directions.Aluminium/aluminum alloy casting around used inset or the holder and cubes are formed net, and this cubes is 0.05cm (0.02 inch) near the side of used inset or holder in the mimic specimen, and its elsewhere is 0.10cm (0.04 inch).The FEA computed in software is along the shear-stress at used inset or each point place, holder surface, and applied pressure is 533.3MPa (is 2900 pounds corresponding to releasing test load).The shear-stress mean value that calculating is determined to pass the shear-stress peak value of used inset or holder surface each point and passed used inset surface or holder surface.The ratio of bonding strength peak value and average shear stress is about 3: 1.

Metal-matrix composite goods of the present invention (comprising first kind and second kind of metal-matrix composite goods) can be different shapes, comprise shaft-like (comprising the shaft-like of circle, rectangle or square cross section), I-strip, L-shape or tubulose.Metal-matrix composite goods of the present invention (comprising first kind and second kind of metal-matrix composite goods) can elongate, and have the cross-sectional area of substantially constant.

The preferable use of some embodiment of first kind and/or second kind metal-matrix composite goods of the present invention is as reinforce in aluminium or its alloy substrate composite product.This metal-matrix composite examples of articles shows at Fig. 4 A, Fig. 4 B, Fig. 4 C and Fig. 4 D.The caliper 40 of Motor vehicles (for example car, sport vehicle, lorry or truck) usefulness comprises aluminium or its alloy 42 and metal-matrix composite goods of the present invention (inset) 30 (seeing also Fig. 3), these goods are mixed with basically continuously (vertically arranging as shown in the figure) ceramic oxide fibers 48.Fig. 4 C and Fig. 4 D are respectively the sectional views of Fig. 4 B FF along the line and GG.In Fig. 4 C and Fig. 4 D, caliper 40 comprises aluminium or its alloy 42 and metal-matrix composite goods of the present invention (inset) 30.

Have first kind of the present invention and/or metal-matrix composite goods caliper another kind of exemplary configurations and use the Motor vehicles (for example car, sport vehicle, lorry or truck) of this caliper to show at Figure 10 A and Figure 10 B with breaking system.The example of the disc brake of motor vehicle comprises rotor; Place the opposite side of rotor and removable and be mated arresting inside brake sheet and outer brake(-holder) block; Be used to make the piston of inside brake sheet near rotor; And caliper, it is included in has the cylindrical body element that is used to hold this piston on rotor one side, be positioned at the rotor opposite side and be used to support the arm linear element of outer brake(-holder) block, reaches the bridge that extends through this rotor plane between this body element and this arm linear element.

With reference to Figure 10 A and Figure 10 B, disc brake component 100 comprises caliper shell 101, and its bridge 106 by body element 102, arm linear element 104 and connection body element 102 1 ends and arm linear element 104 the other ends is formed.Body element 102 is comprising being generally columniform recess 103, and it receives piston 105 slidably, with compression inside brake sheet 107.The internal surface 195 of arm linear element 104 supports the outer brake(-holder) block 109 relative with inside brake sheet 107.Brake rotors 196 links to each other with the wheel of automobile (figure does not show), and lays respectively between inside brake sheet 107 and the outer brake(-holder) block 109.Inset 200 comprises aluminium or its alloy 204.Interface 209 wherein is that the mean vol of metal (selectively additional metal (for example Ni)) in interface 209 of positive Gibbs oxidation free energy is higher than in aluminium or its alloy 208 when being higher than at least 200 ℃ between inset 200 and aluminium or its alloy 208.

Hydraulic efficiency piston 105 or impose other power and make inside brake sheet 107 a side near rotors 196, and reactive force makes caliper shell 101 floating, thus outer brake(-holder) block 109 is cooperated with the opposite side of rotor 196, this is known in the art.

The another kind of exemplary caliper of the present invention shows that in Figure 11 wherein caliper 110 comprises aluminium and/or its alloy 111 and inset 10.

Use the disc brake example of metal-matrix composite caliper of the present invention to comprise first kind of metal-matrix composite goods of the present invention, comprise fixing, unsteady and sliding-type.Additional detail about caliper and breaking system for example is disclosed in United States Patent (USP) 4,705, among 093 (Ogino) and 5,234,080 (Pantale).

Other examples of metal-matrix composite goods of the present invention can be made by first kind and/or second kind of metal-matrix composite goods of the present invention, and it comprises that automatic element (for example control arm and automatic piston pin) automatically and rifle are with element (gun barrel of using as the rifle steel lining).

In certain embodiments, metal-matrix composite goods of the present invention (are first kind and/or second kind of metal-matrix composite goods of the present invention, and by first kind and/or second kind of the third metal-matrix composite goods of the present invention that the metal-matrix composite goods are made of the present invention) in comprising the zone of successive ceramic oxide fibers basically, comprise (in certain embodiments by regional cumulative volume about 70～30%, preferred about 60～35% or even about 45～35%) ceramic oxide fibers of successive basically of the metal of volume and about 30～70% (in certain embodiments, preferred about 40～65% or even about 55～65%) volume.In certain embodiments, preferred metal-matrix composite goods of the present invention (be first kind and/or second kind of metal-matrix composite goods of the present invention, and by first kind and/or second kind of the third metal-matrix composite goods of the present invention that the metal-matrix composite goods are made of the present invention) comprise the ceramic oxide fibers of successive basically by about 50% volume of regional cumulative volume in comprising the zone of successive ceramic oxide fibers basically.

In certain embodiments, inset comprises successive ceramic oxide fibers basically, comprise (in certain embodiments by inset cumulative volume about 30～70%, preferred about 35～60% or even about 35～45%) ceramic oxide fibers of successive basically of the metal of volume and about 70～30% (in certain embodiments, preferred about 65～40% or even about 65～55%) volume.In certain embodiments, preferred inset comprises the ceramic oxide fibers of successive basically that is at least 50% volume by the inset cumulative volume.

The present invention can further be illustrated by the following examples, but described in an embodiment certain material, its amount and other conditions and details should not be interpreted as limiting inadequately the present invention.Various modifications and variations of the present invention are obvious for those skilled in the art.Unless refer else, all umbers and per-cent are by weight.

Embodiment

Embodiment 1

Being prepared as follows of two aluminium matrix composite insets of the present invention.Use the deionized water sizing material twine continuous αYang Hualv fibrous bundle (from 3M Company, St.Paul, MN obtains with trade(brand)name " NEXTEL 610 "; 3,000denier; Young's modulus is about 370GPa; Average tensile strength is about 3GPa; Mean diameter is 11 microns), impregnation of fibers bundle in water-bath immediately before on 20.3cm (8-inch) square mandrel shaft that is wound into the four sides wherein is 65% fibre preforms with the filling of preparation fiber volume.Apply tension force (about 75 grams, with tensiometer (from Tensitron, Boulder CO obtains with trade(brand)name " CERTEN ") measure) twine fiber, thus four pre-templates of orthogonal (10.2cm (4 inches) * 20.3cm (8 inches) * 0.29cm (0.115 inch) is thick) formed.(40F) water cooler freezes water-cooled, and the stable preform that makes then axle to be placed-40 ℃.When freezing, pre-template is cut into the preform of 7.6cm * 15.2cm (3 inches * 6 inches).

Use graphite jig assembly (from Schunk Graphite Technology, Inc., Menomonie Falls, WI obtains) cast aluminum groundmass composite material plate.The width of graphite jig is 9.64cm, and length is 15.24cm, highly is 4.90cm.Mould comprises four inset slits, and the between centers of slit is 0.89cm.Apply the graphite jig assembly with the aqueous dispersion of graphite granule (from AchesonColloids Company, Port Huron, MI obtains with trade(brand)name " AQUADAG ").Four 7.6cm that freezes * 15.2cm preforms are placed the graphite jig assembly, preform in each cavity of four cavitys.The die assembly that preform will wherein be housed then places about 16 hours of the baking oven of 120 ℃ (250), and the water in preform evaporates.

Then die assembly is placed stainless cylinder of steel (length 102mm, width 53mm, height 500mm), the one end opening, inside boron nitride suspension (from ZYP Coatings Inc., Oak Ridge, TN obtains with trade(brand)name " RS 1000 ") apply.Although without wishing to be held to theory, can think that boron nitride coating can be suppressed at the reaction between stainless steel and molten aluminum in the casting cycle of back.

After the coating drying, then 2500 gram aluminium-2% copper alloy ingots (are cut into two, every 5.1cm * 2.5cm * 30.5cm (1 inch * 2 inches * 12 inches)) (from Belmont Metal, NewYork, NY obtains with trade(brand)name " 1980-A ") places the stainless cylinder of steel on assembly top.K type thermopair (from Omega Engineering Inc., Stamford, CT obtains) is placed die assembly top, with the temperature of aluminium-2% copper melt in the monitoring casting cycle.Fixed link is fixed on graphite components top, to prevent that assembly floats in casting cycle in molten aluminum.Then stainless cylinder of steel is placed the pressurized vessel inside of pressure pouring machine (from Process Engineering Technologies, Plaistow, NH obtains), and close pressurized vessel.The size of pressure pouring container is about 16.9cm (internal diameter) * 88.9cm (length).

The pouring container of finding time to close then with vacuum pump, up to pressure less than 1torr.Open the furnace power of pressure pouring machine then, it is 710 ℃ (being higher than about 100 ℃ of alloy melting point) that the Cu alloy pig of graphite jig assembly and Al-2% is heated to temperature.Average heating rate is about 340 ℃/hour.After 710 ℃ of the arrival melt temperatures, close furnace power, the closing containers vacuum valve, thus container and vacuum pump are separated.

Open the low pressure valve that is connected with the bottled argon gas groove that pressurizes then, thus with argon gas backfill container, to initial low pressure power be 1.79MPa (260psi).When arriving this pressure, close the low pressure valve, open high pressure argon gas valve, be 8.96MPa (1300psi) up to pressure.With pressure remain on 8.96MPa ± 1% (1300psi ± 15psi) reach 15-20 minute, thus molten aluminum-2% copper alloy is infiltrated in the preform fully.

Next, reduce pressure, temperature is reduced to 500 ℃.When temperature is lower than 500 ℃, open the container vent valve, argon gas is led in the atmosphere.Open container then, take out stainless cylinder of steel.Die assembly and jar are separated, from graphite jig, take out four cast aluminium groundmass composite material plates.

With Z-axis diamond lapping machine (#11 Blanchard shredder, from PrecisionInstruments, Minneapolis, MN obtains) cast panel being carried out surface grinding to thickness is 0.25cm (0.1 inch).Longitudinally cutting cast panel to width then is 0.94cm (0.37 inch), thereby obtains the cast panel of 15.2cm (6 inches) * 0.95cm (0.375 inch) * 0.25cm (0.1 inch).

Surface treatment/the coating of right latter two cast panel is as follows.Two cast panels with the grinding miller of 100 granularities (from Norton Company, Worcester, MA is with trade(brand)name, and " DIAMDONDWHEEL; ASD100 " obtains) grind, and clean with standard paint thinner (from HCI, St.Paul, MN obtains with Grade 401), embrocate with towel paper, up to there not being appreciable residue to be removed from the surface.

Two cast panels that make are applied about 3 microns nickel through electroless deposition, and (by Co-Operative Plating Co., St.Paul MN), electroplates about 12 microns silver then.

The light micrograph of the polished cross-sections of the inset of embodiment 1 when the 550x enlargement ratio shows in Figure 12.Inset 120 comprises aluminium-2% bronze medal matrix 124, aluminum oxide (" NEXTEL 610 "; About 11 microns of diameter) fiber 122, nickel coating 128 and silver coating 126.

The inset of each band coating preheating 15 minutes to temperature in air is about 750 ℃.Then the inset of heating is put into the punching block chamber.With reference to Figure 13, mould 130 comprises pedestal 132 (9.8cm * 9.8cm * 14cm (3.9 inches * 3.9 inches * 5.5 inches)), it has the rectangular slot 134 (1.3cm * 0.25cm (0.5 inch * 0.1 inch)) that inset is used, and upper element 136 (7.3cm * 7.3cm * 12.7cm (29 inches * 2.9 inches * 5.0 inches)).Upper element 136 comprises cavity 138, and its diameter is 2.54cm (1 inch), and the degree of depth is 10.2cm (4 inches).Apply upper element 136 with boron nitride separant (from The Carborundum Corp., Amherst, NY obtains with trade(brand)name " COMBAT BORON NITRIDE AEROSOL SPRAY CC-18 "), be preheated to about 300 ℃ then.In 4 seconds, the molten aluminium alloy (from Alcan Inc., Montreal, Quebec obtains with trade(brand)name " A356 ") that temperature is about 735 ℃ is poured in the punching block chamber along inset, is cured.When temperature is cooled to about 500 ℃, from die cavity, take out inset and casting component.

Two aluminium matrix composites that make among embodiment 1a and the embodiment 1b are divided into the specimen of 1.16cm (0.46 inch) * 2.5cm (1 inch) diameter.Each several part is along the direction cutting perpendicular to the inset longitudinal axis.

Carry out the compression shear test, to measure " bonding strength " between inset and inset aluminium casting on every side.The synoptic diagram of compression shear test set as shown in figure 14, wherein compression shear test set 140 comprises the compressive load element 147 of release instrument 141, specimen 142, back-up block 143 and 100,000 newton (22,482 pounds).

Release instrument 141 comprises the cross section 2.36mm * 9.37mm (0.0930 inch * 0.3690 inch) of contact inset 144 and specimen 142.Release instrument 141 is clipped in the upper gripper jaw 145 of oild chuck, and hydraulic pressure is 10.34MPa (1500 pounds/square inch).Back-up block 143 diameters are 2.54cm (1.0 inches), the dark 0.15cm of counterbore (0.06 inch).1.1cm the through hole of (0.435 inch) diameter is located at the top of opening jaw 145 of oild chuck 146 bottoms.

Sample 142 to be tested is placed on the back-up block 143, and is enclosed within counterbore, inset, through hole center.The bottom 148 of rising oild chuck 146 is 0.025cm (0.01 inch) up to the space of releasing between instrument 141 and inset on top to be promoted (being sample 144 to be tested).Utilize the gentle sliding support rotatably of the most advanced and sophisticated manual water of the coupling piece 143 of release instrument 141 then, be positioned at the inset that exposes in the specimen with range estimation, up to the cross section coupling of two elements.

Then by release towards fixed instrument 141 with 0.05cm (0.020 inch)/minute the speed lower oild chuck that moves up test monitoring load and deflection simultaneously.Thereby inset is released tool surfaces with fixed and is contacted, and contact force therebetween is recorded as the function of displacement.Reach peak force and total deflection be about 0.05cm (0.020 inch) stop immediately afterwards the test.

After test is finished,,, make that its cross section is overlapping with validation test inset and the most advanced and sophisticated complete matching of release with the enlargement ratio test sample of opticmicroscope with 100X.

Use following formula to calculate average shear stress:

Average shear stress=(load during first slippage, N (lbs.))/(contact area between inset and aluminium alloy, m ²(in ²)).

Load is drawn into the function of the displacement of inset.Release the load of curve interruptions and remember in following table, 6112N (1374 pounds) among 13046N among the embodiment 1a (2933 pounds) and the embodiment 1b, the load at the interface of the aluminium casting around inset and inset is original slippage.

Table

Embodiment	Load N during first slippage, (lbs.)	Average shear stress MPa	Bonding strength peak value MPa
Embodiment	Load N during first slippage, (lbs.)	Average shear stress MPa	Bonding strength peak value MPa	????1a ????1b	????13046(2933) ????6112(1374)	????46.3 ????21.7	????138.9 ????65.1
????2a ????2b	????13976(3142) ????12708(2857)	????49.6 ????45.1	????148.8 ????135.3	????1a ????1b	????13046(2933) ????6112(1374)	????46.3 ????21.7	????138.9 ????65.1
????2a ????2b	????13976(3142) ????12708(2857)	????49.6 ????45.1	????148.8 ????135.3	????3a ????3b	????15270(3433) ????15808(3554)	????54.2 ????56.1	????162.6 ????168.3
????4a ????4b	????17610(3959) ????12134(2728)	????62.4 ????43.0	????187.2 ????129.0	????3a ????3b	????15270(3433) ????15808(3554)	????54.2 ????56.1	????162.6 ????168.3
????4a ????4b	????17610(3959) ????12134(2728)	????62.4 ????43.0	????187.2 ????129.0	????5a ????5b	????2442(549) ????2615(588)	????8.6 ????9.3	????25.8 ????27.9
????6a ????6b	????3469(780) ????4141(931)	????12.3 ????14.7	????36.9 ????44.1	????5a ????5b	????2442(549) ????2615(588)	????8.6 ????9.3	????25.8 ????27.9
????6a ????6b	????3469(780) ????4141(931)	????12.3 ????14.7	????36.9 ????44.1	????7a ????7b	????3865(869) ????5258(1182)	????13.7 ????18.6	????41.1 ????55.8
????8a ????8b	????3002(675) ????3532(794)	????10.7 ????12.5	????32.1 ????37.5	????7a ????7b	????3865(869) ????5258(1182)	????13.7 ????18.6	????41.1 ????55.8
????8a ????8b	????3002(675) ????3532(794)	????10.7 ????12.5	????32.1 ????37.5	????9a ????9b	????2068(465) ????3256(732)	????7.3 ????11.5	????21.9 ????34.5
????10a ????10b	????5182(1165) ????3256(732)	????18.4 ????11.5	????55.2 ????34.5	????9a ????9b	????2068(465) ????3256(732)	????7.3 ????11.5	????21.9 ????34.5
????10a ????10b	????5182(1165) ????3256(732)	????18.4 ????11.5	????55.2 ????34.5	????11a ????11b	????2927(658) ????3367(757)	????10.3 ????11.9	????30.9 ????35.7
????12a ????12b	????15065(3387) ????10173(2287)	????53.4 ????36.1	????160.2 ????108.3	????11a ????11b	????2927(658) ????3367(757)	????10.3 ????11.9	????30.9 ????35.7
????12a ????12b	????15065(3387) ????10173(2287)	????53.4 ????36.1	????160.2 ????108.3	Comparative examples A 1 Comparative examples A 2	????2411(542) ????1948(438)	????8.6 ????6.9	????25.8 ????20.7
Comparative example B1 comparative example B2 comparative example B3	????2295(516) ????1535(345) ????2113(475)	????8.1 ????5.4 ????7.5	????24.3 ????16.2 ????22.5	Comparative examples A 1 Comparative examples A 2	????2411(542) ????1948(438)	????8.6 ????6.9	????25.8 ????20.7
	????2295(516) ????1535(345) ????2113(475)	????8.1 ????5.4 ????7.5	????24.3 ????16.2 ????22.5	Comparative example C1 comparative example C2	????2740(616) ????970(218)	????9.7 ????3.4	????29.1 ????10.2
Comparative Example D 1	????2113(475)	????7.5	????22.5	Comparative example C1 comparative example C2	????2740(616) ????970(218)	????9.7 ????3.4	????29.1 ????10.2

Comparative Example D 2	????1130(254)	????4.0	????12.0
Comparative Example D 2	????1130(254)	????4.0	????12.0	Comparative Example E	????1245(280)	????4.4	????13.2
Comparative Example F 1 Comparative Example F 2 Comparative Example F 3	????2126(478) ????1535(345) ????1281(288)	????7.5 ????5.4 ????4.5	????22.5 ????16.2 ????13.5	Comparative Example E	????1245(280)	????4.4	????13.2
	????2126(478) ????1535(345) ????1281(288)	????7.5 ????5.4 ????4.5	????22.5 ????16.2 ????13.5	Comparative example G1 comparative example G2	????2480(535) ????1539(346)	????8.5 ????5.5	????25.5 ????16.5
Comparative Example H 1 Comparative Example H 2	????2126(478) ????3176(714)	????7.5 ????11.3	????22.5 ????33.9	Comparative example G1 comparative example G2	????2480(535) ????1539(346)	????8.5 ????5.5	????25.5 ????16.5
Comparative Example H 1 Comparative Example H 2	????2126(478) ????3176(714)	????7.5 ????11.3	????22.5 ????33.9	Comparative Example I	????2798(629)	????9.9	????29.7
Comparative Example J 1 Comparative Example J 2	????3171(713) ????2104(473)	????11.2 ????7.5	????33.6 ????22.5	Comparative Example I	????2798(629)	????9.9	????29.7
Comparative Example J 1 Comparative Example J 2	????3171(713) ????2104(473)	????11.2 ????7.5	????33.6 ????22.5	Comparative example K	????1859(418)	????6.6	????19.8
Comparative example L1 comparative example L2 comparative example L3	????2531(569) ????1806(406) ????1779(400)	????9.0 ????6.4 ????6.3	????27.0 ????19.2 ????18.9	Comparative example K	????1859(418)	????6.6	????19.8
	????2531(569) ????1806(406) ????1779(400)	????9.0 ????6.4 ????6.3	????27.0 ????19.2 ????18.9	Comparative example M1 comparative example M2	????3140(706) ????2971(668)	????11.1 ????10.5	????33.3 ????31.5
Comparative example N1 comparative example N2	????13638(3066) ????7633(1716)	????48.4 ????27.1	????145.2 ????81.3	Comparative example M1 comparative example M2	????3140(706) ????2971(668)	????11.1 ????10.5	????33.3 ????31.5
Comparative example N1 comparative example N2	????13638(3066) ????7633(1716)	????48.4 ????27.1	????145.2 ????81.3	Comparative example O	????2139(481)	????7.6	????22.8

" bonding strength peak value " also is recorded in the table.Use finite element analysis (FEA) calculations incorporated intensity peak.Finite element analysis (FEA) software (from Ansys Inc., Canonsburg, PA obtains with trade(brand)name " ANSYS ") and be used to simulate used inset, show that bonding strength peak value and the average shear stress axis that records are about 3.0.

FEA is calculated as follows.Create the finite element geometric model of specimen.Inset is formed net with the cube component that is of a size of 0.02cm * 0.02cm * 0.05cm (0.01 inch * 0.01 inch * 0.02 inch), and except the top of inset, sizing grid is 0.02cm on all directions.Aluminium and cubes are formed net, and this cubes is 0.05cm (0.02 inch) near the side of inset in the mimic specimen, and its elsewhere is 0.10cm (0.04 inch).The FEA computed in software is along the shear-stress at used inset or each point place, holder surface, and applied pressure is 533.3MPa (is 2900 pounds corresponding to releasing test load).The shear-stress peak value that calculating determines to pass inset surface each point is 140Mpa, and the shear-stress mean value that passes the inset surface is 45.8MPa.The ratio of bonding strength peak value and average shear stress is about 3: 1.

During load during original slippage, corresponding average shear stress and bonding strength peak value also are recorded in and show (wherein being the mean value of quantitative sample) to each embodiment.

Embodiment 2

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 2 (being embodiment 2a and 2b), except before coating, using 400 granularity grinding millers (" DIAMOND WHEEL; ASD400 " obtains with trade(brand)name from NortonCompany) to grind inset, reach inset and mould and be preheated to 550 ℃ and 250 ℃ respectively.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 2a and 2b are in last table.

Embodiment 3

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 3 (being embodiment 3a and 3b), except before coating, using 50-micron diameter granulated glass sphere (from AbrasiveSystems, Inc., Maple Grove, MN obtains) by the abrasive blasting sample, the inset and the mould of band coating are preheated to 550 ℃ and 250 ℃ respectively, and molten aluminium alloy is heated to 760 ℃.

The compression shear strength of embodiment 3 is the function of inset displacement when load, and graphic representation shows in Figure 15.Release the load note of curve interruptions and make label 151.The interruption at the interface of the aluminium casting around inset and inset is original slippage.Load, average shear stress and bonding strength peak records during first slippage of embodiment 3a and 3b are in last table.

Then with the sample of semi-automatic metallographic grinding/burnishing device (from Struers, Inc, Cleveland, OH obtains with trade(brand)name " ABRAMIN ") polishing embodiment 3.Polishing velocity is 150rpm.Polish by 6 steps of following successive.Polishing force is 150N, except step 6 is 250N:

-step 1

The silicon carbide paper (from Pace Technologies, Northbrook, IL obtains) that uses 120 granularities is sample polishing 45 seconds, simultaneously in polishing process continuously and automatically with water droplet to polishing pad.After the polishing, water thoroughly cleans sample.

-step 2

The silicon carbide paper (obtaining from Pace Technologies) that uses 220 granularities is sample polishing 45 seconds, simultaneously in polishing process continuously and automatically with water droplet to polishing pad.After the polishing, water thoroughly cleans sample.

-step 3

The silicon carbide paper (obtaining from Pace Technologies) that uses 600 granularities is sample polishing 45 seconds, simultaneously in polishing process continuously and automatically with water droplet to polishing pad.After the polishing, water thoroughly cleans sample.

-step 4

Use polishing underlay (from Struers, Inc. obtain with trade(brand)name " DP-MOL ") with sample polishing 4.5 minutes, its with the lubricant that periodically drips (from Struers with trade(brand)name " PURON; DP-LUBRICANT " obtain) slight wetting and with 6 microns diamond grit (from Struers with trade(brand)name " DP-SPRAY, P-6 μ m " obtain) injection 1 second.After the polishing, water thoroughly cleans sample.

-step 5

Use polishing underlay (" DP-MOL ") with sample polishing 4.5 minutes, its with the lubricant that periodically drips (from Struers with trade(brand)name " PURON; DP-LUBRICANT " obtain) slight wetting and with 3 microns diamond grit (from Struers with trade(brand)name " DP-SPRAY, P-3 μ m " obtain) injection 1 second.After the polishing, water thoroughly cleans sample.

-step 6

Use the synthetic polishing cloth (obtaining with trade(brand)name " OP-CHEM ") of porous with sample polishing 4.5 minutes, come wetting by water and silica gel suspension (obtaining with trade(brand)name " OP-SSUSPENSION " from Struers) being poured on cloth with hand from Struers.In last 5 seconds of polishing, wash sample with water.After the polishing, dry sample.

Detect the polished cross-sections (seeing also Figure 16) of embodiment 3,162 places, interface 163 of inset matrix 166 and cast alloys do not have tangible border, in nickel or silver, there is not lipostrat, two kinds of aluminium alloys (being the aluminium alloy 166 of inset and the aluminium alloy 163 that comprises the aluminium matrix composite of inset) mix limitedly, and mixing the degree of depth is several Fibre diameters.

Embodiment 4

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 4 (being embodiment 4a and 4b), except mould is preheated to 250 ℃, this inset is preheated to 550 ℃, and molten aluminium alloy is heated to 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 4a and 4b are in last table.

Embodiment 5

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 5 (being embodiment 5a and 5B), except before coating, using 400 granularity grinding miller (" DIAMONDWHEEL; ASD400 ") grinds this inset, and mould is preheated to 250 ℃, and molten aluminium alloy is heated to 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of two samples of embodiment 5 are in last table.

Embodiment 6

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 6 (being embodiment 6a and 6b), except press embodiment 3 described before coating by the abrasive blasting insets, mould is preheated to 250 ℃, molten aluminium alloy is heated to 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 6a and 6b are in last table.

Embodiment 7

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 7 (being embodiment 7a and 7b), except mould is preheated to 250 ℃, molten aluminium alloy is heated to 760 ℃.

The compression shear strength of embodiment 7 is the function of inset displacement when load, and the graphic representation of a sample shows in Figure 15 in two samples of test.Release the load note of curve interruptions and make label 153, it is the mean value of two samples.The interruption at the interface of the aluminium casting around inset and inset is original slippage.Load, average shear stress and bonding strength peak records during first slippage of embodiment 7a and 7b are in last table.

Embodiment 8

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 8 (being embodiment 8a and 8B), except press embodiment 3 described before coating by the abrasive blasting insets, mould is preheated to 550 ℃, molten aluminium alloy is heated to 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 8a and 8b are in last table.

Embodiment 9

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 9 (being embodiment 9a and 9b), except before coating, using 400 granularity grinding millers (" DIAMONDWHEEL; ASD400 ") to grind this inset, mould is preheated to 500 ℃, and molten aluminium alloy is heated to 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 9a and 9b are in last table.

Embodiment 10

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 10 (being embodiment 10a and 10b), except mould is preheated to 500 ℃, molten aluminium alloy is heated to 760 ℃.

The aluminium matrix composite of embodiment 10 is divided into the specimen of 1.16cm (0.46 inch) * 2.5cm (1 inch) diameter.Wherein the cross section of a slice shows at Figure 18, and wherein aluminium matrix composite goods 180 comprise aluminium 181 and inset 182, and this inset comprises aluminium-2% copper alloy and αYang Hualv (" NEXTEL 610 ") fiber.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 10a and 10b are in last table.

Embodiment 11

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 11 (being embodiment 11a and 11b), except the groove that is parallel to inset length before coating is cut into the surface by diamond lap, mould is preheated to 500 ℃, and molten aluminum is heated to 760 ℃.The about 0.17mm of each groove is dark * and 0.3mm is wide, and spacing is 0.62mm.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 11a and 11b are in last table.

Embodiment 12

By embodiment 1 described preparation and test the aluminium matrix composite of two embodiment 12 (being embodiment 12a and 12b), except the groove perpendicular to inset length before coating is cut into the surface by diamond lap, mould is preheated to 500 ℃, and molten aluminium alloy is heated to 760 ℃.The about 0.17mm of each groove is dark * and 0.3mm is wide, and spacing is 0.62mm.

Load, average shear stress and bonding strength peak records during first slippage of embodiment 12a and 12b are in last table.

Comparative examples A

By embodiment 1 described preparation and test the aluminium matrix composite of two Comparative examples A (being Comparative examples A 1 and A2), not coated except inset, mould is preheated to 500 ℃.

Load, average shear stress and bonding strength peak records during first slippage of Comparative examples A 1 and A2 are in last table.

Comparative example B

By embodiment 1 described preparation and test the aluminium matrix composite of three comparative example B (being comparative example B1, B2 and B3), not coated except inset, mould is preheated to 400 ℃.

Load, average shear stress and bonding strength peak records during first slippage of comparative example B1, B2 and B3 are in last table.

Comparative example C

By embodiment 1 described preparation and test the aluminium matrix composite of two comparative example C (being comparative example C1 and C2), except inset not coated, inset is surperficial with 400 granularity grinding miller (" DIAMOND WHEEL, and ASD400 ") grinds, and this inset is preheated to 193 ℃.

Average load, average shear stress and bonding strength peak records during first slippage of comparative example C1 and C2 are in last table.

Comparative Example D

By embodiment 1 described preparation and test the aluminium matrix composite of two Comparative Example D (being Comparative Example D 1 and D2), not coated except inset, inset is preheated to 193 ℃.

Load, average shear stress and bonding strength peak records during first slippage of Comparative Example D 1 and D2 are in last table.

Comparative Example E

Press embodiment 1 described preparation and the test Comparative Example E aluminium matrix composite, except inset not coated.

Load, average shear stress and bonding strength peak records during first slippage of Comparative Example E are in last table.

Comparative Example F

By embodiment 1 described preparation and test the aluminium matrix composite of three Comparative Example F (being Comparative Example F 1, F2 and F3), not coated except inset, use 400 granularity grinding miller (" DIAMOND WHEEL, ASD400 ") grinds inset.

Load, average shear stress and bonding strength peak records during first slippage of three samples of Comparative Example F 1, F2 and F3 are in last table.

Comparative example G

By embodiment 1 described preparation and test the aluminium matrix composite of three comparative example G (being comparative example G1, G2 and G3), not coated except inset, press embodiment 3 described sandblast inset surfaces.

Load, average shear stress and bonding strength peak records during first slippage of comparative example G1, G2 and G3 are in last table.

Comparative Example H

By embodiment 1 described preparation and test the aluminium matrix composite of two Comparative Example H (being Comparative Example H 1 and H2), not coated except inset, press embodiment 3 described sandblast inset surfaces, mould is preheated to 400 ℃.

Press a sample of embodiment 3 described polishing Comparative Example H.Detect the polished cross-sections (seeing also Figure 17) of Comparative Example H, show tangible border, be considered to oxide skin at 182 places, interface of inset matrix 186 and cast alloys 183.

Load, average shear stress and bonding strength peak records during first slippage of Comparative Example H 1 and H2 are in last table.

Comparative Example I

Press the aluminium matrix composite of embodiment 1 described preparation and test Comparative Example I, except applying inset with about 12 microns nickel, inset is preheating not.

Load, average shear stress and bonding strength peak records during first slippage of Comparative Example I are in last table.

Comparative Example J

By embodiment 1 described preparation and test the aluminium matrix composite of two Comparative Example J (being Comparative Example J 1 and J2), except applying inset with the nickel described in the Comparative Example I, mould is preheated to 400 ℃.

Load, average shear stress and bonding strength peak records during first slippage of two samples of Comparative Example J are in last table.

Comparative example K

Press the aluminium matrix composite of embodiment 1 described preparation and test comparative example K, except applying inset with about 12 microns copper, inset is preheating not.

Load, average shear stress and bonding strength peak records during first slippage of comparative example K are in last table.

Comparative example L

By embodiment 1 described preparation and test the aluminium matrix composite of three comparative example L (being comparative example L1, L2 and L3), except applying inset with the copper described in the comparative example K, mould is preheated to 400 ℃.

Load, average shear stress and bonding strength peak records during first slippage of three samples of comparative example L are in last table.

Comparative example M

By embodiment 1 described preparation and test the aluminium matrix composite of two comparative example M (being comparative example M1 and M2), comprise the groove that cuts out by embodiment 12 except inset, this inset is not coated, and mould is preheated to 500 ℃, and the temperature of molten aluminium alloy is 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of comparative example M1 and M2 are in last table.

Comparative example N

By embodiment 1 described preparation and test the aluminium matrix composite of two comparative example N (being comparative example N1 and N2), except comprising the groove that cuts out by embodiment 13, but this inset is not coated, and mould is preheated to 500 ℃, and the temperature of molten aluminium alloy is 760 ℃.

Load, average shear stress and bonding strength peak records during first slippage of comparative example N1 and N2 are in last table.

Comparative example O

Press the aluminium matrix composite of embodiment 1 described preparation and test comparative example O, except applying inset with about 12 microns zinc, mould is preheated to 500 ℃, and this inset is preheated to 291 ℃.

Load, average shear stress and bonding strength peak records during first slippage of comparative example O are in last table.

Variations and modifications of the present invention are obvious for those skilled in the art, and this can not depart from the scope of the present invention and spirit, also should be appreciated that to the invention is not restricted to wherein said embodiment.

Claims

1. metal-matrix composite goods, it comprises:

Basically successive ceramic oxide fibers and be selected from first kind of metal of aluminium, its alloy and composition thereof, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, reach wherein said first kind of metal and extend along at least a portion of the described ceramic oxide fibers of successive basically length, described first kind of metal has outside surface; And

Second kind of metal on described first kind of outer metallic surface, described second kind of metal has positive Gibbs oxidation free energy at least when being higher than 200 ℃, and the thickness of described second kind of metal is at least 8 microns.

2. metal-matrix composite goods as claimed in claim 1, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

3. metal-matrix composite goods as claimed in claim 1 also are included in the third metal between the outside surface of described second kind of metal and described first kind of metal.

4. metal-matrix composite goods as claimed in claim 1, the thickness of wherein said second kind of metal are at least 10 microns.

5. metal-matrix composite goods as claimed in claim 1, the thickness of wherein said second kind of metal are about 10～about 15 microns.

6. metal-matrix composite goods as claimed in claim 1, wherein said second kind of metal are at least a in gold or the silver.

7. metal-matrix composite goods as claimed in claim 1, wherein said first kind of metal is a kind of aluminium alloy.

8. metal-matrix composite goods as claimed in claim 7, wherein said aluminium alloy are 200 series alloys.

9. metal-matrix composite goods as claimed in claim 8, wherein said aluminium alloy are 200 series alloys that are selected from A201.1 aluminium alloy, 201.2 aluminium alloys, A206.0 aluminium alloy and 224.2 aluminium alloys.

10. metal-matrix composite goods as claimed in claim 8, wherein said aluminium alloy comprise the Cu that is at least 1.5wt.% by the total restatement of described aluminium alloy.

11. metal-matrix composite goods as claimed in claim 10, wherein said aluminium alloy comprise by the impurity of the total restatement of described aluminium alloy less than 0.25wt.%.

12. metal-matrix composite goods as claimed in claim 11, wherein said aluminium alloy comprise the Cu that is at least 1.5wt.% by the total restatement of described aluminium alloy.

13. metal-matrix composite goods as claimed in claim 11, wherein said aluminium alloy comprises the Cu by the total restatement 1.5～2.5wt.% of described aluminium alloy.

14. metal-matrix composite goods as claimed in claim 11, wherein said aluminium alloy comprises the Cu by the total restatement 1.8～2.2wt.% of described aluminium alloy.

15. metal-matrix composite goods as claimed in claim 7, wherein said aluminium alloy comprises the Cu by the total restatement 1.5～2.5wt.% of described aluminium alloy.

16. metal-matrix composite goods as claimed in claim 1, the wherein said ceramic oxide fibers of successive basically is a polycrystalline αYang Hualv fiber.

17. metal-matrix composite goods as claimed in claim 16, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, and wherein said polycrystalline αYang Hualv fiber accounts for the Al of sapphire whisker gross weight greater than about 99wt.% by theoretical oxide compound ₂O ₃SiO with about 0.2-0.5wt.% ₂, and the mean particle size of the αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

18. metal-matrix composite goods as claimed in claim 16, wherein said αYang Hualv fiber account for 50% volume that is at least of described metal matrix goods cumulative volume.

19. metal-matrix composite goods as claimed in claim 1, the wherein said ceramic oxide fibers of successive basically accounts for 50% volume that is at least of described metal matrix goods cumulative volume.

20. metal-matrix composite goods as claimed in claim 1, wherein said metal-matrix composite goods can elongate, and have the cross-sectional area of substantially constant.

21. metal-matrix composite goods as claimed in claim 1 comprise the first layer and second layer successive ceramic oxide fibers basically.

22. metal-matrix composite goods as claimed in claim 21, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

23. metal-matrix composite goods, it comprises:

Basically successive ceramic oxide fibers and be selected from the metal of aluminium, its alloy and composition thereof, wherein said metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, reach wherein said metal and extend along at least a portion of the described ceramic oxide fibers of successive basically length, described metal has outside surface;

Ni is on the outside surface of described metal, and Ni has outside surface; And

Ag is on the outside surface of Ni, and the thickness of Ag is at least 8 microns.

24. metal-matrix composite goods as claimed in claim 23, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

25. metal-matrix composite goods as claimed in claim 23, wherein the thickness of Ag is at least 10 microns.

26. metal-matrix composite goods as claimed in claim 23, wherein the thickness of Ag is about 10～about 15 microns.

27. metal-matrix composite goods as claimed in claim 23, wherein said metal are a kind of aluminium alloys.

28. metal-matrix composite goods as claimed in claim 27, wherein said aluminium alloy are 200 series alloys.

29. metal-matrix composite goods as claimed in claim 28, wherein said aluminium alloy are 200 series alloys that are selected from A201.1 aluminium alloy, 201.2 aluminium alloys, A206.0 aluminium alloy and 224.2 aluminium alloys.

30. metal-matrix composite goods as claimed in claim 28, wherein said aluminium alloy comprises the Cu by the total restatement 1.5～2.5wt.% of described aluminium alloy.

31. metal-matrix composite goods as claimed in claim 28, wherein said aluminium alloy comprises the Cu by the total restatement 1.8～2.2wt.% of described aluminium alloy.

32. metal-matrix composite goods as claimed in claim 23, the wherein said ceramic oxide fibers of successive basically is a polycrystalline αYang Hualv fiber.

33. metal-matrix composite goods as claimed in claim 32, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, and wherein said polycrystalline αYang Hualv fiber accounts for the Al of sapphire whisker gross weight greater than about 99wt.% by theoretical oxide compound ₂O ₃SiO with about 0.2-0.5wt.% ₂, and its mean particle size of αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

34. metal-matrix composite goods as claimed in claim 32, wherein said αYang Hualv fiber account for 50% volume that is at least of described metal matrix goods cumulative volume.

35. metal-matrix composite goods as claimed in claim 23 comprise the first layer and second layer successive ceramic oxide fibers basically.

36. metal-matrix composite goods as claimed in claim 35, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

37. a method for preparing the metal-matrix composite goods, described method comprises:

Fixing successive ceramic oxide fibers basically in being selected from first kind of metal of aluminium, its alloy and composition thereof, so that described first kind of metal extends along length at least a portion of the described ceramic oxide fibers of successive basically, described first kind of metal has outside surface; And

Provide second kind of metal so that the metal-matrix composite goods to be provided on the outside surface of described first kind of metal, it comprises:

The described ceramic oxide fibers of successive basically and described first kind of metal,

Wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, wherein said first kind of metal extends along at least a portion of the described ceramic oxide fibers of successive basically length, wherein said second kind of metal is positioned on the outside surface of described first kind of metal, described second kind of metal has positive Gibbs oxidation free energy at least when being higher than 200 ℃, and the thickness of wherein said second kind of metal is at least 8 microns.

38. method as claimed in claim 37, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

39. method as claimed in claim 37, wherein said second kind of metal are at least a in gold or the silver.

40. method as claimed in claim 37, wherein said first kind of metal is a kind of aluminium alloy.

41. method as claimed in claim 40, wherein said aluminium alloy are 200 series alloys that are selected from A201.1 aluminium alloy, 201.2 aluminium alloys, A206.0 aluminium alloy and 224.2 aluminium alloys.

42. method as claimed in claim 40, wherein said aluminium alloy comprises the Cu by the total restatement 1.5～2.5wt.% of described aluminium alloy.

43. method as claimed in claim 40, wherein said aluminium alloy comprises the Cu by the total restatement 1.8～2.2wt.% of described aluminium alloy.

44. method as claimed in claim 37, wherein said fiber account for 50% volume that is at least of described metal matrix goods cumulative volume.

45. method as claimed in claim 37 comprises the first layer and second layer successive ceramic oxide fibers basically.

46. method as claimed in claim 45, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

47. a method for preparing the metal-matrix composite goods, described method comprises:

Fixing successive ceramic oxide fibers basically in the metal that is selected from aluminium, its alloy and composition thereof makes described metal extend along at least a portion of the described ceramic oxide fibers of successive basically length, and described metal has outside surface; And

Provide Ni on the outside surface of described metal, Ni has outside surface; And

Provide Ag on the outside surface of Ni, the thickness of Ag is at least 8 microns,

So that the metal-matrix composite goods to be provided, it comprises:

Described ceramic oxide fibers of successive basically and described metal, wherein said metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, reach wherein said metal and extend along length at least a portion of the described ceramic oxide fibers of successive basically, described metal has outside surface;

Ni is on the outside surface of described metal; And

Ag is on the outside surface of Ni, and wherein the thickness of Ag is at least 8 microns.

48. method as claimed in claim 47, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

49. method as claimed in claim 47, wherein said first kind of metal is a kind of aluminium alloy.

50. method as claimed in claim 49, wherein said aluminium alloy are 200 series alloys that are selected from A201.1 aluminium alloy, 201.2 aluminium alloys, A206.0 aluminium alloy and 224.2 aluminium alloys.

51. method as claimed in claim 49, wherein said aluminium alloy comprises the Cu by the total restatement 1.5～2.5wt.% of described aluminium alloy.

52. method as claimed in claim 49, wherein said aluminium alloy comprises the Cu by the total restatement 1.8～2.2wt.% of described aluminium alloy.

53. method as claimed in claim 47, wherein said fiber account for 50% volume that is at least of described metal matrix goods cumulative volume.

54. method as claimed in claim 47 comprises the first layer and second layer successive ceramic oxide fibers basically.

55. method as claimed in claim 54, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

56. metal-matrix composite goods, the inset that it comprises first kind of metal and strengthens described first kind of metal, wherein said first kind of metal is selected from aluminium, its alloy and composition thereof, wherein said inset comprises basically the successive ceramic oxide fibers and is selected from aluminium, second kind of metal of its alloy and composition thereof, wherein said second kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, wherein said second kind of metal extends along at least a portion of the described ceramic oxide fibers of successive basically length, wherein between described first kind of metal and described inset, interfacial layer is arranged, wherein the bonding strength peak value of the interfacial layer between described first kind of metal and described inset is at least 100MPa, and wherein said metal-matrix composite goods are calipers.

57. metal-matrix composite goods as claimed in claim 56, the wherein said ceramic oxide fibers of successive basically are vertically to arrange.

58. metal-matrix composite goods as claimed in claim 56, wherein said first kind of metal is one of 300 or 400 series alloys, and wherein said second kind of metal is a kind of 200 series alloys.

59. metal-matrix composite goods as claimed in claim 58, wherein said 200 series alloys are selected from A201.1 aluminium alloy, 201.2 aluminium alloys, A206.0 aluminium alloy and 224.2 aluminium alloys, and wherein said first kind of metal is 300 series alloys that are selected from A319.1 aluminium alloy, 354.1 aluminium alloys, 355.2 aluminium alloys and A356.1 aluminium alloy.

60. metal-matrix composite goods as claimed in claim 58, wherein said 200 series alloys are selected from A201.1 aluminium alloy, 201.2 aluminium alloys, A206.0 aluminium alloy and 224.2 aluminium alloys, and wherein said first kind of metal is 400 series alloys that are selected from 443.2 aluminium alloys and 444.2 aluminium alloys.

61. metal-matrix composite goods as claimed in claim 56, the interfacial layer bonding strength peak value between wherein said first kind of metal and the described inset is at least 125MPa.

62. metal-matrix composite goods as claimed in claim 56, the bonding strength peak value of the interfacial layer between wherein said first kind of metal and the described inset is at least 150MPa.

63. metal-matrix composite goods as claimed in claim 56, the bonding strength peak value of interfacial layer is at least 175MPa between wherein said first kind of metal and the described inset.

64. metal-matrix composite goods as claimed in claim 56, the bonding strength peak value of interfacial layer is at least 180MPa between wherein said first kind of metal and the described inset.

65. metal-matrix composite goods as claimed in claim 56, described interfacial layer does not contain aerobic.

66. metal-matrix composite goods as claimed in claim 56, wherein said interfacial layer comprises second kind of metal of the Gibbs oxidation free energy that having of mean vol is positive when being higher than at least 200 ℃, and the mean vol of wherein said second kind of metal is high in described interfacial layer than in described first kind of metal.

67. metal-matrix composite goods as claimed in claim 56, wherein said interfacial layer comprise Ag and the Ni that is higher than the mean vol that exists in described first kind of metal.

68. metal-matrix composite goods as claimed in claim 56, the wherein said ceramic oxide fibers of successive basically is a polycrystalline αYang Hualv fiber.

69. as the described metal-matrix composite goods of claim 68, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, and wherein said polycrystalline αYang Hualv fiber comprises the Al greater than about 99wt.% that accounts for the sapphire whisker gross weight by theoretical oxide compound ₂O ₃SiO with about 0.2-0.5wt.% ₂, and the mean particle size of the αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

70. as the described metal-matrix composite goods of claim 68, wherein said αYang Hualv fiber accounts for 50% volume that is at least of described metal matrix goods cumulative volume.

71. metal-matrix composite goods as claimed in claim 56, the wherein said ceramic oxide fibers of successive basically accounts for 50% volume that is at least of described metal matrix goods cumulative volume.

72. metal-matrix composite goods as claimed in claim 56 also comprise at least two described insets.

73. metal-matrix composite goods as claimed in claim 56 comprise at least four described insets.

74. the disc brake of a motor vehicle, it comprises rotor; Place the opposite side of rotor and removable and be mated arresting inside brake sheet and outer brake(-holder) block; Be used to make the piston of inside brake sheet near rotor; And caliper as claimed in claim 57, it is included in has the cylindrical body element that is used to hold described piston on rotor one side, be positioned at the rotor opposite side and be used to support the arm linear element of outer brake(-holder) block, and the bridge between described body element and described arm linear element extends through described rotor plane.

75. metal-matrix composite goods as claimed in claim 56, wherein first kind and second kind of metal each all have fusing point, and the fusing point of wherein said second kind of metal is higher than 20 ℃ of the fusing points of described first kind of metal at least.

76. metal-matrix composite goods as claimed in claim 56, wherein said second kind of metal are a kind of comprising by the total restatement of the described aluminium alloy aluminium alloy of the Cu of 1.5wt.% at least.

77. metal-matrix composite goods as claimed in claim 56, wherein said second kind of metal are a kind of aluminium alloys that comprises by the Cu of the total restatement 1.5～2.5wt.% of described aluminium alloy.

78. metal-matrix composite goods as claimed in claim 56, wherein said second kind of metal are a kind of aluminium alloys that comprises by the Cu of the total restatement 1.8～2.2wt.% of described aluminium alloy.

79. metal-matrix composite goods as claimed in claim 56, described interfacial layer does not contain aerobic.

80. metal-matrix composite goods as claimed in claim 56 comprise the first layer and second layer successive ceramic oxide fibers basically.

81. as the described metal-matrix composite goods of claim 80, the wherein said ceramic oxide fibers of successive basically is vertically to arrange.

82. a method for preparing the metal-matrix composite goods, described method comprises:

Inset is put into mould, described inset comprises basically the successive ceramic oxide fibers and is selected from aluminium, first kind of metal of its alloy and combination thereof, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, and wherein said first kind of metal extends along at least a portion of the described ceramic oxide fibers of successive basically length, described first kind of metal has outside surface, and second kind of metal on described first kind of outer metallic surface, described second kind of metal has positive Gibbs oxidation free energy at least when being higher than 200 ℃, the thickness of described second kind of metal is at least 8 microns;

The third metal of fusion that is selected from aluminium, its alloy and combination thereof is put into mould; And

Cool off the third metal of described fusion so that the metal-matrix composite goods to be provided.

83., comprise the first layer and second layer successive ceramic oxide fibers basically as the described method of claim 81.

84. as the described method of claim 82, wherein said first kind of metal is a kind of 200 series alloys, and wherein said the third metal is a kind of 300 or 400 series alloys.

85. as the described method of claim 82, the wherein said ceramic oxide fibers of successive basically is a polycrystalline αYang Hualv fiber.

86. as the described method of claim 85, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, wherein said polycrystalline αYang Hualv fiber comprises by theoretical oxide compound and accounts for the Al of sapphire whisker gross weight greater than about 99wt.% ₂O ₃SiO with about 0.2-0.5wt.% ₂, and the mean particle size of the αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

87. as the described method of claim 85, wherein said αYang Hualv fiber accounts for 50% volume that is at least of described inset cumulative volume.

88. as the described method of claim 85, the third metal of wherein said fusion was in molten state less than 75 seconds in mould.

89. as the described method of claim 85, the third metal of wherein said fusion was in molten state less than 60 seconds in mould.

90. as the described method of claim 82, wherein before the third metal of fusion is put into mould, described inset has first kind of outside dimension shape, and wherein have second kind of size shape with described inset metal-matrix composite is provided after at cooling described fusion the third metal, wherein said first kind substantially the same with described second kind of size shape.

91. as the described method of claim 82, before the third metal of described fusion was about to put into mould, the temperature of described inset was at least 500 ℃.

92. as the described method of claim 82, wherein said second kind of metal is at least a in gold or the silver, and wherein said first kind and the third metal are aluminium alloys.

93. as the described method of claim 82, the wherein said ceramic oxide fibers of successive basically accounts for 50% volume that is at least of described inset cumulative volume.

94. as the described method of claim 82, wherein said first kind of metal is a kind of aluminium alloy that comprises by the Cu of the total restatement 1.5～2.5wt.% of described aluminium alloy.

95. as the described method of claim 82, wherein said first kind of metal is a kind of aluminium alloy that comprises by the Cu of the total restatement 1.8～2.2wt.% of described aluminium alloy.

96., comprise the first layer and second layer successive ceramic oxide fibers basically as the described method of claim 82.

97. as the described method of claim 96, the wherein said ceramic oxide fibers of successive basically is vertically to arrange.

98. as the described method of claim 82, the third metal of wherein said fusion was in molten state less than 75 seconds in mould.

99. a method for preparing the metal-matrix composite goods, described method comprises:

Inset is put into mould, described inset comprises successive ceramic oxide fibers and the first kind of metal that is selected from aluminium, its alloy and combination thereof basically, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, and wherein said first kind of metal extends along at least a portion of the described ceramic oxide fibers of successive basically length, described first kind of metal has outside surface, Ni is on described first kind of outer metallic surface, Ni has outside surface, Ag is on the outside surface of Ni, and the thickness of Ag is at least 8 microns;

The second kind of metal of fusion that is selected from aluminium, its alloy and combination thereof put into mould; And

Cool off second kind of metal of described fusion so that the metal-matrix composite goods to be provided.

100. as the described method of claim 99, the wherein said ceramic oxide fibers of successive basically is vertically to arrange.

101. as the described method of claim 99, wherein said first kind of metal is a kind of 200 series alloys, and wherein said second kind of metal is one of 300 or 400 series alloys.

102. as the described method of claim 99, the wherein said ceramic oxide fibers of successive basically is a polycrystalline αYang Hualv fiber.

103. as the described method of claim 102, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, wherein said polycrystalline αYang Hualv fiber comprises by theoretical oxide compound and accounts for the Al of sapphire whisker gross weight greater than about 99wt.% ₂O ₃SiO with about 0.2-0.5wt.% ₂, and the mean particle size of the αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

104. as the described method of claim 102, wherein said αYang Hualv fiber accounts for 50% volume that is at least of described inset cumulative volume.

105. as the described method of claim 99, wherein said first kind of metal is a kind of aluminium alloy that comprises by the Cu of the total restatement 1.5～2.5wt.% of described aluminium alloy.

106. as the described method of claim 99, wherein said first kind of metal is a kind of aluminium alloy that comprises by the Cu of the total restatement 1.8～2.2wt.% of described aluminium alloy.

107. as the described method of claim 99, second kind of metal of wherein said fusion was in molten state less than 75 seconds in mould.

108. as the described method of claim 99, second kind of metal of wherein said fusion was in molten state less than 60 seconds in mould.

109. as the described method of claim 99, wherein described inset has first kind of outside dimension shape before second kind of metal of fusion put into mould, and wherein have second kind of size shape with described inset metal-matrix composite is provided after at cooling described fusion second kind of metal, wherein said first kind substantially the same with described second kind of size shape.

110. as the described method of claim 99, before second kind of metal of described fusion was about to put into mould, the temperature of described inset was at least 500 ℃.

111., comprise the first layer and second layer successive ceramic oxide fibers basically as the described method of claim 99.

112. as the described method of claim 111, the wherein said ceramic oxide fibers of successive basically is vertically to arrange.

113. as the described method of claim 99, second kind of metal of wherein said fusion was in molten state less than 75 seconds in mould.

114. a method for preparing the metal-matrix composite inset, described inset is used to prepare the metal-matrix composite goods, and described method comprises:

Design metal-matrix composite goods strengthen inset to comprise metal-matrix composite, and described inset comprises:

Basically successive ceramic oxide fibers and be selected from first kind of metal of aluminium, its alloy and combination thereof, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, and wherein said first kind of metal extends along at least a portion of the described ceramic oxide fibers of successive basically length; And

Prepare metal-matrix composite by the design that forms and strengthen inset, it comprises:

Described ceramic oxide fibers of successive basically and the described first kind of metal that is selected from aluminium, its alloy and combination thereof, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, reach wherein said first kind of metal and extend along at least a portion of the described ceramic oxide fibers of successive basically length, described first kind of metal has outside surface; And also comprise:

115. as the described method of claim 114, wherein said successive ceramic oxide fibers is a polycrystalline αYang Hualv fiber.

116. as the described method of claim 114, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, wherein said polycrystalline αYang Hualv fiber comprises by theoretical oxide compound and accounts for the Al of sapphire whisker gross weight greater than about 99wt.% ₂O ₃SiO with about 0.2-0.5wt.% ₂, and the mean particle size of the αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

117. as the described method of claim 114, wherein said αYang Hualv fiber accounts for 50% volume that is at least of described inset cumulative volume.

118., comprise the first layer and second layer successive ceramic oxide fibers basically as the described method of claim 114.

119. a method for preparing the metal-matrix composite inset, described inset is used to prepare the metal-matrix composite goods, and described method comprises:

Basically successive ceramic oxide fibers and be selected from the metal of aluminium, its alloy and composition thereof, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, and wherein said metal extends along at least a portion of the described ceramic oxide fibers of successive basically length; And

Described ceramic oxide fibers of successive basically and the metal that is selected from aluminium, its alloy and composition thereof, wherein said first kind of metal is fixed on the appropriate location with the described ceramic oxide fibers of successive basically, reach wherein said metal and extend along at least a portion of the described ceramic oxide fibers of successive basically length, described first kind of metal has outside surface; And also comprise:

120. as the described method of claim 119, wherein said successive ceramic oxide fibers is a polycrystalline αYang Hualv fiber.

121. as the described method of claim 119, the average tensile strength of wherein said polycrystalline αYang Hualv fiber is at least 2.8GPa, wherein said polycrystalline αYang Hualv fiber comprises by theoretical oxide compound and accounts for the Al of sapphire whisker gross weight greater than about 99wt.% ₂O ₃SiO with about 0.2-0.5wt.% ₂, and the mean particle size of the αYang Hualv in the wherein said polycrystalline αYang Hualv fiber is less than 1 micron.

122. as the described method of claim 119, wherein said αYang Hualv fiber accounts for 50% volume that is at least of described inset cumulative volume.

123., comprise the first layer and second layer successive ceramic oxide fibers basically as the described method of claim 119.