CA1236709A - Wear resistant material and method for making - Google Patents
Wear resistant material and method for makingInfo
- Publication number
- CA1236709A CA1236709A CA000455213A CA455213A CA1236709A CA 1236709 A CA1236709 A CA 1236709A CA 000455213 A CA000455213 A CA 000455213A CA 455213 A CA455213 A CA 455213A CA 1236709 A CA1236709 A CA 1236709A
- Authority
- CA
- Canada
- Prior art keywords
- cermet particles
- wear
- cermet
- composite
- particles
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/09—Mixtures of metallic powders
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B24—GRINDING; POLISHING
- B24D—TOOLS FOR GRINDING, BUFFING OR SHARPENING
- B24D3/00—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents
- B24D3/02—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent
- B24D3/04—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent and being essentially inorganic
- B24D3/06—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent and being essentially inorganic metallic or mixture of metals with ceramic materials, e.g. hard metals, "cermets", cements
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B24—GRINDING; POLISHING
- B24D—TOOLS FOR GRINDING, BUFFING OR SHARPENING
- B24D3/00—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents
- B24D3/02—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent
- B24D3/04—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent and being essentially inorganic
- B24D3/06—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent and being essentially inorganic metallic or mixture of metals with ceramic materials, e.g. hard metals, "cermets", cements
- B24D3/08—Physical features of abrasive bodies, or sheets, e.g. abrasive surfaces of special nature; Abrasive bodies or sheets characterised by their constituents the constituent being used as bonding agent and being essentially inorganic metallic or mixture of metals with ceramic materials, e.g. hard metals, "cermets", cements for close-grained structure, e.g. using metal with low melting point
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Ceramic Engineering (AREA)
- Inorganic Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
TITLE
WEAR RESISTANT MATERIAL AND METHOD FOR MAKING
INVENTORS
Roch Angers Blaise Champagne ABSTRACT OF THE DISCLOSURE
A wear-resistant composite material and method of making said material. The material comprises hard cermet particles dispersed in a metallic matrix, and particularly of cemented tungsten carbide particles dispersed in a steel powder matrix. This wear-resistant composite mate-rial is made by consolidating mixtures of steel powders and hard cermet particles. Porosity of the composite is removed by infiltrating. This material is suited for applications which require good wear and abrasion resistance and toughness, such as for inserts for snow plows, wearing parts of excavators, mining vehicles and other equipment subject to abrasion and impact.
WEAR RESISTANT MATERIAL AND METHOD FOR MAKING
INVENTORS
Roch Angers Blaise Champagne ABSTRACT OF THE DISCLOSURE
A wear-resistant composite material and method of making said material. The material comprises hard cermet particles dispersed in a metallic matrix, and particularly of cemented tungsten carbide particles dispersed in a steel powder matrix. This wear-resistant composite mate-rial is made by consolidating mixtures of steel powders and hard cermet particles. Porosity of the composite is removed by infiltrating. This material is suited for applications which require good wear and abrasion resistance and toughness, such as for inserts for snow plows, wearing parts of excavators, mining vehicles and other equipment subject to abrasion and impact.
Description
~3~
BACKGROUND OF l'HE tNVENTION
This invention relates to wear-resistant composite materLa]s.
The wear resistance of materials normally increases with l1ard-ness but it is also strongly affected by their microstructural character-iatics, especially by the presence oE a second phase. It is known thatabrasion resistance of steels lncreases when they contain hard second phases like carbides. ~lowever, the abrasive wear of steels containlng a large proportion of carbides depends fitrongly on the cohesion of these carbidea with the matrix, as well as on tlle si~e, shape and brittleness of the carbides. The highest abrasion resistances are generally found in alloys havlng hard second phases coherently bonded to the matrix and not distributed as a brittle contim1ous network in it. Many works have been done to attain this objective using powder meT~allurgy techniques, especi-ally in the production of rnetallic articles containing a disperslon of hard particles which consist of intermetallic or ceramic (usually carhide particles). There are two drawbacks for this kind of material. First, these intermetallic or ceramic particles are brittle and can fracture under high stress abrasive condition~s, and secondly, they cannot be easily or properly bonded to the matrix. Under such condLtions, the hard phase tends to be dislodged, thus giving rise to acceLerated wear.
It has been proposed in United States Patent No. 3,790,353, to provide a wear resistant pad by uti1i~ing cemented metal carbide parti-cles in a metal matrix wherein the metal matrix is melted to form the wear pad. The above ment:Lolled patent specTLEies the pad thickrless Ln terms of partlcle size which places a slgn-LEicant restrictlon on tlle product geometry particularly witrl regard to product thickness. It wL1L
be apparent that wlth melting oTE the matrix the hLgher density cermet partLcles ~ill tend to settle, and therefore, thickness cannot be increased as desired unless a suEficiently hLgh proportion oE cerlTIet partLcLes are used in order that tlle partLcles contact one another all(l cannot aettle. Such high proportions of cermet parttc]es, namely greater than about 50% by volume, provide a rLaterlal with less toughness than obtninable with lower proportions. Also, tlle higll temperatures required Eor melting cause a reaction wLth the cermet produclllg a brittle carbide at the cermet-matrix interface, further reducing toughness.
V~
It has been found tllflt the limitation~s of prior n~tllods an he overcome, and specifically, that a wkle range o~ thiclcness, sllape or com-positions of tougll wear-resistant cl~mpo6ites call he rrovided by tlle use of cermet partlcles, a steel powder matrix, an-l consolidating hy sublect-lng to lleat in the solld state. Slncc? tlle n~trix Ls not melted in tbepresent lnventlon, the aforesaid .settllnr prohlem does not ~rise an(l the composltlon in terms of cermet particle si~e, p;trticle-to-matrix propor-tlon, can be chosen to provide tlle clcs~recl wenr- resistant prorertles nncl toughl1es~ characterlstics without tlle previous restrictlons of product thickness, etc.
In accordance with tlle prese!lt invention, a wear-resistallt com-posite ls provided wltll a composite comrrisillg cermet particles dispersed ln a iron-base matrix that i8 consolidsted in the so1lcl state.
The wear-resistant materia] of tlle ~resent invelltion is made by forming a mixture of cermet particles 3nd all iron-bAse n~3trlx powdc~r, and consolidating the mixture by subjecting to lleat at a temperature below the melting polnt of the matrix.
In accordance Witll one specific embodiment oE tl-e inveTItiorl, consolidation co~prises slntering tlle mlxture nlld in~iltratLng witll a metal having a relatlvely low melting point.
BP~IEF DESCI'IPTION ()F Tlll URAWINGS
Figure 1 is a micrograph fillOW~, tlle mi crostructure of an examrle of a com~osite made in accord;lllte with one elllbodiment of the invention.
Fig~re 2 is a baclcscatterecl e~ectroll micrograph sllowillg the microstructure of a wear-reslstant composite materlal mflde by the metllod describecl in Example l.
DESCRIPTION OF PRIFI.RPNiD E~ ()DI~IENTS
The prodnceion oE cermet particle~s as usecl in the preseot inventlon, iæ known. One metlloci involves agglooleratlng WC and ~etal binder powders (0.2 to lO ~m) and consoli(lating by vacuum sintering. Tlle 7~
most commonly used and preferred cermet is tun~sten carbide with cohalt as blnder. Nickel, or nickel or cobalt alloys, may also be used as hind-er. For the present invention, the preEerred size range of the cermet particles is 0.1 to 5 mm, and pre~eral)ly from 0.5 to 2 mm. Preferably the cermet particles are generally spllerical, since these are less susceptlble to breakap,e.
The matrix ~aterial ~y comprtse var~ou~q iron-ba~se powders and, preferably, carbon steel9 alloy steel ~r sta-lnless steel. The ma~rix materlal may be prepared by known techn~ques.
Productlon of the composite ll~volves mi~inK the cermet parti-cles with the steel ~tr~x powder. The cllolce of the ~Itrix and the pro-portions will depend on the particul~r propertles, such a~s wear-resist-ance and tougllness, desired. It appears that suitable compof,~tes can be provided with volume proportlons oF the cermet partlcles up to nbout 6()%, and preferably, in the range of 20 tn 40~.
The mixture is then consolid.~ted by subject~ng to heat at a temperature below the melting pOi[lt of the matrix. Prior to consolida-tion, the mixture may ~e compacted or mnlded to the desired shape. The mlsture may also be formed by slip~casting.
Consolidation involves, sintering and subsequent infiltrating, or simultaneous sintering and infiltrating, with metals such as copper, copper alloys or nickel alloys.
The micrograph of Figure 1 shows the resulting microstructure in a composite consolidated with sintering and infiltration. It can be seen that the ~C~Co cermet particles are distributed in a copper infil-trated steel matrix and that the particles are surrounded by a layer of steel. There is little or no copper film immediately around the cemented particles. The steel matrix deforms plastically during cold pressing and bonds to cermet particles preventing massive copper penetration to the surface of these particles. ~xamination of fracture surfaces oE green compacts has shown that a steel layer is present on the surface of ~36~7~
cemented particles. It was observed tllat the porosity in the composite -ieces before consolidation tends to concentrnte nround cemented c<qrbLde particles. Tbis local poroslty is detrimelltal to the collesion betwr-~>n tlle cermet particles and the ~ trix nn(l to the strengtl1 of ti~e non infil-trated sintered specimens. In SllCh nOn~ fi1trated SpeC:LlnerlS, Celllentedpartlcles are easily pulled out oi tl1e materi.ll whicl1 doe6 not occllr wlth material lnf1Ltrated in accord.lllce wlth the preser1t invention. Sim-ilarly the alternate n~thods of consolidatior1 by subjecting to heat ancl pressure referred to hereinbefore involve plastlc deEormation of tlle 0 rnatrix to remove porosity and achieve a similar result.
EXAMPLI~' I
Mearly spherical (0.4 to 0.7 mm in diameter) cementecl tun~sten carbide particles were used in the wenr-resistarlt composite material~s.
The cornposition o~ the cemented cnrbide particles were 907O by weight of WC and 10% by welght of cobalt. ~n atomized low alloy s~eel powder known by the trademark "Ancorsteel 2000" was used to form the steel matrlx.
Graphite was added to the steel powder to give a steel matrix containing 0.5% by weight of carbon.
Various amounts o~ cernented carbide particles and steel powders were wet miY~ed with water and alcoh()l. The volr1me proportion of cemented carbide particles was between 7 to 35%. A binder known by tlle trademark "Superloid" was added to the water to increase the strength o~ future green compacts. Preforms were then molded fro1n these mixtures. Afl:er drying at about 80C the preEorms were cornpacted at 55() ~l'a to a rlel-)s;ty of abol1t 80% of thr theoretical lens~ty.
The green compacts were sinterecl and Ln~iltratecl at ll2()C
durtng 1800 seconds wlth a copper alloy contair1lng 1% by wt. o~ cl)romJum.
'Che lnfiltrated pieces were subsequently oil quenclled and tllen tempere(l at 5U0C ~or 3600 seconds. A typical microgr.1pl1 oi the cermet coltalning 3~ wear-resistant material obtained by tllis metho(l is ShOWII ln F'Lgllre 2.
Abrasive wear mensuren)ents were made by tl)e higl) stress A~.TM
B611/76 metllod. In this method a steel lisk turrls in an abrasive-wlLer oll~ture ~ile tlle tested spec:imen is pressed a~nLrlst it. Arl nbr-l-;ive~
water Eilm is pulled between the specimell and tlle steel disk c~usin~
abrasiorl of tlle specimen. In tlle plrsent work 30 mesl1 Ottawa si]Lca abrasive particles were used with the FoLlowlng water to grit ratLo:
3~7~
0.4 cm3 ~ /g of gri.t. Volurne 10sses and re1atlve llfe spa-ls n~ selected iron base alloys arld oE the cermet coll~aining wear-resistallt l~terlals are presented ln 'rable I.
TA~I~F. I
Volume 106ses and relatlve llfe sparls of selected iron b,~se alloys and oE tlle cermet cont.lLIlillg wear-resistal1t m;ltertals prodllced by sinterin~ an~l subseql1ellt Lnfiltration Vo.lume l.osses Rel.ative ~aterials ~cm3/10()() wllr.~cl l.ife Spr revolutLons~
ASTM A36 steel C.30 1*
Austeni.tic rnangallese steel 0.198 1.52 112.1% (wt.) Mrl]
High ~lromlum cast iron U.227 1.32 125-30% (wt,) Cr]
Cermet containing wear-resistant materla1 Volume proportion of cemented carbide particles (%) 7 O.In9 2.75 1~ ().068 4.41 22 0.0525 5.71.
o.n373 ~.04 0.0198 15.15 * A value of 1 was glven to the ASTM ~36 steel
BACKGROUND OF l'HE tNVENTION
This invention relates to wear-resistant composite materLa]s.
The wear resistance of materials normally increases with l1ard-ness but it is also strongly affected by their microstructural character-iatics, especially by the presence oE a second phase. It is known thatabrasion resistance of steels lncreases when they contain hard second phases like carbides. ~lowever, the abrasive wear of steels containlng a large proportion of carbides depends fitrongly on the cohesion of these carbidea with the matrix, as well as on tlle si~e, shape and brittleness of the carbides. The highest abrasion resistances are generally found in alloys havlng hard second phases coherently bonded to the matrix and not distributed as a brittle contim1ous network in it. Many works have been done to attain this objective using powder meT~allurgy techniques, especi-ally in the production of rnetallic articles containing a disperslon of hard particles which consist of intermetallic or ceramic (usually carhide particles). There are two drawbacks for this kind of material. First, these intermetallic or ceramic particles are brittle and can fracture under high stress abrasive condition~s, and secondly, they cannot be easily or properly bonded to the matrix. Under such condLtions, the hard phase tends to be dislodged, thus giving rise to acceLerated wear.
It has been proposed in United States Patent No. 3,790,353, to provide a wear resistant pad by uti1i~ing cemented metal carbide parti-cles in a metal matrix wherein the metal matrix is melted to form the wear pad. The above ment:Lolled patent specTLEies the pad thickrless Ln terms of partlcle size which places a slgn-LEicant restrictlon on tlle product geometry particularly witrl regard to product thickness. It wL1L
be apparent that wlth melting oTE the matrix the hLgher density cermet partLcles ~ill tend to settle, and therefore, thickness cannot be increased as desired unless a suEficiently hLgh proportion oE cerlTIet partLcLes are used in order that tlle partLcles contact one another all(l cannot aettle. Such high proportions of cermet parttc]es, namely greater than about 50% by volume, provide a rLaterlal with less toughness than obtninable with lower proportions. Also, tlle higll temperatures required Eor melting cause a reaction wLth the cermet produclllg a brittle carbide at the cermet-matrix interface, further reducing toughness.
V~
It has been found tllflt the limitation~s of prior n~tllods an he overcome, and specifically, that a wkle range o~ thiclcness, sllape or com-positions of tougll wear-resistant cl~mpo6ites call he rrovided by tlle use of cermet partlcles, a steel powder matrix, an-l consolidating hy sublect-lng to lleat in the solld state. Slncc? tlle n~trix Ls not melted in tbepresent lnventlon, the aforesaid .settllnr prohlem does not ~rise an(l the composltlon in terms of cermet particle si~e, p;trticle-to-matrix propor-tlon, can be chosen to provide tlle clcs~recl wenr- resistant prorertles nncl toughl1es~ characterlstics without tlle previous restrictlons of product thickness, etc.
In accordance with tlle prese!lt invention, a wear-resistallt com-posite ls provided wltll a composite comrrisillg cermet particles dispersed ln a iron-base matrix that i8 consolidsted in the so1lcl state.
The wear-resistant materia] of tlle ~resent invelltion is made by forming a mixture of cermet particles 3nd all iron-bAse n~3trlx powdc~r, and consolidating the mixture by subjecting to lleat at a temperature below the melting polnt of the matrix.
In accordance Witll one specific embodiment oE tl-e inveTItiorl, consolidation co~prises slntering tlle mlxture nlld in~iltratLng witll a metal having a relatlvely low melting point.
BP~IEF DESCI'IPTION ()F Tlll URAWINGS
Figure 1 is a micrograph fillOW~, tlle mi crostructure of an examrle of a com~osite made in accord;lllte with one elllbodiment of the invention.
Fig~re 2 is a baclcscatterecl e~ectroll micrograph sllowillg the microstructure of a wear-reslstant composite materlal mflde by the metllod describecl in Example l.
DESCRIPTION OF PRIFI.RPNiD E~ ()DI~IENTS
The prodnceion oE cermet particle~s as usecl in the preseot inventlon, iæ known. One metlloci involves agglooleratlng WC and ~etal binder powders (0.2 to lO ~m) and consoli(lating by vacuum sintering. Tlle 7~
most commonly used and preferred cermet is tun~sten carbide with cohalt as blnder. Nickel, or nickel or cobalt alloys, may also be used as hind-er. For the present invention, the preEerred size range of the cermet particles is 0.1 to 5 mm, and pre~eral)ly from 0.5 to 2 mm. Preferably the cermet particles are generally spllerical, since these are less susceptlble to breakap,e.
The matrix ~aterial ~y comprtse var~ou~q iron-ba~se powders and, preferably, carbon steel9 alloy steel ~r sta-lnless steel. The ma~rix materlal may be prepared by known techn~ques.
Productlon of the composite ll~volves mi~inK the cermet parti-cles with the steel ~tr~x powder. The cllolce of the ~Itrix and the pro-portions will depend on the particul~r propertles, such a~s wear-resist-ance and tougllness, desired. It appears that suitable compof,~tes can be provided with volume proportlons oF the cermet partlcles up to nbout 6()%, and preferably, in the range of 20 tn 40~.
The mixture is then consolid.~ted by subject~ng to heat at a temperature below the melting pOi[lt of the matrix. Prior to consolida-tion, the mixture may ~e compacted or mnlded to the desired shape. The mlsture may also be formed by slip~casting.
Consolidation involves, sintering and subsequent infiltrating, or simultaneous sintering and infiltrating, with metals such as copper, copper alloys or nickel alloys.
The micrograph of Figure 1 shows the resulting microstructure in a composite consolidated with sintering and infiltration. It can be seen that the ~C~Co cermet particles are distributed in a copper infil-trated steel matrix and that the particles are surrounded by a layer of steel. There is little or no copper film immediately around the cemented particles. The steel matrix deforms plastically during cold pressing and bonds to cermet particles preventing massive copper penetration to the surface of these particles. ~xamination of fracture surfaces oE green compacts has shown that a steel layer is present on the surface of ~36~7~
cemented particles. It was observed tllat the porosity in the composite -ieces before consolidation tends to concentrnte nround cemented c<qrbLde particles. Tbis local poroslty is detrimelltal to the collesion betwr-~>n tlle cermet particles and the ~ trix nn(l to the strengtl1 of ti~e non infil-trated sintered specimens. In SllCh nOn~ fi1trated SpeC:LlnerlS, Celllentedpartlcles are easily pulled out oi tl1e materi.ll whicl1 doe6 not occllr wlth material lnf1Ltrated in accord.lllce wlth the preser1t invention. Sim-ilarly the alternate n~thods of consolidatior1 by subjecting to heat ancl pressure referred to hereinbefore involve plastlc deEormation of tlle 0 rnatrix to remove porosity and achieve a similar result.
EXAMPLI~' I
Mearly spherical (0.4 to 0.7 mm in diameter) cementecl tun~sten carbide particles were used in the wenr-resistarlt composite material~s.
The cornposition o~ the cemented cnrbide particles were 907O by weight of WC and 10% by welght of cobalt. ~n atomized low alloy s~eel powder known by the trademark "Ancorsteel 2000" was used to form the steel matrlx.
Graphite was added to the steel powder to give a steel matrix containing 0.5% by weight of carbon.
Various amounts o~ cernented carbide particles and steel powders were wet miY~ed with water and alcoh()l. The volr1me proportion of cemented carbide particles was between 7 to 35%. A binder known by tlle trademark "Superloid" was added to the water to increase the strength o~ future green compacts. Preforms were then molded fro1n these mixtures. Afl:er drying at about 80C the preEorms were cornpacted at 55() ~l'a to a rlel-)s;ty of abol1t 80% of thr theoretical lens~ty.
The green compacts were sinterecl and Ln~iltratecl at ll2()C
durtng 1800 seconds wlth a copper alloy contair1lng 1% by wt. o~ cl)romJum.
'Che lnfiltrated pieces were subsequently oil quenclled and tllen tempere(l at 5U0C ~or 3600 seconds. A typical microgr.1pl1 oi the cermet coltalning 3~ wear-resistant material obtained by tllis metho(l is ShOWII ln F'Lgllre 2.
Abrasive wear mensuren)ents were made by tl)e higl) stress A~.TM
B611/76 metllod. In this method a steel lisk turrls in an abrasive-wlLer oll~ture ~ile tlle tested spec:imen is pressed a~nLrlst it. Arl nbr-l-;ive~
water Eilm is pulled between the specimell and tlle steel disk c~usin~
abrasiorl of tlle specimen. In tlle plrsent work 30 mesl1 Ottawa si]Lca abrasive particles were used with the FoLlowlng water to grit ratLo:
3~7~
0.4 cm3 ~ /g of gri.t. Volurne 10sses and re1atlve llfe spa-ls n~ selected iron base alloys arld oE the cermet coll~aining wear-resistallt l~terlals are presented ln 'rable I.
TA~I~F. I
Volume 106ses and relatlve llfe sparls of selected iron b,~se alloys and oE tlle cermet cont.lLIlillg wear-resistal1t m;ltertals prodllced by sinterin~ an~l subseql1ellt Lnfiltration Vo.lume l.osses Rel.ative ~aterials ~cm3/10()() wllr.~cl l.ife Spr revolutLons~
ASTM A36 steel C.30 1*
Austeni.tic rnangallese steel 0.198 1.52 112.1% (wt.) Mrl]
High ~lromlum cast iron U.227 1.32 125-30% (wt,) Cr]
Cermet containing wear-resistant materla1 Volume proportion of cemented carbide particles (%) 7 O.In9 2.75 1~ ().068 4.41 22 0.0525 5.71.
o.n373 ~.04 0.0198 15.15 * A value of 1 was glven to the ASTM ~36 steel
Claims (14)
1. A wear-resistant composite comprising cermet particles dispersed in an iron-base matrix, and an infiltrated metal material having a melting temperature less than that of said matrix, and wherein the volume proportion of the cermet particles is not greater than 60% and wherein the size range of the cermet particles is from 0.1 to 5 mm.
2. The composite of claim 1 wherein the size of the cermet particles is from 0.5 to 2 mm.
3. The composite of claim 1 wherein the cermet particles are generally spherical.
4. The composite of claim 1 wherein the proportions of cermet are from 20 to 40%.
5. The composite of claim 1 wherein the iron-base matrix comprises carbon steel, alloy steel or stainless steel.
6. The composite of claim 1 wherein the cermet particles comprise tungsten carbide cemented together with cobalt or nickel.
7. A method of making a wear-resistant composite comprising forming a mixture of cermet particles in an iron-base matrix, consolidating the mixture by subjecting to heat at a temperature below the melting point of the matrix and infiltrating by a metal or alloy having a melting temperature less than the melting temperature of the matrix metal.
8. The method of claim 7 wherein the mixture is compacted prior to consolidation.
CLAIMS (Cont)
CLAIMS (Cont)
9. The method of claim 7 wherein the volume proportion of the cermet particles is less than about 60%.
10. The method of claim 7 wherein the volume proportion of the cermet particles is from 20 to 40%.
11. The method of claim 7 wherein the cermet particles comprise tungsten particles cemented with cobalt or nickel.
12. The method of claim 7 wherein the size of the cermet particles is from 0.1 to 5 mm.
13. The method of claim 7 wherein the size of the cermet particles is from 0.5 to 2 mm.
14. The method of claim 7 wherein the cermet particles are generally spherical.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA000455213A CA1236709A (en) | 1984-05-25 | 1984-05-25 | Wear resistant material and method for making |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA000455213A CA1236709A (en) | 1984-05-25 | 1984-05-25 | Wear resistant material and method for making |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1236709A true CA1236709A (en) | 1988-05-17 |
Family
ID=4127943
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000455213A Expired CA1236709A (en) | 1984-05-25 | 1984-05-25 | Wear resistant material and method for making |
Country Status (1)
| Country | Link |
|---|---|
| CA (1) | CA1236709A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0348804A2 (en) * | 1988-06-27 | 1990-01-03 | Deere & Company | Wear-resistant component and process for preparing it |
| US4954058A (en) * | 1988-06-27 | 1990-09-04 | Deere & Company | Method for making composite sintered apex seal material |
-
1984
- 1984-05-25 CA CA000455213A patent/CA1236709A/en not_active Expired
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0348804A2 (en) * | 1988-06-27 | 1990-01-03 | Deere & Company | Wear-resistant component and process for preparing it |
| EP0348804A3 (en) * | 1988-06-27 | 1990-03-28 | Deere & Company | Wear-resistant component and process for preparing it |
| US4954058A (en) * | 1988-06-27 | 1990-09-04 | Deere & Company | Method for making composite sintered apex seal material |
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