ContentslistsavailableatScienceDirect
Journal
of
Asian
Ceramic
Societies
jo u r n al h om ep a g e :w w w . e l s e v i e r . c o m / l o c at e / j a s c e r
Influence
of
ceramic
particulate
type
on
microstructure
and
tensile
strength
of
aluminum
matrix
composites
produced
using
friction
stir
processing
I.
Dinaharan
∗DepartmentofMechanicalEngineeringScience,UniversityofJohannesburg,AucklandParkKingswayCampus,Johannesburg2006,SouthAfrica
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c
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f
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Articlehistory:
Received8February2016
Receivedinrevisedform28March2016 Accepted13April2016
Availableonline29April2016 Keywords:
Aluminummatrixcomposites Frictionstirprocessing Microstructure Tensilestrength
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Frictionstirprocessing(FSP)wasappliedtoproducealuminummatrixcomposites(AMCs).Aluminum alloyAA6082wasusedasthematrixmaterial.Variousceramicparticles,suchasSiC,Al2O3,TiC,B4Cand
WC,wereusedasreinforcementparticle.AA6082AMCswereproducedusingasetofoptimizedprocess parameters.Themicrostructurewasstudiedusingopticalmicroscopy,filedemissionscanningelectron microscopyandelectronbackscattereddiagram.Theresultsindicatedthatthetypeofceramicparticledid notconsiderablyvarythemicrostructureandultimatetensilestrength(UTS).Eachtypeofceramicparticle providedahomogeneousdispersioninthestirzoneirrespectiveofthelocationandgoodinterfacial bonding.Nevertheless,AA6082/TiCAMCexhibitedsuperiorhardnessandwearresistancecompared tootherAMCsproducedinthisworkunderthesamesetofexperimentalconditions.Thestrengthening mechanismsandthevariationinthepropertiesarecorrelatedtotheobservedmicrostructure.Thedetails offracturemodearefurtherpresented.
©2016TheCeramicSocietyofJapanandtheKoreanCeramicSociety.Productionandhostingby ElsevierB.V.ThisisanopenaccessarticleundertheCCBY-NC-NDlicense(http://creativecommons.org/ licenses/by-nc-nd/4.0/).
1. Introduction
Reinforcingaluminumalloyswithceramicparticlescreateshigh elasticmodulus,stiffnessandwearresistance.Theresultant mate-rialisuniversallycalledasaluminummatrixcomposites(AMCs). The research on AMCs is intensified due to the great interest of theautomobile, aerospace and defense industries toreplace conventionalaluminumalloys inseveralapplications[1–3].The performanceandpropertiesoftheAMCsdependonseveralaspects, whicharenotlimitedtouniformdistributionofreinforcing par-ticles,interfacialbondingbetweenthealuminummatrixandthe reinforcingparticlesandintegrityofthereinforcingparticle dur-ingtheproductionprocess [4].Therefore,it isanuphilltaskto producesoundAMCsshowcasinguniformdistributionandgood interfacialbondingwithoutdecomposingofreinforcingparticles. Hitherto,powdermetallurgyandstircastingwerepredominantly usedtoproduceAMCs.But,thecommondefects,suchasporosity,
∗ Tel.:+27797018997.
E-mailaddress:[email protected]
PeerreviewunderresponsibilityofTheCeramicSocietyofJapanandtheKorean CeramicSociety.
clusteringandsegregationofparticlesandinterfacialreactions,are alwaysencountered[5–9].
Frictionstirprocessing(FSP)hasemergedasapotential solid-statetechniquetoproducesoundAMCs.Itisfacileandeconomic toprepareAMCsusingFSP.Theceramicparticlesarecompacted initiallyalongtheFSPdirectionusinggroovesofvariousshapes. Asquaregrooveispreferredtocompactparticles.Theopenendof thegrooveisclosedbytraversingapinlesstoolpriortoFSPtoavoid thelossofceramicparticlesduringprocessing.Thefrictionalheat generatedbytherotatingshoulderandthepinhelpstoplasticize thealuminumalloy.Thetransversemovementofthetoolresultsin thetransportationofplasticizedmaterialfromtheadvancingside totheretreadingside.Subsequently,thegrooveportioncollapses andthestirringactionof thetool dispersesthepackedceramic particlesintotheplasticizedaluminumalloy.TheAMCsarethus formedandforgedatthebackofthetoolduetotheappliedaxial force.FSPisa lowenergyconsumptionprocess.Theentire pro-cessisaccomplishedinsolidstatewithoutmeltingofaluminum. Hence,thechancesofinterfacialreactionanddecompositionare remote.Neitherthedensitygradientbetweentheceramicparticle andthealuminumalloynortheparticlesizeinfluencestheultimate distributionofparticles[10–13].
AMCsreinforcedwithvarietiesofceramicparticlesproduced using FSP were reported in literatures [14–22]. Shahraki et al. http://dx.doi.org/10.1016/j.jascer.2016.04.002
2187-0764©2016TheCeramicSocietyofJapanandtheKoreanCeramicSociety.ProductionandhostingbyElsevierB.V.ThisisanopenaccessarticleundertheCCBY-NC-ND license(http://creativecommons.org/licenses/by-nc-nd/4.0/).
Table1
ChemicalcompositionofAA6082aluminumalloy.
Element Mg Si Fe Mn Cu Cr Zn Ti Aluminum
wt.% 0.78 1.06 0.21 0.55 0.09 0.03 0.06 0.01 Balance
[14]developedAA5083/ZrO2AMCsandevaluatedthe
microstruc-tureandtensilebehavior.MoghaddasandBozorg[15]produced AA5754/Si3N4AMCsandcorrelatedthethermalprofileswiththe
evolutionofmicrostructure.Youetal.[16]preparedAl/SiO2AMCs
andanalysedtheinsituformationofAl2O3particles.Bahramietal.
[17]fabricatedAA7075/SiC AMCsand analyzed therole oftool pingeometryonmicrostructureandmechanicalproperties. Maza-herietal.[18]synthesizedA356/Al2O3AMCsandinvestigatedthe
microstructureandtribologicalbehavior.Khodabakhshietal.[19] createdAA5052/TiO2 AMCsand studiedtheeffect of annealing
onthesoild-statechemicalreactions.Thangarasuetal.[20] pro-ducedAA6082/TiCAMCsandexaminedtheeffectofTiCcontent onmicrostructureandtensilestrength.Zhaoetal.[21]prepared AA6061/B4CAMCsandstudiedtheeffectofnumberofpasseson
thedistributionofB4Cparticles.HashemiandHussain[22]formed
AA7075/TiNAMCsandestimatedtheinfluenceoftooldesignon dryslidingwearbehavior.
It is inferred from the short literature survey that FSP has beensuccessfullyappliedtoproduceAMCsreinforcedwith vari-ousceramicparticulates,includingSiC,Al2O3,B4C,TiC,ZrO2,Si3N4,
SiO2,TiO2 andTiN.However,variousceramicparticleswerenot
comparedinanysingleresearchwork,whichwouldassisttoassess theperformanceofseveralpotentialreinforcementsunderasetof identicalexperimentalconditions.Therefore,theobjectiveofthis researchworkistoproduceAMCsreinforcedwithSiC,Al2O3,TiC,
B4CandWCandevaluatetheeffectofvariousreinforcementson
themicrostructureandtensilebehavior.
2. Experimentalprocedure
Aluminum alloy AA6082 plates of size 100mm×50mm× 10mmwereusedforthisresearchwork.Thechemicalcomposition ofAA6082aluminumalloyisfurnishedinTable1.Agrooveof5mm deepand1.2widthwasmachinedalongthecenterlineoftheplates
usingwirecutElectricalDischargeMachining(EDM).Thevolume fractionofceramicparticlewas18%.TheSEMmicrographsof as-receivedceramicparticlesareshowninFig.1.Apinlesstoolwas initiallyemployedtocoverthetopofthegrooveafterfillingwith ceramicparticlestopreventtheparticlesfromscatteringduring FSP.TheFSPwascarriedoutonanindigenouslybuiltFSWmachine. Thetoolhadashoulderdiameterof18mm,pindiameterof5mm, pinlengthof5.5mmandathreadedpinprofile.Thetoolmaterial washighcarbonhighchromiumsteel(HCHCr),whichwasoil hard-enedtoobtainahardnessof60–62HRC.Theprocessparameters employedweretoolrotationalspeedof1600rpm,travelspeedof 60mm/minandaxialforceof10kN.Theparameterswereselected basedontrialexperimentsandpreviousworksdonebytheauthor. Fivesuchplates werefrictionstirprocessedbyvaryingceramic particles,suchasSiC(∼8m),Al2O3 (∼1m),TiC(∼2m),B4C
(∼4m)andWC(∼5m).AdetailedFSPproceduretoproducethe compositeispresentedelsewhere[23].
Specimenswereobtainedfromthecenterof thefrictionstir processedplatesandwerepolishedasperstandardmetallographic procedure. The polished specimens were etched with Keller’s reagent.Themicrostructurewasobservedusinganoptical micro-scope(OLYMPUS-BX51M) at various locations in the stir zone. Theceramicparticledistributionwasfurtherviewedusingafield
emissionscanningelectronmicroscope(FESEM,CARLZEISS-SIGMA HV)andelectronbackscatterdiffraction(EBSD).Anacceleration voltageof 15kV wasselectedfor FESEM.EBSD wascarriedout ina FEIQuantaFEG SEMequippedwithTSL-OIMsoftware.The mean grainsize was measured according to ASTM E1382−97. Themicrohardness wasmeasuredusing amicrohardnesstester (MITUTOYO-MVK-H1) at 500g loadapplied for 15s at various locations in the surface composite. Mini tensile specimens of gauge length21mm and diameter4mm wereprepared asper ASTMB557M-10standardfromtheFSPzone.Theultimatetensile strength(UTS)wasestimatedusingacomputerizedtensiletester. ThefracturesurfaceswereviewedusingSEM.
3. Resultsanddiscussion
3.1. MicrostructureofAA6082AMCs
Fig.2showsrepresentativeSEMmicrographsofAA6082AMCs reinforcedwithvariousceramicparticles,whichclearlyrevealthe dispersionofceramicparticlesinthealuminummatrix.The dis-persionofceramicparticlesisobservedtobefairlyhomogeneous. Therearenoclustersoragglomerationofparticlesseen.Moreover, there is nosegregationof particlesalong thegrainboundaries.
Fig.3. FESEMmicrographAA6082AMCsreinforcedwith(a)SiC,(b)Al2O3,(c)TiC,(d)B4Cand(e)WCathighermagnification.
Someparticlesmightbelocatedonthegrainboundariesdueto smallergrainsize.Butentrapmentofparticleswithingrain bound-ariesisabsent.Hence,thedispersionisconsideredtoberoughly intragranular.ThemechanicalandtribologicalpropertiesofAMCs areinfluencedbythenatureofdispersion.Ahomogeneousand intragranulardispersionisessentialtoattainhigherproperties.The FSPprocesshasresultedinthedesirabledispersion.Stircasting techniquefrequentlyproducesinhomogeneousandintergranular dispersionowingtosolidificationrelatedphenomena.Thedensity gradientresultsinimproperdispersion[8].Sincethealuminum matrixdoesnotmeltduringFSP,densitygradientdoesnotcause freemovementofceramicparticles.Thisleadstoproperdispersion. Thedispersionofceramicparticlesisafunctionofprocess parame-ters,suchastoolrotationalspeedandtraversespeed[12,13,15,24]. AfineandhomogeneousdispersionintheSEMmicrographs con-firm that the chosen set of process parameters is sufficient to producethedesirabledispersion.Thecompactedceramicparticles aredispersedthroughoutthestirzone.
FSPinducedachangeinthesizeandmorphologyofceramic par-ticles,Figs.1and2.Thesevereplasticdeformationtogetherwith therotatingactionofthetoolisabletosmashtheceramicparticles. Thestrongstirringactionofthetoolknocksoffthesharpcorners oftheceramicparticle. Largesizevariationof ceramicparticles
(SiC,TiC,B4CandWC)inFig.2indicatesthefragmentation.Similar
observationswerereportedbyotherresearchers[13,25].Therate offragmentationdependsupontheinitialsizeandshapeofthe par-ticles.Largesizeparticlesandirregularorpolygonalshapeparticles havethetendencytobreakoffduringFSP.Theretentionofshape andsizeofAl2O3particlesinFig.2afterFSP,whichdidnotundergo
muchfragmentation,confirmsthisstatement.ItisobservedinFig.2 thatthelargeceramicparticlesarenotsurroundedbydebris gen-eratedduetofragmentation.Thereisnoclusteringofsmalldebris either.Thissuggeststhatthedebrisalsomixedwellwiththe plasti-cizedaluminumanddispersedhomogeneouslyintheAMC.Thesize ofdebrisisremarkablylowintheorderofnanometercomparedto thesizeofinitiallypackedceramicparticles.Thesizevariationleads tofunctionallygradedlocalareaswithintheAMC.
Fig.3presentstheSEMmicrographsofAA6082AMCsreinforced withvariousceramicparticlesathighermagnification.The inter-facebetween thealuminum matrix and theceramic particleis detailedinthisfigure.Theinterfaceisclearwithoutthepresence ofporesorreactionproducts.Eachtypeofceramicparticleappears tobebondedwellwiththealuminummatrix.Someinvestigators observedporesaroundceramicparticlesinAMCSproducedusing FSP[12,13].Nosuchporesareobservednearanyceramic parti-cleinFig.3.Thiscanbeattributedtoadequatematerialflowand
Fig.4. OpticalphotomicrographofAA6082/SiCAMCsobservedatvariouslocationswithinthestirzone;(a)nearadvancingside,(b)nearretreadingside;(c)centerand(d) bottom.
plasticizationofaluminumunderthechosenexperimental condi-tions.Theinterfaceplaysacrucialroleintensileloadingtotransfer theloadeffectivelytotheceramicparticle.Goodinterfacialbonding isaprerequisiteinspiteofhomogeneousdispersiontoimprovethe properties.Thetemperatureoftheprocessingmethodinfluences theinterfacialstrengthsignificantly.Higherprocessing tempera-turetendstoinitiateinterfacialreactionsbetweenthealuminum matrixandtheceramicparticle.Thereactionproductsusually sur-roundtheceramicparticleandweakentheinterfacialstrength[8]. Absenceofreactionproductsindicatesthatthetemperaturerise duringFSPisinsufficienttoinitiateanyinterfacialreaction.
Figs.4–8presentstheopticalmicrographsofAA6082AMCs rein-forcedwithvariousceramicparticlescapturedatdifferentlocations withinthestirzone.Theopticalmicrographsshowthedispersion ofceramicparticlesalloverthestirzone.Noareainthestirzoneis leftwithoutparticles.Itissignificanttoobservethatthedispersion oftheceramicparticleisindependentofthelocationinthestir zone.Thechangeinthedispersionoftheceramicparticlesfrom theadvancingsidetotheretreadingsideorfromthetopsidetothe bottomsideisnegligible.However,someresearchersfound signif-icantvariationinthedistributionofceramicparticleswithinthe stirzoneofAMCsproducedbyFSP[14,26,27].
Theabsenceofsignificantvariationindispersioncanbeascribed toadequateplasticizationofaluminummatrixandoptimizedtool rotationalspeed,whichmakeseasytodispersetheceramic parti-clestoallregionsofthestirzone.
ItcanbeseenfromFigs.4–8thatthetypeofceramic parti-cledoesnotplayamajorroletodirectthenatureofdispersionin thecomposite.Alltheceramicparticlesconsideredinthisresearch workmixedwellwiththeplasticizedaluminumandproducedthe composite.ThiscanbeattributedtothenatureoftheFSP pro-cess,whichproducesthecompositeinsolidstatewithoutmelting thealuminumalloy.Neitherthedensity gradientnorthe wett-abilitybetweenthetype of ceramicparticleand thealuminum causesinhomogeneousmicrostructure.Singlaetal.[28]produced AA6061/SiCandAA6061/Al2O3AMCsusingstircastingandfound
Table2
PropertiesofAA6082aluminummatrixcomposites.
Material Grainsize(m) Microhardness(VHN) UTS(MPa)
AA6082 39.4 62 254 AA6082/SiCAMC 6.2 102 286 AA6082/Al2O3AMC 4.8 106 297 AA6082/TiCAMC 5.2 120 326 AA6082/B4CAMC 5.3 115 315 AA6082/WCCMC 6.1 98 283
thatthedispersionofSiCparticleswasnotsimilartothedispersion of Al2O3 particles.The dispersionofSiCparticles was
homoge-nouswhilesevereagglomerationsofAl2O3particleswereobserved.
Mazaherietal.[7]developedAl/TiCandAl/B4CAMCsusingstir
cast-ingandobservedthatthedensitygradientbetweenthealuminum and theceramicparticleplayed a crucialrole in thedispersion ofparticles.Theyconcludedthatitisdifficulttoobtaindesirable dispersionofvariousceramicparticlesusingsamesetofprocess parameters.Therefore,itisdifficulttoproduceAMCsreinforced withvariousceramicparticlesbyapplyingstircastingtechnique undera setofsimilarprocessparameters. Thedensitygradient movestheceramicparticleeithertofloatorsinkwhilepoor wett-abilitycausestherejectionofparticlesfromthealuminummelt. FSPprocessissuitableandcapableofproducingAMCsreinforced withvariousceramicparticles.
The EBSD images of AA6082 AMCs reinforced with various ceramicparticlesandthealuminummatrixaredepictedinFig.9 andthequantitativevaluesofgrainsizearefurnishedinTable2. Thealuminummatrixshowselongatedgrainsduetotherolling process.AlltheAA6082AMCsexhibitfineandequiaxedgrains. Thegenerationoffinegrainstructurecanbeexplainedusingthe followingfactors.FSPresultsindynamicrecrystallizationdueto intenseplasticdeformationsincealuminumisahighstackingfault energymaterial. Arearrangementofdislocationsinto sub-grain boundaries by dynamic recovery takes place [29]. The severe plastic strain ratecausesgrainrefinement. Thedriving forceis
Fig.5. OpticalphotomicrographofAA6082/Al2O3AMCsobservedatvariouslocationswithinthestirzone;(a)nearadvancingside,(b)nearretreadingside;(c)centerand
(d)bottom.
Fig.6.OpticalphotomicrographofAA6082/TiCAMCsobservedatvariouslocationswithinthestirzone;(a)nearadvancingside,(b)nearretreadingside;(c)centerand(d) bottom.
theincreaseddislocationdensitythatresultedfromtheapplied strain,which hinders graingrowth [30].Asa result, morenew grainsnucleateatthemovingboundaries.Secondly,theceramic particles have a tendency to pin the movement of the grain boundaries and hold up the grain growth caused by dynamic
recrystallization. A growing grainboundary encounters several obstaclesinitsmovementduetohomogeneousdispersionof rein-forcementparticles.Thirdly,thevariationindeformationofhard reinforcementparticlesandsoftaluminummatrixduringplastic deformationassiststofragmentthegrains.Thiscreatesfinergrains.
Fig.7. OpticalphotomicrographofAA6082/B4CAMCsobservedatvariouslocationswithinthestirzone;(a)nearadvancingside,(b)nearretreadingside;(c)centerand(d)
bottom.
Fig.8. OpticalphotomicrographofAA6082/WCAMCsobservedatvariouslocationswithinthestirzone;(a)nearadvancingside,(b)nearretreadingside;(c)centerand(d) bottom.
ThevariationingrainsizeamongthevariousAA6082AMCsis insignificant.Thisleadstoaconclusionthatthetypeofceramic particleisnotcrucialforgrainrefinement.Alltheceramic parti-clescontributedtograinrefinementbyoneortwomechanismsas discussedabove.
3.2. MicrohardnessandtensilestrengthofAA6082AMCs
ThemicrohardnessandUTSofAA6082AMCsreinforcedwith various ceramic particles are given in Table2. The microhard-ness andUTS ofas-receivedAA6082 were62HVand 254MPa,
Fig.9.EBSD(IPF+grainboundary)mapofAA6082AMCsreinforcedwith(a)noparticle(i.e.AA6082),(b)SiC,(c)Al2O3,(d)TiC,(e)B4Cand(f)WC.
respectively. The incorporation of various ceramic particles improvedthemirohardnessandUTS.AA6082/TiCAMCexhibited highermicrohardnessandUTSundertheexperimentalconditions appliedin this researchwork. The various AMCs are strength-enedbythedifferentceramicparticles.Themechanicalproperties suchasmicrohardnessandUTSimprovedowingtothechanges thattookplaceinthemicrostructure.Thepossiblestrengthening mechanismsareelaboratedasfollows.Thehardnessof ceramic particles is very high tothat of aluminum matrix. The disper-sionofceramicparticlesasahardphaseinthealuminummatrix
results in strengthening. According to Hall–Petch relationship, the grain size influences the mechanical properties of metal-lic materials.Thegrainsizeof AA6082AMCsis smallertothat of the AA6082 aluminum matrix due to grain refinement.The finegrains help toimprove themechanical properties. Thirdly, the variation in thermal contraction between the aluminum matrix and the ceramic particles produces quench hardening effect.Further,the homogenousdispersion ofceramic particles all over the aluminum matrix provides Orowan strengthening [31].
Fig.10.FractographsofAA6082AMCsreinforcedwith(a)noparticle(i.e.AA6082),(b)SiC,(c)Al2O3,(d)TiC,(e)B4Cand(f)WC.
ThehardnessofSiC,Al2O3,TiC,B4C andWCarerespectively
2480HK,2100HK,2470HK,2750HKand1880HK.Nevertheless, AA6082/TiCAMCshowedhighermirohardnessandUTS.The vari-ationsinmicrohardnessandUTSarerespectivelywithin19%and 13%.Thereareseveralfactorsthatgovernthemechanical prop-ertiesofAMCs includingsize, shape,volumefraction, natureof distributionofceramicparticles[32,33].Alltypesofceramic parti-clesdisplayedhomogeneousdispersioninthealuminummatrixfor aselectedconstantvolumefraction.Therearenoclustersor porosi-tiespresentinconsiderablequantity.Al2O3 particleissmallerin
sizecomparedtootherceramicparticlesstudiedinthiswork.But, thehardnessofAl2O3islowertothatofTiC.ThehardnessofB4Cis
highercomparedtoallotherceramicparticles.However,B4C
parti-clesdisplay(Fig.2dand3d)sharpedgesintheAMCwhichmayact asstressraiserduringtensileloading.SiCparticlesarebiggerinsize andhavingsharpedges.Thefinesizeandsphericalmorphologyof theTiCparticlescouldbethepossiblereasonforhighermechanical propertiesofAA6082/TiCAMC.
ThefracturesurfacesofAA6082AMCsreinforcedwithvarious ceramicparticlesandthealuminummatrixarepresentedinFig.10. Thefracturesurfaceofthealuminummatrixiscoveredwitha uni-formdispersionof largesizevoid.It indicated largeamountof materialflowbeforefailure.Thefracturemodeobservedisductile.
ThefracturesurfaceoftheAA6082AMCsrevealsabimodal dis-persionoflargeandsmallsizeofdimples.Thisisatypicalfracture surfaceofAMCs,whichhavewell-bondedreinforcementparticles. Largedimplesareformedwhereverceramicparticlesarepresent. Smalldimples arise dueto theductile failureof thealuminum matrix.Thebimodaldispersionofdimplesindicatesthatthefailure isbrittlemacroscopically andductile microscopically.The pres-enceofceramicparticlesrestrictstheflowof aluminummatrix duringtensileloading.Fracturesurfacesconfirmthattheapplied loadwaseffectivelytransferredtotheceramicparticlesduetogood interfacialbonding.
4. Conclusion
AA6082/X(X=SiC,Al2O3,TiC,B4Cand WC)AMCswere
suc-cessfullyproducedusingFSP.Themicrostructure,microhardness andtensilestrengthwereevaluated.Thefollowingconclusionsare derivedfromthepresentwork.
• Thevariationingrainsize,microhardnessandUTSwaswithin ashortrange.Nevertheless,AA6082/TiCAMCdisplayedbetter hardnessandUTScomparedtootherAMCsproducedinthiswork underthesamesetofexperimentalconditions.
• ThedispersionoftheceramicparticlesintheAA6082AMCswas independentofthelocationwithinthestirzone.Thedispersion washomogeneousandunaffectedbythetypeofceramicparticle used.
• SiC,TiC,B4CandWCparticlesencounteredfragmentationduring
FSPduetosevereplasticdeformationandinteractionwiththe rotatingtool.Thefragmenteddebrisalsomixedwellwiththe plasticizedaluminumanddispersedhomogeneouslyintheAMC. Al2O3particledidnotsufferfragmentationduetoitssmallersize.
• Therewasnointerfacialreactionbetweenaluminum andany type of ceramic particle and good interfacial bonding was observed.
• AlltypesofceramicparticlesenhancedtheUTSofaluminumalloy AA6082andinfluenced thefracturemode. Thefracturemode shiftedfromductiletobrittle.
• FSPisasuitableprocessingmethodtoproduceAMCsreinforced withvariouskindsofceramicparticleswithacceptable proper-ties.
Acknowledgements
TheauthorisgratefultoWeldingResearchCellatCoimbatore InstituteofTechnology,OIM andTextureLabatIndianInstitute ofTechnologyBombayandMetmech EngineersResearchLabat Chennaiforprovidingthefacilitiestocarryoutthisinvestigation.
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