*e-mail:freirej@ufrnet.br,eve@dem.ufrn.br
FatigueDamageMechanismandFailurePreventionin
FiberglassReinforcedPlastic
RaimundoCarlosSilverioFreireJr.a*,EveMariaFreiredeAquinob*
a
CCET,PDCEM,UniversidadeFederaldoRioGrandedo�orte
CampusUniversitário,Lagoa�ova,59072-970�atal-R�
b
DEM,PPGEM,UniverdadeFederaldoRioGarndedo�orte,CentrodeTecnologia
CampusUniversitário,Lagoa�ova,59072-970�atal-R�
Receveid:September3,2004;Revised:January17,2005
Damagingofcompositelaminateswasmonitoredduringfatiguetests,revealingtheformationandpropagation stages for compressive, tensile, or alternate cyclic loading.Two different laminate stacking sequences, with differentnumberoflayers,weretested.ThelaminatesconsistedofE-glassfibersreinforcedorthoftalicpolyester resin(FGRP)shapedasmatsor(bi-direction)wovenfabrictextile.Preliminarydensity,calcinationtestsand staticcompressiveandtensilemechanicaltestswerecarriedout.Then,tensile(R=0.1),compressive(R=10) andalternateaxial(R=-1)fatiguetestswereperformedatdifferentmaximumstresses.Tensilecyclicloading resultedincrackformationandpropagationconfirmingthefindingsreportedinotherstudies.Ontheotherhand, damagefromalternateandcompressivefatiguedepictedpeculiarfeatures.Lessextendeddamageandbetter fatigueresistancewereobservedforthelaminatewithsymmetricallydistributedlayers.
Keywords:fatigue,laminates,FRPcomposites,damageformationandpropagationdiagrams
1.Introduction
Compositelaminatesinservicearesubmittedtoloading,includ-ingcyclicloading,whichleadstotheformationofinternaldamages, suchasmatrixfissures,fiberrupture,delaminationandmicrobuck-ling1-2.Severalstudies3-7haveaddressedtherelationshipsbetween
damageformationandpropagationandtheirnegativeeffectonthe mechanicalperformanceoflaminates,whichreducestheusefullife ofthematerial.Reifsnider3proposedadiagramwhichdemonstrates
the stages of formation and propagation of damage upon fatigue. Transversalcracksareformedinthelaminate.Theirnumberincreases withthenumberofcyclesuptoasaturationlimitcorrespondingto acertainnumberofcycles.Reifsnidernamedthissaturationlimit
CDS(characteristicdamagestate).Delaminationthentakesplaceand extendsleadingtofulllossofmechanicalstrength.Thecomposite thenfailsbyfiberrupture.
Gamstedt8 also developed a model for damage formation and
propagation in laminates with transversally oriented fibers with respect to the load direction. In that study, the interface between transversalfibersandmatrixwasconsideredastheregionwithhigh-estsusceptibilitytodamageformation.Inaddition,theformationof suchdamageswouldbedifferentincompressionandtension.Finally, alternateloadingwouldsignificantlydecreasethelifeofthelaminate asaresultofthecombinedeffectoffiberandmatrixdebondingunder tensileandcompressiveloads,thusincreasingthenumberofcracks and,consequently,decreasingitsstrength.
Thepresentstudyinvestigatesthedamageformationandpropaga-tionduringfatiguetestsoftwocompositelaminateswithsymmetric andasymmetricdistributionofE-glassfiberlayersinanorthoftalic polyester matrix. Both short fiber mats and bi-direction) woven fabrictextilewereevaluated.Uniaxialfatiguetestswerecarriedout forR=-1,R=0.1andR=10.Differentmaximumappliedstresses (Risdefinedasstressratio,i.e.,theratiobetweenminimumand maximumstress)werealsoevaluated.Eachspecimenwastestedat constantstressamplitudeandhigh-cyclefatigue,above103cycles.
Uniaxialtensileandcompressiontestswerealsocarriedoutinorder todeterminetheultimatestrengthofthelaminates.
2.ExperimentalProcedure
Thecompositematerialsusedhereinweremanuallylaminated into 1m2plates. Unsaturated orthoftalic polyester resin was
rein-forcedwithbothE-glassmats(5cm,450g/m2)and(bi-direction)
wovenfabrictextile(450g/m2).Twoplateswerethenmanufactured
containing10or12layers(7and10mmthick,respectively)having thefollowingstackingsequences:
[M/T/M/T/M]S
Stackingsequencesoflaminatewith10layers(C10)
[M/T/M/T/M/M/T/M/T/M/T/M]
Stackingsequencesoflaminatewith12layers(C12)
whereMandTcorrespondtoE-fiberglassmatsand(bi-direction)wovenfabric textile,respectively,andsreferstothesymmetryofthelaminate.OnlytheC10 laminatewassymmetricwithrespecttothedistributionofitslayers.
Theabove-mentionedlaminatesareusedbytheindustryforthe manufacturingofreservoirsingeneral.Originallytheyarebuiltfol-lowingtheC10laminateconfigurationtype.However,inordertoget betterstaticpropertiesregardingbothstrengthandrigidityarounda wallsectionofthereservoir,twoextralayersarelaminatedandthe C12 configuration is obtained.This procedure leads to symmetry problemsinthatsectionwhilethelayersarebeingdistributed.Ac-cordingtotheresultsdemonstratedinthispaper,thispracticecauses fatiguestrengthlossesfortheC12laminatetype.
Theplatesweresectionedusingadiamonddisk(DIFERD252) topreventfiberpulloutoranyotherdamage.ASTMD3039provided theguidelinesforthegeometryandsizeofthesamplesusedinthe uniaxial tensile tests9, whereas uniaxial compressive and fatigue
samples(R=10,R=-1andR=0.1)werecutaccordingtoMandell10.
Allspecimenswererectangularandhadthefollowingdimensions: 200x25mmfortensileandfatiguetests,and100x 25mmforcom-pressivetests.Samplegaugewas127mmfortensileandfatiguetests withR=0.1;40mmforfatiguesampleswithR=-1,and35mmfor compressiontestswithR=10. UniaxialtensiletestswerecarriedoutinauniversalPAVITEST testingmachineandcompressivetestsinaMTS-810servo-hydraulic machine.Theverticalspeedoftheplungerwassetto1mm/minfor bothseriesoftests.Fivesampleswererupturedineachsetofstatic tests.Theresults,showninTable1,revealedthatdespitethe11% differenceintheircompressiveelasticmodulus,theultimatestresses andelasticmoduliofbothlaminateswerenearlyidentical,yielding similarresistancetostaticloads. FatiguetestswereperformedusingaMTSservo-hydraulictest-ingmachine.Thefrequencywassetto5Hzanddepictedsinusoidal variation.StressratioswereR=0.1,R=-1orR=10.Inorderto plotS-Ncurves,maximumtensilestresstestswereperformedat60% oftheultimatetensilestressvalueofthelaminate(forR=0.1and R=-1theultimatetensilestresswasemployedwhereasultimate compressivestresswasusedforR=10).Theseresultswereusedto selectthemaximumstressvaluesusedforallothertests.Thetests wereperformedtoassurethatthenumberofcyclestofailurewas between103and106,thuscharacterizinghighcyclefatigue.Three
specimensweretestedforeachvalueofmaximumstressselectedto-taling87specimens.Alltestswerecarriedoutatambienttemperature (25°C)and50%relativeairhumidity. Damageevolutionduringfatiguetestswasassessedbyestablish-ingboththenumberofcyclesnecessarytostopthepropagationof transversalcracks(damageestate)andthenumberofcyclesfordela-mination.AdigitalKodak–Dc215camera(1100x 900pixelsresolu-tion)wasalsousedtocapturetheimagesnecessarytoanalyzedamage formationandpropagationacrossthelaminate(freeedges).
3.Results
DamageanalysesoflaminatesC10andC12werecarriedoutfor eachstressratioused(R=0.1,R=-1eR=10),sincethemechanism ofdamageformationandpropagationdependedonthisparameter. DamageFormationandPropagationDiagrams(DFPD)werethen plottedandcanbeusedasatooltopreventcomponentfailureby establishingtheconditionsofdamageinitiationforeachmaterial.
3.1.DamageanalysisoffatiguetestswithR=0.1
DFPDsoflaminatesC10andC12testedwithR =0.1areillus-tratedinFigure1.Damageoccurredinthefollowingstages,which areingoodagreementwiththeresultsobtainedbyReifsnider3who
carriedoutdamageanalysesforunidirectionallaminates: 1)Formationoftransversalcracksalongtheentiresampleuseful area(freeedgeandwidth)uptothepointofsaturation; 2)Propagationofdelaminationformedbymergingtransversal cracks; 3)Fiberruptureandultimatesamplefracturedescribedbythe S-Ncurve.
DelaminationstartedsoonerforlaminateC12thanforlaminate
C10.Thiswasrelatedtothefactthat,forthesamemaximumapplied stress,cracksaturationwasobservedunder104cyclesforlaminate C12(Figure1b)andabovethatmarkforlaminateC10(Figure1a)for thesamemaximumappliedstress(σmax).Thesymmetricdistribution
oflayersallowedbetteraccommodationofinternalstresses11reducing
thenumberofpointsofstressconcentrationanddelayingtheforma-tionoftransversalcracks.Asaresult,laminateC10depictedhigher
fatigueresistance,whichdemonstratedtheimportanceofdetermin-Table1.MechanicalpropertiesoflaminatesC10andC12.
LaminateC10 LaminateC12
Ultimatetensilestrength (MPa) 116.7±7.0 115.3±7.7 Ultimate compressive strength(MPa) 171.3±10.0 181±7.1
Tensile elastic modulus (GPa)
4.81±0.61 4.5±0.17
Compressive elastic modulus(GPa)
4.27±0.28 4.79±0.33
Maximum tensile strain (%)
2.45±0.35 2.54±0.24
Maximum compressive strain(%)
4.07±0.41 3.92±0.34
103 104 105 106
60 65 70 75 80 Delaminationonset andpropag ation Transv ersal Cracks MaximumStress(MP a) NumberofCycles SaturationLine FinalFracture (S-NCurve)
103 104 105 106
ingthepointofsaturationfortransversalcracksonthediagnostic oftheusefullifeoflaminatecomposites.Inaddition,delamination initiatedintheinnerlayersoflaminateC10andintheouterlayersof laminateC12probablyasaconsequenceoflowerfatigueresistance ofthelatter.Eventually,ruptureoftheouterlayersoflaminateC12 tookplacebeforetheultimatefailureofthesample(Figure2),which wasnotobservedinlaminateC10.
3.2.DamageanalysisforfatiguetestswithR=-1
DFPDs of laminatesC10 andC12 tested withR = -1 are il-lustrated in Figure 3.The following sequence of events could be established:
1)Formationoftransversalcracks;
2)Delaminationstartingatfreeedgesandsubsequentpropagation alongthewidthofthesample;
3)Saturationoftransversalcracks;
4)Continuedformationandpropagationofdelamination; 5)Fiberruptureandultimatesamplefracture.
Delaminationprecededthesaturationoftransversalcracksand wasprobablyrelatedtothenatureoftheloadappliedtothelaminates. SinceR=-1,laminatesunderwentalternatetensile–compressive loadwhichprematurelyresultedindelamination.Thisrevealedthe importanceofthetypeofloadappliedduringfatiguetestsondamage formationandpropagationoflaminates.
Bothdelaminationonsetandsaturationoftransversalcrackstook placeafterfewercyclesforlaminateC12(500-104cycles,Figure3b)
comparedtolaminateC10(103-105cycles,Figure3a)foragiven
appliedmaximumstress,thusresultinginlowerfatigueresistanceof laminateC12.Thiswasprobablyrelatedtothesymmetryoflaminate
C10,whichnotonlydelayedthesaturationoftransversalcracksbut alsohindereddelamination,mainlyintheouterlayersofthelaminate. ThisisshowninFigure4,whichportraitsaseriesofimagessequen-tiallyrecordedaftervariousnumbersofcycles,N,duringfatiguetest oflaminateC10submittedtoσmax=69MPa.Thenumberofcycles
torupture,N0,was4400.Delaminationoccurredintheinnerregion oflaminateC10(Figure4)butrandomlyforlaminateC12(Figure5,
R=-1,σmax=46MPa,N0=17500cycles).
3.3.DamageanalysisforfatiguetestswithR=10
DFPDs of laminatesC10 andC12 forR = 10 are shown in
Figure6.Damageformationandpropagationtookplaceinthefol-lowingorder:
1)Delaminationstartedatthefreeedges.
2)Propagationofdelaminationalongthewidthofthesample. 3)Fiberrupturefollowedbyultimatefracture.
NotransversalcrackswereobservedforR=10ineitherlaminate asaconsequenceoftheessentiallycycliccompressiveloadapplied to the laminates. The absence of tensile stresses limited rupture to the final stages of the fracture process. Compared to laminate
C10, delamination started sooner for laminateC12, i.e., between 400and 10300 cycles for laminateC12 and between 2100 and 90000cyclesforlaminateC10forthesamemaximumappliedstress (99.6-132.8MPa).Asaresult,laminateC12depictedshorteruseful lifetime.Theformationandpropagationofdelaminationalongthe freeedgeoflaminateC12isshowninFigure7(σmax=99.6MPa,
N0=38700 cycles). Delamination occurred in most of its layers, which significantly reduced the useful lifetime of the composite. Conversely,delaminationwasrestrictedtotheinnerlayersoflaminate
C10(Figure8)undersimilarexperimentalconditions,resultingin
Ruptureof outerlayer
Figure2.LaminateC12(σmax=69MPa,R=0.1,N=18700cycles,number
ofcyclestorupture,N0=21200cycles). Figure3.DamageFormationandPropagationDiagrams(DFPD)forlaminate:a)C10;b)C12withR=-1. (a)
longerusefullifetime.ThedamagesequencesoflaminatesC10and
C12underthesamemaximumstress(σmax =132.8MPa)areillus-tratedinFigures8and9,respectively.Virtuallynosignofdamage could be observed in laminateC10 after 29% of the fatigue test, whereaslaminateC12revealedextensivedelaminationofmostof itslayersafter34%ofthetest.
4.Conclusions
• ForR =0.1bothlaminatesexperiencedfatiguedamageac-cording to: formation and saturation of transversal cracks, formationandpropagationofdelamination,fiberruptureand ultimatecompositefracture;
• ForR=-1theorderoftheeventsleadingtofractureofboth laminatesslightlychangedto:transversalcracking,formation and propagation of delamination, saturation of transversal cracks,continuedformationandpropagationofdelamination, fiberruptureandultimatecompositefracture;
• ForR=10fracturewasrestrictedtodelamination,fiberrupture andultimatecompositefracture;
0.99
0.28 �0
�� 0.44 0.570.86
Figure 5. Damage sequence for laminate C12 tested with R = -1 (N0=17500cycles,σmax=46MPa)(freeedgeregion).
103 104 105 106
100 110 120 130 140 150
DelaminationOnset FinalFracture(S-NCurve)
Delamination Onsetand Propagation
NoCracks
MaximumStress(MP
a)
NumberofCycles
103 104 105 106
90 100 110 120
130 DelaminationOnset
FinalFracture(S-NCurve)
Delamination Onsetand Propagation NoCracks
MaximumStress(MP
a)
NumberofCycles (a)
(b)
Figure6.DamageFormationandPropagationDiagrams(DFPD)forlaminate (a)C10and(b)C12withR=10.
01 . 0
�
�0
� 0.03 0.560.890.16
Figure 7. Damage sequence for laminate C12 tested with R = 10 (N0=38700cycles,σmax=99.6MPa).
0.04
�
�0
� 0.16 0.68
Delamination
�0.01 �0
�
0.290.570.94
Figure 8. Damage sequence for laminate C10 tested with R = 10 (N0=3500cycles,σmax=132.8MPa).
0.03 = �0
�
0.34 0.48
Figure 9. Damage sequence for laminate C12 tested with R = 10 (N0=1460cycles,σmax=132.8MPa).
• Thenumberofcyclesfordelaminationinitiation(forallvalues ofRinvestigated)isdirectlyrelatedtothefatigueresistance, andthereforeishelpfultoassestotheusefullifetimeofthe composite;
• LaminateC12revealeddelaminationofinnerandespecially outerlayerswhereasdelaminationofthesymmetriclaminate
C10wasrestrictedtoitsinnerlayers;
•DFPDsare tools to estimate failure prevention or damage formationasafunctionofthemaximumstressandnumberof cycles.
Acknowledgments
TheauthorswishtoacknowledgeCAPESforgrantingaM.Sc. schorlarship,theDepartmentofMechanicalEngineeringofUFPB CampusIIfortheuseoftheMTSmachineandCEFET–RNforthe useofthePAVITESTmachine.
References
1. YangB,KoseyV,AdanurS,KumarS.Bending,CompressionandShear BehaviorofWovenGlassFiber-EpoxyComposites.Composites–Part B:Engineering.2000;31:715-721.
2. Felipe RCTS.Comportamento Mecânico e Fratura de Moldados em PRFV.[DissertaçãodeMestrado].Natal:UniversidadeFederaldoRio GrandedoNorte;1997.
3. ReifsniderKL,HennekeEG,StinchcombWW,DukeJC.Mechanicsof CompositesMaterials,RecentAdvances.Ed.Pergamon,1983. 4. NationalInstituteofStandardsandTechnology[DirectorKammerRG].
AFatigueModelforFiber-ReinforcedPolymericCompositesforOffshore Applications.Blacksburg:TechnicalNote1434;2000.
5. TakedaN,KobayashiS,OgiharaS,KobayashiA.EffectsofToughened InterlaminarLayersonFatigueDamageProgressinQuasi-IsotropicCFRP Laminates.InternationalJournalofFatigue,1999;21:235-242. 6. OgiharaS,TakedaN,KobayashiS,KobayashiA.EffectsofStacking
SequenceonMicroscopicFatigueDamageDevelopmentinQuasi-Iso-tropicCFRPLaminateswithInterlaminar-toughenedLayers.Composites ScienceandTechnology.1999;59:1387-1398.
7. GamstedtEK,BerglundLA,PeijsT.FatigueMechanismsinUnidirecional Glass-fibre-reinforcedPolypropylene. CompositesScienceandTechnol-ogy.1999;59:759-768.
8. GamstedtEK,SjögrenBA.MicromechanismsinTension-Compression FatigueofCompositeLaminatesContainingTransversePlies.Composites ScienceandTechnology.1999;59:167-178.
9. StandardTestMethodforTensilePropertiesofOrientedFiberCompos-ites.ASTMD3039;1990.
10. SandiaNationalLaboratories[MandellJF,SamborskyDD].DOE/MSU Composite Material Fatigue Database: Test Methods, Materials and Analysis.Bozeman:ContractorReportSAND97-3002;1997. 11. HerakovichCT.MechanicsofFibrousComposites.Ed.McGraw-Hill,