SCI论文写作重要结构4.docx
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SCI论文写作重要结构4.docx
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SCI论文写作重要结构4
1.Infact,aneffectiveinterfaceisnecessarytoguaranteethestresstransferfromthematrixtotheload-bearingfibers.
2.Thelinearfitofaveragevalues(lineinFig.4)indicatesarateofweightincreasesofGOonGFsof0.00133±0.00003%cmmin_1V_1.AsimilartrendwasobservedalsobyAnetal.[39]whostudiedtheEPDprocessofCNTsontoE--glassfibersfabrics.(116中)
3.Thisexperimentalevidencecouldbeexplainedbythegoodefficiencyof
theloadtransfermechanismsduetothesurfacefunctionalgroupsavailableontheGOlayersandtheconcurrentincreaseoftheapparentfiberdiameterduetotheGOcoating.
4.Thispositiveeffectcouldbetentatively(暂且)attributedtothefactthatGOcreatesafavorablebondbetweentheGFsandepoxyresinwhichultimatelyenhancestheeffectivedistributionofloadontheGF.
5.InthisworkapartofCBwithGNPswasreplacedtoproduceethylene-propylenedieneterpolymerrubber(EPDM)basednanocomposites.
6.Itsmaindrawbackisthepercolationthresholdthatisusuallyhighanddetrimentalforthemechanicalproperties.
7.OwingtosignificantvanderWaal'sinteractionsbetweennanotubes,achievementofefficientMWNTdispersioninpolymermatricesremainsachallenge.
8.Butthedisruptionofthepsystemofnanotubeshasanirreversibleeffectontheirelectricalproperties.
Themixturewasthentransferredtoathree-necked,round-bottomedflaskundericebath,whereupon30mLofHClsolution,having1.53gAPSandananilinemolarratioof1:
1,wasslowlyaddeddropwiseinto
thesuspensionwithconstantmagneticstirring.
9.Fig.4showstheroom-temperatureelectricaltransportpropertiesofMWNT/PANIcomplexasafunctionofMWNTcontent.
10.Allthreeelectricalconductivitycurvespossesstwophases:
firstasharpincrease,thenaplateau.
11.Carbonnanotubeshavewellordered,long,hollownanostructuresconsistingofcarbonatomsbondedtoeachotherthroughsp2hybridizedbonds.
12.ThecrucialobstacletodesignanelectricallyconductingdeviceisthepoorandheterogeneousdispersionofthepristineCNTsinpolymermatrices[21].Asaresult,thepristineCNTsareaggregatedandexistasabundleintheirnativestate.Forthesereasons,itishighlydesirabletodevelopanefficientandsimplemethodnotonlyindividuallytodissolveCNTsinpolymermatrices,butalsotocontrolconcentrationofCNTs,resultinginincrementoftheCNTinterconnectivitywithinthepolymermatrix,whichtranslatestheindividualCNTpropertiesintothewholecomposite.
13.ThethicknessoftheP3PT-COOHphasegraduallyincreasedwiththe
increaseofP3PT-COOHconcentration:
e.g.~2e~5nmforP3PTCOOH/CNT-50-1,~4e~6nmforP3PT-COOH/CNT-40-1,and
~5e~7nmforP3PT-COOH/CNT-30-1.
14.Toshedfurtherlightontheeffectofgrapheneaspect-ratio,we
usedgraphenenanosheetswithtwodifferentsizes.
15.Surfacemodificationofgrapheneusingorganicmaterialsisoneapproachtoexfoliategrapheneinwhichtheinteractionoccursviaeithercovalentbondingorviap–pstacking.Althoughthistechniqueisshowntobeeffectivetoexfoliategraphenelayers,ithinderstheirelectricalpropertiesbecauseitdisturbsthep-electronsdelocalizationofgraphenesurface.
16.Withtheincorporationof4wt%ofc-MoS2,the5%masslosstemperatureofWPUnanocompositefilmwasincreasedby30_CrelativetoneatWPU.
17.Comparedtothepolymermatrix,thesenanocompositesexhibitsignificantlyenhancedthermal,mechanicalandbarrierpropertiesinthepresenceoflownano-fillerloading.
18.Deionizedwaterisusedforallexperimentsunlessotherwisestated.
19.AggregatedMoS2fillerscanalsoserveasdefectcenters,whichisdetrimentaltomechanicalproperties.
20.TEMandXRDtechniquesshowedthatcMoS2swerewellexfoliatedandrandomlydispersedinWPUmatrix,whilebareMoS2sexistedwithastacked/aggregatedstructure.
21.(d)isthehighmagnifiedimageoftheredsquare-markedregionsin(c).
22.Itsfavorablephysicochemicalstability,aswellasappealingelectronicstructurecombinedwithasuitablebandgap(2.7eV)makesitapromisingcandidateforsolarenergyphotocatalyticapplications.
23.Significantchallengesstillremaininthesynthesisofg-C3N4based
nanocompositeswithwell-designedarchitecturesandoptimizedchargecascadingprocesses.
24.thecharyieldoftheneatBMIresinat800Cis28.2%,andthatofthecompositeis30.9%,anincreaseof9.6%,indicatingthatthepresenceofNH2-rGO/MoS2canenhancethethermalpropertyoftheneatBMIresin.
25.Thus,inrecentyears,themodificationofBMIresinhasbecomea
hotspotofresearch.
26.ButthecarbonyieldofHBPSi-rGO/BMIcompositesat800_Cis4.7%higherthanthatoftheneatBMI.ThecarbonyieldforHBPSi-rGO/BMI
is29.5%andneatBMIis24.8%.
27.ThemorphologiesofSi−C−Gcompositeswereexaminedbyafield-emissionscanningelectronmicroscopy(FESEM,JEOL,JSM-7000F)equippedwithenergydispersiveX-rayspectroscopy(EDS).ThemicrostructuresofSi−C−Gcompositeswereinvestigatedusingatransmissionelectronmicroscopy(TEM,JEOL,ARM-200F,200kV).
28.TheSiNPshaveanarrowparticle-sizedistributionof50−100nmandNGmicrosphereshaveaparticlesizeofapproximately12−15μm.
29.Asexpected,theSi−C−GcompositesshowhigherelectricalconductivitiesthanthatofphysicallymixedNGandSiNPs.
30.Morethan10measurementsforthethicknessofapapersamplewerecarriedout,andtheresultswereaveraged.
31.Itisthusvalidtocontend(认为)thatAgNWscanbecoatedtightlyoncellulosepapersviathespecificinteractionsmeditatedbyPVP,asrepresentedschematicallyinFigure4B.
32.ItwasalsoreportedthatcelluloseandPVPblendsaremiscibleatthemolecularlevelviaaspecificinteractionbetweencarbonylgroupsofPVPandprimaryhydroxylgroupsofcellulose.
33.ThemainadvantageofusingthisapproachforECAsapplicationisthatweareabletopreservethesinglelayerstructureofgrapheneandpreventtheirre-stackinginsidethenanocompositewithoutdisturbingitsstructure.
34.Fivesamplesweretestedforeachcomposite,andtheaveragevaluewasreported.
35.Whileinrecentyears,withtherapiddevelopmentofenergyandautomobileindustries,epoxy-basedcompositeswithfurtherenhancementinmechanicalpropertieswereurgentlycalledforhigh-performancepurposes.Promisingly,theadditionofnanofillersintopolymermatrixeswasahighlyefficientpathtoachievethisgoal,sincetheconcepthadbeen
welldocumentedbymanynewlyemergedhigh-performancecompositescontainingmultiscaleandmultifunctionalfillers.
36.Amongvariousnanofillers,graphenewasbelievedaspromisingfillerforhigh-performancecompositesbecauseofitssuperiormechanical,electrical,andthermalproperties,whichoriginatedfromitstwo-dimensionalhoneycombstructurecomposedofsp2carbonatoms.
37.However,thekeychallengeforfullyexertingthewholeperformanceofGOinpolymercompositesistoachieveitsuniformdispersioninthecompositesviaensuringitsstronginterfacialbondingwithpolymericmatrixes.
38.Allfinalvaluesoftensileandflexuralpropertieswereaveragesoffivemeasurements.
39.BydeconvolutionoftheC1speakinthecaseofpDop-rGO,aC−Ncomponentat285.5eVwasidentified(Figure3b).(XPS分峰的说法)
40.InFigure3c,thedeconvolutionoftheN1speakindicatedthatthe
NelementinpDopwasinformsof-N=(398.5eV),-NH-
(399.8eV),and-NH2(401.7eV),andthesecondaryaminewasdominant.(XPS分峰的说法)
41.TheresultedpDop-rGOhadshowndifferentsurfacemorphologyandchemicalfeaturesfrompristineGO,whichevokedkeeninterestinstudyingitseffectonmechanicalpropertiesandcuringkinetic
ofepoxycomposites.
42.AsshowninFigure5,mostofpDop-rGOsheetswereobservedscatteringintheepoxymatrixevenlywithsporadicaggregations.
43.Theoretically,theenhancementinmechanicalstrengthandmodulusofEP/pDop-rGOcompositesshouldbekeptgoingupcontinuouslywiththecontentofpDop-rGOincreasing.Indeed,thepracticaltensilestrengthandmodulusofepoxycompositesincreasedwhenthecontentofpDop-rGOchangedfrom0to0.2wt%.However,thesevaluesbegantodecreasewhenthecontentofpDop-rGOwasfurtherraisedto0.5wt%,whichwasinconsistentwiththepredictedtendency(Figure4a).
44.Incontrast,theprimaryandsecondaryaminegroupsonpDop-rGOwerereactivewithepoxidegroup.Theirenhancementincuringreactionofepoxymatrixwasabletooffsetthenegativeeffectoncuringreactionfromthesterichindrance.
45.WiththestrengthenedinterfacialbondingbetweenpDop-rGOandepoxymatrix,thereinforcingmechanismofpDop-rGOonepoxycompositesarousedourkeeninteresttolookintoit.
46.Theabovecharacterizations,intermsofFT-IR,XRD,UV–vis,XPS,andTGA,indicatethatGOhasbeenreducedandfunctionalizedbyDA,whichpavesthewayforthepreparationofPDA-GO/epoxycomposites.
46.Reporteddataaretheaveragevaluesofatleastthreeindividualmeasurements.
47.ItclearlyindicatesthattheMWCNTremainsaggregatedintheLi–Al-LDH/MWCNT/SRcompositeascompactbundles.
48..Furthermore,thereisapossibilitythatthehighestspecificsurfaceareaofMg–Al-LDH/MWCNThybridanditshomogeneousdispersioncouldresultinthestronginterfacialinteractionandefficientstresstransferbetweenSRandMg–Al-LDH/MWCNTfillers.ThiscouldaccountforthemaximumimprovementinthemechanicalpropertiesMg–Al-LDH/MWCNT/SRcomposite.
49.Li–Al-LDHfilledSRshowsalmostnoimprovementinthethermalstabilityinallprobabilityduetoitsthermaldecompositionproduct(Li2O)actingasdestabilizerforSR.
50.ThisisprobablyduetothehomogeneousdispersionandstronginterfacialinteractionbetweenMg–Al-LDH/MWCNTandS
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