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Cambon, Jean-Baptiste and Ansart, Florence and Bonino, Jean-Pierre and Turq,
Viviane
Effect of cerium concentration on corrosion resistance and
polymerization of hybrid sol–gel coating on martensitic stainless steel. (2012)
Progress in Organic Coatings, pp. 75 (n° 4). pp. 486-493. ISSN 0300-9440
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Effect
of
cerium
concentration
on
corrosion
resistance
and
polymerization
of
hybrid
sol–gel
coating
on
martensitic
stainless
steel
Jean-Baptiste
Cambon
∗,
Florence
Ansart,
Jean-Pierre
Bonino,
Viviane
Turq
InstitutCarnotCIRIMAT,UniversitédeToulouse,UMRCNRS5085,118RoutedeNarbonne,31062ToulouseCedex9,France
Keywords: Stainlesssteel Sol–gelcoating Corrosioninhibitor EIS NMRspectroscopy
a
b
s
t
r
a
c
t
Stainlesssteelsareincreasinglyusedintheaeronauticsfieldforthemanufactureofstructuralparts.One ofthem,theX13VDmartensiticstainlesssteel(X12CrNiMoV12-3),knownforitsgoodmechanical prop-erties,hasapoorcorrosionresistanceinconfinedorsevereenvironments.Inthepastyears,Cr(VI)based pre-treatmentshavebeencurrentlyusedforcorrosionprotectionofdifferentmetals,however,theyare toxicandduetoenvironmentalregulations,theywillbedefinitelybannedinanearfuture.Alternatives toreplaceCr(VI)showadvantagesanddrawbacksconsideringkeypropertiessuchas:corrosion resis-tance,adhesionofcoatings,fatigueresistance,durabilityandreliability.However,someoftheirpossible alternativesshowhighpotential.
Inthispaper,aprocesswasdevelopedtoimprovethecorrosionresistanceofthemartensitic stain-lesssteel.Organic–inorganichybridcoatingswithdifferentceriumconcentrationsweredepositedonto stainlesssteelbysol–gelprocess.Corrosionresistanceofthecoatingswasevaluatedby electrochemi-calimpedancemeasurementsandithasbeenprovedthatceriumconcentrationof0.01Mintohybrid coatingwasanoptimalcontent.Adhesiontestswerealsocarriedoutby“nanoscratchtest”to character-izethecoatingsmechanicalpropertiesasafunctionofceriumconcentrationbutresultsdonotclearly showtheinfluenceofceriumforthecoatingadhesiontowardthesubstrate.Totrytocorrelatewiththe electrochemicalproperties,liquid29SiNMRspectroscopywasthenperformedtoinvestigatehydrolysis
andcondensationreactionsofsol–gelprocess,andbythismethod,itwasdemonstratedthatforhigher ceriumconcentration(>0.01M)thereisamodificationofthechemicalstructureofthesol–gelnetwork.
1. Introduction
Metallic corrosion occurs as a result of chemical reactions betweenthemetalsurfaceandtheenvironment,whichconverts themetalintoitsoriginalore.Inthecaseofsteelandaluminum, Cl−,O
2andH2Ospecies,inadditiontoelectrontransport,playkey rolesinthecorrosionprocess[1,2].Generally,corrosion preven-tiontechnologyusesoneormoreofthefollowingmethods.The firstoneistheadditionofelements(Cr,Ni,etc.)inthemetalsto enrich thesurface witha corrosion-resistantcomponentduring thecorrosionprocess. Thiscan beassociatedtotheadditionof aqueousinhibitors,whichcanbestronglyadsorbedbychemical conversiontreatmentonthemetalsurfacetopreventthereaction withtheoxidizingagent.Chromates(Cr(VI))areusedasthemost commoncompoundsduetotheirefficiencyinsevereatmosphere andtheirlowcost.Butchromiumbasedcompoundsareextremely toxicadditives,carcinogen,mutagenandreprotoxic.Sotheuseof chromateswillbestrictlyprohibitedinthenextyears[3].
∗ Correspondingauthor.
E-mailaddress:cambon@chimie.ups-tlse.fr(J.-B.Cambon).
Sol–gelcoatingsareoneofthemostpromisingalternative pre-treatments,completelychrome-freewithotheradvantagessuchas cost-effectiveness,lowlife-cycleenvironmentalimpactandsimple applicationprocedures.Thepotentialapplicationofsol–gel coat-ingsas a corrosion protectionsystemfor metalsubstrates was highlighted15yearsagobyGuglielmi[4].Thenseveralworkshave beenundertakentomake varioussol–gelbasedprotective coat-ings,asdescribedinnumerousrecentreviews.Submicronmetal oxidefilmsinhibitcorrosionbyprovidingachemicallyinertbarrier tothediffusionofcorrosivespecies,andtheprotective character-isticsofsol–gelfilmscontainingSiO2[5],TiO2 [6],Al2O3[7],and ZrO2[8],havebeenreportedinvariousstudies.Despiteadvantages ofsol–gelprocessing,ceramiccoatingssufferfromseveral draw-backs:(a)high-temperaturetreatments(>600◦C)arerequiredto decreaseporosityandstabilizethefilms;(b)cracksoccurduring temperaturefluctuationsduetothebrittlenatureofceramicfilms andincompatibilitybetweenthethermalexpansioncoefficientsof metalsandprotectivecoatings;(c)thick(>1mm)crack-freesol–gel coatingsaredifficulttoobtain.Theselimitationscanbeavoidedby thedevelopmentofhybridorganic–inorganicprotectivecoatings, whichcombinethehardness,scratchresistanceandthermal sta-bilityoftheceramiccomponentwiththeflexibility,transparency andtunableadhesionoftheorganicsubstances[9–12].
Table1
ChemicalcompositionofCX13VDstainlesssteel(Febalance).
Element C Cr Ni Mo Va
mol% 0.12 11.5 2.50 1.60 0.30
Fig.1. Semi-developedformulaofGPTMS(glycidoxyproil-trimethoxysilane)(a) andAl(OsBu)
3(aluminumsec-butoxide)(b).
Corrosioninhibitorsareincorporatedintothecoatinginorderto improveitscorrosionresistance.Rareearthelementsand particu-larlyceriumareamongthosecommonlyusedforthatpurposeand ceriumhasbeenfoundasanefficientcathodicinhibitor[13–16]. Theobjectiveofthisworkwastostudytheinfluenceofcerium con-centrationwithinasol–gelhybridcoatingappliedonmartensitic stainlesssteelanddevelopedfromthesystem: glycidoxypropyl-trimethoxysilane(GPTMS)andaluminumsec-butoxideAl(OsBu)
3. Aninvestigationofthesolformulationandchemicalmechanisms wasmade,kineticofhydrolysisandcondensationofalkoxysilanes hasbeenfollowedwithdifferentceriumconcentrationsbyliquid 29SiNMRspectroscopytoidentifysol–gelmechanisms. Hydropho-bic and adhesion properties of different coatingswere studied respectivelybycontactanglemeasurementand“nanoscratchtest” devicetoverifyceriuminfluence.Finally,theanti-corrosion prop-ertiesofceriumdopedorundopedhybridorganic–inorganicwere investigatedbyelectrochemicalconventionaltechniquesandan optimalceriumconcentrationwasfound:0.01Mandacorrelation with29SiNMRresultshasbeentakeninevidence.
2. Experimentalprocedure
2.1. Material
Metallicsubstrates,CX13VDmartensiticstainlesssteelSS (com-positiongiveninTable1)50mm×25mm×1mmsizessamples are cleaned and pre-treated using several steps, after alkaline degreasing,chemicalcleaningcorrespondsto:1minimmersionin fluonitricacid(pH=1)maintainedat60◦C.Sampleisfinallywashed inethanolanddriedinair.
2.2. Solandcoatingpreparation
Solsfromwhich coatingswereprocessed, werepreparedby mixingglycidoxypropyl-trimethoxysilane(GPTMS)andaluminum
tri-sec-butoxideAl(OsBu)
3(formulasinFig.1)anddistilledwater andpropanolinmolarratio5:1:1:10.ThenCe(NO3)3·6H2Owas addedto reach0.001,0.005,0.01,0.05 and 0.1M Ce3+.The sol wasstirredduring2hatroomtemperatureandmaturedfor24h beforedepositiononthesubstratetoinitiatethesol–gelreactions. Theycouldschematicallybedividedintotwosteps,thefirstisa hydrolysisreaction(1)whichaimstopromotereactivehydroxyl groupsreactiveM-OH.Thesecondstepisthecondensation reac-tioninvolvingthealkoxide(2)oronlythehydrolyzedspecies(3).
M(OR)n+nH2O→ M(OH)n+nROH
M(OH)n+M(OR)n→(HO)n−1M-O-M(OR)n−1+ROH M(OH)n→(HO)n−1M-O-M(OH)n−1+H2O
Thesol–gelfilmswereobtainedbydip-coatingprocedure,using animmersion followedby a withdrawalat a controlledrateof 20cmmin−1.Thiswithdrawalspeedhasbeenchosenintherange [1–50cmmin−1] becauseitcorrespondstothemoreconvenient coveringintermofthickness(LandauandLevichlaw)and homo-geneityofthefilm.Afterdeposition,coatedsamplesweredriedin anovenat100◦Cduring24htocompletepolymerizationofthe hybridfilm.
2.3. Characterization
Theviscosityofeachsolwasdeterminedbyaviscometer Rheo-matRM100of typeTaylor–Couette flowat ashear in therange [600–966s−1].
Kineticsofhydrolysisandcondensationofalkoxysilaneswere studiedbyliquid29SiNMRspectroscopy.Themeasurementswere performedonaBrucker400MHzspectrometer.NMRspectrawere recordedwithbenzenelikeinternalchemicalshiftreference.The chemicalshiftsweregiveninppmrelativetotheinternalreference. MacrostructuralpropertiesofcoatingswereevaluatedbySEM microscopy,observationswereperformedonsampleswithaJEOL JSM-6510LVapparatus.
Thickness measurements were performed with a fisher dualscopeFMP20,thistechniqueiscommonlyusedforthe deter-minationofcoatingthicknessessuchaspaints.
Coatingroughnessisevaluatedbywhite-lightinterferometry (ZygoInstruments).
Contactanglemeasurementswereperformedwithwaterdrop methodusingcamera.Thentheimagewasprocessedbyasoftware package(windrop).
ScratchtestswereperformedusingaNanoScratchTesterCSM withadiamondindenterwithconicalgeometry.Thescratchtest wascarriedoutwithprogressiveloadingfrom0to60mN.After thescratchtest,thechangesinthemechanismofscratchandthe criticalloadswerevisualizedbyopticalmicroscopy.
The electrochemical behavior of coating was evaluated by electrochemical impedance spectrometry (EIS) in NaCl (0.1M)+Na2SO4(0.04M)solution.AKClsatelectrode,connectedto theworkingsolution,wasusedasreferenceelectrodeanda plat-inumtapeasauxiliaryelectrode.Allelectrochemicalexperiments wereperformedafterstabilization(1h)offreeopencircuit poten-tial.Electrochemicalimpedancespectra(EIS)rangingfrom65kHz to10mHzwerecarriedwitha80mVsinusoidalperturbation sig-naltothecorrosionpotentialwithSolartronInstrumentSI1286 ElectrochemicalInterfacepotentiostatandaSolartronInstrument SI1260Impedance/Gain-Phase-analyser.Alltheelectrochemical experimentswerecarriedouttoroomtemperatureand theEIS diagramswererecordedforimmersiontimesupto24h.
3. Resultsanddiscussion
Thescanningelectronmicrographsofsubstratebeforeandafter cleaningareshowninFig.2anditwasrevealedaftersurface prepa-rationofmetallicsubstrate,themartensiticmicrostructurewith thepresenceoflamellas.
Theviscosityofasolundergoinghydrolysisand polyconden-sationisstronglydependentintimeandisrelatedtothesizeof particles.Thelargertheformedmolecules,thehighertheviscosity [17].Fig.3showstheeffectofceriumconcentrationonthe viscos-ityofthesolagedfor24h(justbeforedeposition).Anincreaseof viscositycanbeobservedwiththeincreasingofcerium concen-tration.Thisisassociatedwiththehighhygroscopiccharacterof ceriumwhichabsorbsthelargeamountofwatertrappedinthesol network[18].
Fig.2. SEMimagesofsurfacemorphologiesofX13VDstainlesssteelbefore(a)andafter(b)cleaning.
Fig.3.Viscosityofsolswithdifferentconcentrationsofcerium.
Forabetterunderstandingofsol–gelmechanismsintothesols theworkwasonthebondinvolvedinthereactionsversuscerium concentration.
Liquid29SiNMRspectroscopywasusedtoinvestigatethe chem-icalstructureoftheinorganicnetworkjustafterthesynthesisof sols(0h)andafter(24h).Duringhydrolysisandcondensation reac-tions,thesiliconenvironmentchangesfromSi ORtoSi OHthento Si O Si.Then,eachcondensationreaction,withtheformationofa Si O Sioxobridgeinducesachemicalshiftof8–10ppminthehigh field[19].29SiNMRwascarriedouttofollowtheinorganicphase polymerizationofeachsol.The29Sipresentstheresonancesignals at−39,−49,−59and−67ppm,denotedT0,T1,T2andT3 respec-tively[20,21].TheTspeciescorrespondtothesilanescontaining0, 1,2or3hydrolysedgroupsasshowninFig.4.
Fig.5showsthe29SiNMR ofdifferentsampleswithvarious cerium concentrations atthe initialstate(0h). Atthis reaction stage,T0,T1 andT2,werethepresentspeciesinallsamples,no studiedsamplesshowedanysignalofT3.Eachpeakwhich corre-spondedtoT0,T1 and T2 respectivelyhadthesameareaforall samples,whichmeansthattheconcentrationofceriumhad no realinfluenceonthecondensationofsol–gelnetworkand each speciewaspresentinthesameconcentration.Howeveraslight
Fig.5. Liquid29SiNMRspectraofsolwithdifferentceriumconcentrations(0h).
displacementofsignalsinthelowfieldwasobservedforsolswith higherceriumconcentration(0.05and0.1M).Fig.6showsthe29Si NMRofsamesamplesafterasol–gelreactionat24hjustbeforethe depositionstep.Nostudiedsampleshowedsignalofthefree tri-alkoxysilaneprecursorT0andpeakareacorrespondingtospecieT2 increasedforallsamples.Itmeansthatthecondensationincreased inthesamewayforthesolswithdifferentceriumconcentrations. Thisphenomenonisstillobservedforsolswhichcontainedcerium concentrationof0.05and0.1M.Forexample,thefocusontheshift ofT2specie(Fig.7),thiswasclearlyobservedforcerium concentra-tionhigherthan0.01M.Furthermore,onthiszoom,thepresence ofsatellitepeakscanbeunderlined.TheyalsocorrespondtoT2 bondsbutfordifferentspeciesinthesecondsphereof coordina-tion.Inallcases(meanpeakandsatellitepeaks)theshiftfrom0.01 to0.1ispreserved.Intheliterature[22,23],forothersilanebased matrixwithTEOSitcanbeduetotheelectronegativeeffectofCe(III) whichcanreducethelocaldiamagneticshieldinginthevicinityof
Fig.6. Liquid29SiNMRspectraofsolwithdifferentceriumconcentrations(24h).
Fig.7.Liquid29SiNMRspectraofsolwithdifferentconcentrationsofcerium(24h)
focuson10mm.
theattachedprotons.Ceriumhadnoinfluenceoncondensationof networksol–gelbutalargequantityofthisdopant(>0.01M)can changethechemicalstructureofsol–gelnetwork.
Nowitisinterestingtocharacterizethecoatingselaboratedby dip-coatingwiththesolsstudiedpreviously.Fig.8presentsaSEM micrographofasurfaceandcrosssectionofsol–gelcoating with-outceriumdepositedX13VDsubstrate.Atthisscale,thecoatingis homogeneous,covering,crack-freeandadherenttothesubstrate. Theaveragethicknessofcoating,estimatedbythecrosssection analysis(Fig.8b)isabout5–6mm.Thelevelingcharacterofthis filmcanbeunderlinedbywhitelightinterferometry(Fig.9)andthe surfaceroughnessRadecreases(0.42→0.17mm).
Thickness measurements performed by fisher dualscope for hybrid coatings with different cerium concentrations and are reportedinTable2.Thevaluesandtheiraccuracycannotshowa realinfluenceonthelayerthicknessalthoughtheceriumpresence hasincreasedthesolviscosity,parameterdirectlycorrelatedtothe layerthickness[24].
Thehydrophobicitywasevaluatedfromcontactangle measure-mentofawaterdroponhybridcoating.Theobtainedvaluesversus theceriumconcentrationaregiveninFig.10.Thisgraphshowsa slighttendencyofthecontactangleincreasewiththeincreaseof ceriumconcentration,from75◦foracoatingwithoutceriumuntil about80◦forcoatingswithhigherceriumconcentration.Thisvalue underlinesthehydrophobiccharacterofcoatingandimprovesthe tightnesstoward waterwhichisanimportantcharacteristic for anticorrosionproperties.
Anticorrosionpropertiesdependonintrinsicpropertiesofthe coatingsbutalsoonbondsestablishedwiththesubstrateandas a consequenceontheadhesion.To investigatetheinfluence of ceriumonthecoatingsadhesiontostainlesssteelsubstratesscratch testswithincreasingloadwereperformedonthevarious sam-ples.Differentcriticalloads,indicatingchangesinthemechanism ofscratchweredefined[25–27]asitcanbeseeninFig.11: - CL0:Plasticdeformation
-CL1:Brittlefracture -CL2:Delamination
Thedifferentcriticalloadvalues(mN)ofthehybridsol–gel coat-ingwhichcontaindifferentinhibitorconcentrationswereshowed inFig.12.Itwasobservedthatthisconcentrationhadno significa-tiveinfluenceontheadhesionpropertiesofcoatings.Thisgraph showsthatforallceriumconcentrationsinthecoating,thetwo criticalloadsCL0,CL1stayedalmostunchangedconsideringthe accuracyofthemeasurementsbecausethecurveswhich repre-senteachcriticalloadarequitestable.ForthecriticalloadCL2,a slightdecreaseofthisloadcanbeunderlined,probablyduetoa lowerdelaminationresistanceforhighceriumcontent.Thentotry
Fig.9.3Dtopographicanalysisofthesurfacesof(a)X13VDstainlesssteeland(b)hybridcoatingonX13VD,fromawhitelightinterferometer.
Table2
Hybridcoatingthicknessobtainedfordifferentconcentrationsofcerium.
Ceriumconcentration(M) 0 0.001 0.005 0.01 0.05 0.1
Thickness(mm) 5.73±0.6 5.35±0.7 6.01±0.8 5.61±0.5 5.77±0.7 5.89±0.9
Fig.10.ContactanglevaluesofawaterdroponhybridcoatingonX13VDwith differentceriumconcentrations.
tounderstandwhyceriumcontentplaysaroleonsolproperties, itwasplannedtodeterminetheceriumcontentinfluenceonthe corrosionresistanceofcoatings.
Theelectrochemicalimpedancespectroscopy(EIS)isoneofthe mostcommonlytechniqueusedforinvestigationandpredictionof theanticorrosionprotection[28,29].Thispowerfulmethodallows notonlyacomparisonbetweenperformancesofdifferentsystems butalsocangivekeyinformationonkineticsmechanismsofthe coatingdamageandthecorrosionactivityduringimmersioninthe corrosionmedia.InthisworkEISwasusedtoinvestigatetheeffect ofcerium concentrationin solonthecorrosionbehaviorofthe
0 10 20 30 40 50 60 0,12 0,1 0,08 0,06 0,04 0,02 0 Ce(NO3)3 (M) Load (mN) CL 0 CL1 CL2
Fig.12.CriticalloadsforhybridcoatingonX13VDstainlesssteelwithdifferent ceriumconcentrations.
X13VDsubstratescoatedincorrosivesolution(NaCl0.1M+Na2SO4 0.04M).EISdiagramswithX13VDstainlesssteelandhybridcoated sampleswereobtainedafterstabilizationofthecorrosionpotential andfordifferentimmersiontimes.
Fig.13showstheEISplotsinBoderepresentationobtainedfrom thesol–gel hybridcoating withoutceriumcompared toX13VD substrateafter respectively1hand 24himmersion. ForX13VD substrate,theelectrochemicalimpedancediagramsobtainedafter differentimmersiontimesarecharacterizedbytwotimeconstants
Fig.13.Bodephase(a)andmodulusimpedance(b)plotsforX13VDstainlesssteeluncoatedandhybridcoatingwithoutceriumonX13VDstainlesssteelinNaCl (0.1M)+Na2SO4(0.04M)1hand24himmersion.
Fig.14.NyquistplotsforhybridcoatingonX13VDstainlesswithdifferent concen-trationsofceriuminNaCl(0.1M)+Na2SO4(0.04M)1himmersion.
(Fig.13a).Thefirsttimeconstant[0–1000Hz]isindependentofthe immersiontimeandthesecond[0.01–1Hz]oneisbetterdefined forincreasingimmersiontimes.Accordingtoliterature[30,31]if thebarsteelisconsidered,thetimeconstantathighfrequency isattributedtochargetransferprocessandthetimeconstantat thelowfrequencyiscorrelated withtheredoxprocessestaking placeintothepassivefilm.Theincrease ofimpedancemodulus in thelow frequency range (Fig.13b)when immersion time is longercanbeinterpretedbytheimprovementoftheprotection ofthepassivefilm.Forthehybridcoatingdepositedonthe sub-strate(Fig.14a)after1himmersion,twotimeconstantscanbethen observed,oneforthehighfrequencyarea(HF)[1000–65000Hz] whichcanbeattributedtothehybridcoatingproperties:barrier effectwhichlimitschargetransferprocessandanothertime con-stantatmediumfrequency(MF)[1–1000Hz]whereaninflexionof thecurveisobservedwhichcanbeassociatedtothehybridfilm permeability.On hybridcoatingafter24himmersion (10mHz), theappearanceofathirdtimeconstantwasobservedatlow fre-quency(LF).Itisprobablyduetotheformationofapassivation layerattheinterfacebetweenthehybridcoatingandthesubstrate. Thislayer can resultfrom the reactionbetween stainless steel andtheelectrolyte,whichdiffusesintothecoating.Itisthesame phenomenonthatforuncoatedsubstratebuthoweverthis contri-butionremainedrelativelylowduetothehybridbarriereffect.The
highmodulusimpedance(Fig.14b)ofcoatedstainlesssteelslightly decreasedafter24hofimmersionandindicatesthebeginningof thefilmdamage;howevertheperformancesarestillgreatly supe-riortotheseofthepassivatedsubstrate,sothisprovesthegood barriereffectofthesol–gelcoating.
Fig.14showsEISmeasurementswithNyquistplotforhybrid sol–gelcoatingscontainingdifferentconcentrationsofceriumafter 1himmersion.Whenceriumwasaddedincoatingto0.01M,itwas clearlyobservedanincreaseofthecapacitiveloop,itmeansthatthe barriereffectwasimprovedwithlowceriumcontentintherange [0–0.01M].Whenceriumcontentishigherthan0.01M,another behaviorwastakeninevidence:animportantdropofthebarrier effectwithadecreaseofcapacitiveloops,butthistimeitisnot duetoadecreaseofthecoatingthicknessbecausethesolswith ceriumcontentof0.05and0.1Mhaveaviscosityhigher(Fig.3). Thedeteriorationofbarrierpropertiesofthefilmcanbeattributed tothemodificationin thehybridfilmsnetworkby theCeions incorporation,asitwasmentionedbeforebyotherothers[32].
Fig.15 shows EISmeasurements in theBode representation (phaseandmodulus)inordertocomparecorrosionperformance forhybridsol–gelcoatingscontainingdifferentcerium concentra-tions after1himmersion.Whenceriumwasadded insol until aconcentrationreaching0.01M,itwasclearlyobserved onthe curves (Fig. 15a), an improvement of the barrier effect and a decreaseofthepermeabilityofhybridcoatingbecausethe inflec-tionofthecurveatmediumfrequency(MF)wasshiftedtolower frequency.Forhigherceriumconcentrations(0.05and0.1M),the corrosionperformancesofthesecoatingsclearlycollapsedandthe inflectionof thecurveatMFwasshiftedtohigher frequencies. These coatings are more permeable and the electrolyte pene-tratesthecoatings moreeasilyto reactwiththesubstrate and toformthepassivationlayerbecausetheconstanttime at low frequency,characteristicofthispassivationlayer,ismore significa-tive.Theimpedancemodulus(Fig.15b)increasesforlowcerium content(<0.01M)and sharplydecreasesforthesesame cerium concentrationsin thesol–gel coating.Fig.16 shows impedance modulusatlowfrequency(10MHz)versusceriumconcentration. Thismodulusischaracteristicofcorrosionprotectionofthewhole system:hybridcoatingand reactivitywiththesubstrate.Itwas alsoobservedthatthismodulusincreasedwhencerium concen-trationreachedavaluebetween0.005and0.01M.Then,forhigher inhibitorconcentrations, themodulus highlydecreased andthe coatingbecamelessprotectorthancoatingwithoutcerium.The sameremark maybemade for coatingwithdifferent inhibitor concentrationsafteranimmersionof24hinthecorrosive solu-tion. Bode representation withphase (Fig. 17) and impedance
Fig.15.Bodephase(a)andimpedancemodulus(b)plotsforhybridcoatingonX13VDstainlesswithdifferentconcentrationsofceriuminNaCl(0.1M)+Na2SO4(0.04M)1h
immersion.
Fig.16.Impedancemodulus(f=10mHz)withdifferentconcentrationsofceriumin NaCl(0.1M)+Na2SO4(0.04M)1himmersion.
modulus(Fig.18), showsthattheoptimalcerium concentration inthecoatingcorrespondstoavalueof0.01M.
Takenintoaccounttheseresults,onekeypointisconfirmed: theexistenceofathresholdconcentrationofcerium correspond-ingto0.01M.So,itispossibletotrytocorrelatethesecorrosion resultswithchemicaldisplacementsobtainedbyliquid29SiNMR spectroscopyforsolswithahighceriumconcentration.Theseshifts correspondtotheimportantcollapseinanti-corrosionproperties ofsol–gelhybridcoating.Ceriumhadnotanyinfluenceon conden-sationnetworksilanebutalargequantityofthisdopant(>0.01M) canchangethechemicalstructureofhybridnetwork.Thereisan
Fig.18.Impedancemodulus(f=10mHz)forhybridcoatingonX13VDstainlesswith differentceriumconcentrationsinNaCl(0.1M)+Na2SO4(0.04M)24himmersion.
abilitytocreatenewconnection(Ce–Al)withaluminumfromthe ASBofthematrixwhichcoulddestabilizethehybridnetworkand alsoreducetheresistancetowardcorrosionofcoatings.Itwillthen beinterestingtostudythechemicalstructureofsol–gelhybridsat solidstatewithtechniquessuchassolid29Siand13CNMR charac-terizationandRamanspectrometryinordertobetterunderstand nowtheinfluenceofceriumdirectlyoncoatingproperties(these experimentsarenowinprogress).
Fig.17. Bodephase(a)andimpedancemodulus(b)plotsforhybridcoatingonX13VDstainlesswithdifferentceriumconcentrationsinNaCl(0.1M)+Na2SO4(0.04M)24h
4. Conclusion
The influence of cerium concentration on behavior against corrosionofhybridsol–gel coatingonmartensiticX13VD stain-lesssteelhasbeeninvestigated.Theincrease ofceriumcontent improved hydrophobic character of coating and its tightness towardwater.Electrochemicalimpedancespectroscopyshowedan optimalceriumconcentrationof0.01Minthehybridlayer.Besides, theincreaseofceriumconcentrationabove0.01Mdecreasedthe barriereffectofsol–gelcoating.Thecoatingswereperformedby scratchtests,andnosignificativeceriuminfluencehasbeenproved onthe adhesion properties of coatingsto themartensitic sub-strate;soadirectcorrelationbetweenanticorrosionandadhesion performancesofsol–gelcoatingisnotpossible.Liquid29SiNMR spectroscopywasthencarriedouttodeterminatethecerium influ-enceonsolcondensation.Itwasshownthatanexcessofcerium (>0.01M)leadtoachemicalshiftofTspeciesandcanchangethe chemicalstructure of sol–gelnetwork. Thereforea reduction of corrosionresistanceofcoatingsupwasnotedtothesamecerium concentration(0.01M).
Acknowledgments
Thiswork wascarried out in theframework of the ARCAM project,withthefinancial supportof DGCIS,Regions Aquitaine, AuvergneandMidi-Pyrénées.Theauthorsthankfullyacknowledge thepartnersoftheproject:Ratier-Figeac,Aubert&Duval,Olympus, theMechanicalandEngineeringInstituteofBordeaux,the Materi-alsDepartmentofICAMandtheInstituteCARNOTCIRIMAT. References
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