Case
study
Premature
failure
of
dissimilar
metal
weld
joint
at
intermediate
temperature
superheater
tube
Mohammed
Al
Hajri,
Anees
U.
Malik
1,
Abdelkader
Meroufel
*,
Fahd
Al-Muaili
DesalinationTechnologiesResearchInstitute,SalineWaterConversionCorporation,31951Jubail,SaudiArabia
1. Introduction
Forsuperheaterorreheaterboilertubesoperatingathighertemperatures(above5408C),itiscustomarytousestainless steel(SS)inthefinalstagescoveringaportionoftheboilertubingwhichispredominantlycomprisedoflowalloyferritic steel(AS).SSandAStubesarejointbyweldingasinthepresentcaseofITSHtube.Problemsofprematurefailureofwelds betweenthetwodissimilarmaterials(SSandAS)havebeenacommonoccurrenceinboilerindustry.Threemajorcausesof thesecreepfailuresare:carbonmigrationfromtheheat-affectedzone(HAZ)oftheASintotheweldmetal,expansion differencesbetween thetwo varietiesofsteel, andthedifferencesin corrosionresistancetofluegasesleading tothe formationofanoxidewedgeontheoutsidediameteroftheAStubenexttotheweld[1].API571standardconsidermore detailsonthecriticalfactorsleadingtoDMWfailuressuchasweldinggeometry,thermalcycling,etc.[2].DMWfailureof superheatertubeshasbeenreportedinpulverizedcoal-firedpowerplantwherethedifferenceofexpansioncoefficientwas pointedasthemainreason[3].
Ontheotherhand,aninterestingresearchprogramwasconductedbyEPRIinstitutewithobjectivetoprovideguidelines forimprovingdesign andwelding proceduresfor increasingreliabilityandlongevity ofDMW[4].Thefindingsof this programsuggestedthatnickelbaseweldingwithproperheattreatmentformingbandofwelldistributedcarbides(instead ofsharpinterfaceofcarbides)nearthefusionlinewouldimproveDMWlife.Shallowwelddesign,lowtemperatureandlow stressregionoftheDMWwouldalsoprovideadditionalmarginofsafety[4].Asindicationoftherecordedlifetime,nickel baseweldingwassubjectoffailuresinthemid-1970aftergenerally15–17yearsofservice[5].
ARTICLE INFO
Articlehistory:
Received3January2015
Receivedinrevisedform24March2015 Accepted24March2015
Availableonline8April2015
Keywords:
Dissimilarmetalweld Creep
Nickelfiller Superheater PWHT
ABSTRACT
Dissimilarmetalweld(DMW)jointbetweenalloyedsteel(AS)andstainlesssteel(SS) failed at one of intermediate temperature superheater (ITSH) tube in steam/power generationplantboiler.Theprematurefailurewasdetectedafterarelativelyshorttimeof operation(8years)wherethecrackpropagatedcircumferentiallyfromASsidethroughthe ITSHtube.Apartfromphysicalexamination,microstructuralstudiesbasedonoptical microscopy,SEMandEDXanalysiswereperformed.Theresultsoftheinvestigationpoint outthelimitationofCarbidesprecipitationatthealloyedsteel/weldinginterface.Thisis synonymofcreep stageI involvementin thefailureof ITSH.Improper post-welding operationandbendingmomentareconsideredasrootcausesoftheprematurefailure. ß2015TheAuthors.PublishedbyElsevierLtd.ThisisanopenaccessarticleundertheCC
BY-NC-NDlicense(http://creativecommons.org/licenses/by-nc-nd/4.0/).
*Correspondingauthor.Tel.:+96633430333. 1
Retired.
ContentslistsavailableatScienceDirect
Case
Studies
in
Engineering
Failure
Analysis
j o urn a l hom e pa g e : ww w . e l se v i e r. c om / l oca t e / cs e fa
http://dx.doi.org/10.1016/j.csefa.2015.03.006
2213-2902/ß2015TheAuthors.PublishedbyElsevierLtd.ThisisanopenaccessarticleundertheCCBY-NC-NDlicense(http://creativecommons.org/ licenses/by-nc-nd/4.0/).
Inthepresentcase,ASandSSsuperheatertubesarejoinedbynickelbasefillerweldingwhichisknowntohavelow tendencyofcarbidesformation.InadditionithasthermalcoefficientveryclosetothelowalloyferriticsteelssuchasSA213 gradeT11andT22[1].So,theoreticallyweexpectlowstresslevelatelevatedtemperatureforthisweldingmaterial.
However,prematurefailureofDMWoccurredonlyafter8yearsofoperationatITSHtube.Allsuperheatertubesare drainableandhorizontaltype.PartofITSHislocatedinsecondpassandthesecondpartislocatedinthefurnacewhereit receivespartorallofheatbyradiation.FailurelocationisindicatedinFig.1andBoilerspecificationsincludingITSHmaterial informationaresummarizedinTables1and2.
Fig.1.SchematicdiagramshowingthefailurelocationintheITSHarea.
Table1
Boilerspecifications.
Boilerdetail Steamcapacity:637t/h;designpressure:106bar;steamtemp.atS.H.outlet5258C Normalfuel Naturalgas
Commissioned 2000 Failurenoticeddate 28/05/2008
Fluegastemp.atITSHinlet 11218Catnormaloperatingloadwithgasfiring SteampressureatITSHinlet 85.0baratnormaloperatingloadwithgasfiring Steamtemp.atITSHinlet 508Catnormaloperatingloadwithgasfiring Approx.tubemetaltemp. 4808C
2. Results
2.1. Visualinspection
Fig.2showstwoboilertubesamples,madefromlowalloysteel(AS)andstainlesssteel(SS)asreceived.Circumferential crackingwasevidentattheareaadjacenttotheweldregionfromtheASsidewithnoplasticdeformation.Therewasno evidenceofbranchingintheobservedcrack.Fig.3showsinnersideviewofSSandASsplittubes.TheASinnersurface appears to have uniform oxide film whereas SS shows some disruption of the oxide film. Table 3 shows chemical compositionsofASandSSsamplesasanalyzedbyOESandcarbonsulfuranalyzer.Thealloycompositionsarematchingthe gradementionedbyplantauthoritiesshowninTable2[6].
2.2. Microstructurestudy
Fig.4ashowslongitudinalviewoftheSSsampleadjacenttotheweld(heataffectedzone).Thephotomicrographshows polygonalferriticcoarsegrainedstructurealong withsomepocketsofcarbideaggregates.In fact,carbideformationis inhibitedbyextra-lowcarboncontent[7].Thiscouldbeexplainedbyanincreaseoftemperatureduringpost-weldingheat
Table2
Materialinformationaboutboilertubeassuppliedbytheplantauthorities.
Basematerials AusteniticstainlesssteelASMESA-213TP347H–OD:50.8mmandthickness4.4mmferriticsteelASMESA-213Gr T12–OD:50.8mmandthickness4.6mm
Weldjoint SingleV
Weldingprocess GTAW(gastungstenarcweldingTIGwelding)bymachine
Weldingfillerwire TGS-70NCb(ofKOBESteelLtd)orWELTIG-m82(ofNipponWeldingRodCo.Ltd).Thisfillerisequivalent to(AmericanWeldingSociety)-AWSA5.14ERNiCr-3andisanInconel-82ROD
Preheattemperature Min.1218C
Fig.2.Boilersuperheatertubessamplesasreceived.AS:alloyedsteel,SS:stainlesssteel.
treatment(PWHT)above5408CwhichisknownasthresholdtemperatureofcreepforStainlesssteelSA213gradeTPH347 alloy[2].InthisSSalloy,carbidecanformat5408Cafter15min,buttheamountofprecipitateistoosmalltoaffectcorrosion behavior[7].Fig.4bshowsphotomicrographofacross-sectionoftheSSsampleawayfromweldingatthecenter.The structureistwinnedausteniticstructurewithvariablegrainsizewhichisquitedifferentfromtheoneviewedlongitudinally neartheweld(Fig.4a).
Fig.5ashowsmicrostructureatthejunctionofASandwelding.TwophasesarepresentinwhichAShasintermetallic dispersion in a matrix (S1)and theweld exhibitsa single homogeneous phase(S2). Fig.5b shows closeviewof the microstructureattherootofweldingwhereelongated(islandtype)grainscoexistwithdispersedparticles.Fig.6shows microstructureofacross-sectionofASboilertubesample(farawayfromwelding)atthecenterlocationinwhichislandsof pearlitearepresentinaferriticmatrix.
Fig.7a–dshowsmicrostructuresofheataffectedzones(HAZ)at4locationsfromtheASmatrixtotheweldingareanamed HAZ1,HAZ2,HAZ3andHAZ4respectively.AtlocationHAZ1,thestructureiscoarsenedpolygonalferriticinwhichatthe interstitialspearlitegrainsarepacked(Fig.7a).AtlocationHAZ2,afinesecondarybainitestructureisobserved(Fig.7b).The microstructureofHAZ3appearsasafinestructureresemblingtosecondarybainite(Fig.7c).HAZ4showsatypicaltempered martensiticstructuremicrostructureinwhichfreecarbidesaggregationisexhibited(Fig.7d).
Table3
ChemicalcompositionsofASandSSsamplesasanalyzedbyOES.
Element AS SS Fe Balance Balance Cr 0.0625 18.687 Ni – 12.306 Mo 0.452 0.241 C 0.143 0.087 S 0.0035 0.003 Si 0.189 1.57 Mn 0.369 1.567 Cu 0.003 0.148 W 0.009 0.036 V 0.012 0.063
Fig.4.MicrostructureofSSsample,(a)neartheweldjunction;(b)awayfromtheweldjunction(200).
2.3. Hardnesstesting
Thehardnessvalues(inBHN)oftheweldedASandSSsamplesshowincreasingtrendsofhardnessatlocationsawayfrom weldtothelocationsattheweld(Table4).Thevaluesobtainedawayfromtheweldingaresignificantlyreducedcomparedto thevaluesrecommendedinASMEboilercodeparticularlyforAS[6].Thisisduemainlytothelossofcarboninfavortothe junctionareawherewenoteanincreaseofhardnessduetothecarbideprecipitationobservedinthemicrostructurestudy. ThehighhardnessvaluecorrespondstothetemperedmartensiteobservedinHAZ4(Fig.7d).
2.4. Scanningelectronmicroscopy
TheweldingareaobservedbySEM(Fig.8)showscrackprogressingwhichisconsideredassourceofweldingfailures.This crackhasnobranchingandseemsjoiningthegrainboundary.Thiscrackcouldbeduetothepost-weldingtreatmentwhich
Fig.6.MicrostructureatthecenterofAStubefarawayfromwelding(200).
inducesresidualinternalstresses.CrackingofweldmetalcanbecriticalevenifEPRIconsideritassecondorderfactorwhich hasledtofrequentservicefailures[8].
Threelocations(regions)areselectedtobeanalyzedbyEDXi.e.regionS1iscarbidedispersedmatrixclosetotheHAZ,S2 showstheweldingareaandS3showsgrainboundaries.
EDXprofileofthematrix(regionS1)showsveryhighconcentrationsofNi(48%)followedbyFe(25%),Cr(18%)andC (3.5%)indicatingthepresenceof(Fe,Cr)carbidesinthematrix(Fig.9).
Table4
HardnessmeasurementsofASandSSsuperheatertubeparts.
HRB EquivalentHBN Location
ASsuperheatertubepart
75.4 138.2 Awayfromweld
80.1 150 NeartheHAZ
92.0 195 Atthewelding
SSsuperheatertubepart
83.8 161.9 Awayfromweld
85.6 167 NeartheHAZ
90.3 186.3 Atthewelding
Fig.8.SEMimageoftheareaaroundthejunctionofASwelding.
EDXprofileshowninFig.10indicatesastrongpresenceofNi(43%),Fe(31%),Cr(16%),andC(4.9%).Thisresultconfirms thenickel-chromebasecompositionofthefillerasmentionedinTable2.Thistypeofweldingalloyhasverylowtendencyto formcarbidesandthermalcoefficientveryclosetoferriticASsteel[1].
Fig.11showsEDXprofileofregionS3representinggrainboundariesalsoindicatesthehighcontentsofcarbon.This carbideprecipitationisknowntobeinducedbytemperatureincreaseleadingtothecarbondiffusiontothegrainboundaries.
3. Discussion
Based on the above investigation results, it appears that dissimilar metal welds (DMW) failed on the AS side. Microstructurestudyshowedcarbonmigratedfromalloysteelintotheweldmetal.Thismigrationresultsintheformationof chromiumironcarbidesalongthewelding/ASinterfaceasobservedbymicroscopeanddetectedbyEDXanalysis.Two consequencesofthiscarbidesprecipitationcouldbementioned:
Fig.10.EDXprofileofpositionS2(weldedarea).
1.ThedecreaseofthecreepstrengthofAS(whichisafunctionofcarboncontent)neartheweldinginterface. 2.Theincreaseoftheweldinghardness.
ThefailureofDMWintheformofmicrocrackobservedinthefillerweldingmaterialjoiningtheASgrainboundarycould beduemainlytothreereasons:
a.Highhardnessoftheweldingcombinedtothethermalfatigue, b.ResidualthermalstressescausedbyimproperPWHT,
c.BendingstressesduetothehorizontalpositionoftheweldingintheITSHtubeswhichisnotrecommendedbyEPRI guidelinesasdiscussedbyFrench[9].
Thethermalfatiguemechanismpossibilitycouldbeexcludedformanyreasonsi.e.thegoodthermalstabilityofthefiller anditsthermalexpansioncoefficientwhichisclosetotheoneofAS.Inaddition,theboilerwasincontinuousserviceto supplynecessarysteamforthermaldesalinationplant(duetothehighwaterdemand).Therefore,thenumberofthermal cyclesismuchreduced.
The possibilityof animproperPWHT is reinforcedbythedetection ofcreep stageI (carbidesspheroidization and precipitation)intheareaclosetotheweldingwhileitwasnotobservedfarfromthefailurearea(basematerial).Itiswell establishedthathightemperaturesencounteredduringeitherpost-weldingheattreatment(PWHT)orserviceprovidethe activationenergyforcarbondiffusiontooccur[10].ToillustratethatimproperweldingcouldbetherootcauseofDMWin shorttimecouldbefoundintheworkdonebyUl-Hamidetal.[11]wherethelifetimewaslessthan2.5years.
OntheotherhandandaccordingtoEPRIrecommendations[12],theusedfiller(Inconel82)doesnotneedPWHT. Thethirdreasonrelatedtothebendingstresses,isdependentonthestart-upprocedureandthehorizontalpositionof ITSHtubesandclosetothestringertubes.AsdepictedinFig.1,theimpactofbendingmomentcouldbeconsideredsincethe failurelocationveryclosetoastringertube.
4. Conclusions
1.Thefailuremechanismofintermediatetemperaturesuperheater(ITSH)appearstobedissimilarmetal(SSandAS)weld (DMW).
2.ThemicrostructuralstudiesoftheweldsamplessupportedbyEDXanalysisshowtheprecipitationofcarbideattheweld/ metalinterfacewhichisastrongevidenceofcreepstageIprocessinvolvement.
3.Bendingstressesand/orimproperweldingoperationappearstoplaysomerolecrackformationintheweldstructure. 4.Themiss-applicationofrecommendedNi-baseweldingfillerplaysaneffectiveroleinshorteningthelifetimeofthis
junction.
5. Recommendations
1.Thereappearstobeshortcomingsduringtheweldingofdissimilarmetalboilertubesresultinginthefailureoftubes. Therefore,thestandardprocedureforproperweldingshouldbestrictlyfollowed.
2.Strictcontroloftheboilerstart-upprocedureshouldreducethepossibilityofbendingstressesonhorizontalDMW.
References
[1]ASMhandbook.Failureanalysisandprevention,vol.11.ASM;2002.
[2]API571.Damagemechanismsaffectingfixedequipmentintherefiningindustry–recommendedpractice.1sted.AmericanPetroleumInstitute;2003.
[3]RahmanMM,KadirAK.Failureanalysisofhightemperaturesuperheatertube(HTS)ofapulverizedcoal-firedpowerstation.IntJAdvSciEngInfo Technol2011;1:517–22.
[4]PragerM.Dissimilar-weldfailureanalysisanddevelopmentprogram.Vol.8.In:EPRIreport;1989.
[5]PortRD,HerroHM.TheNALCOguidetoboilerfailureanalysis.NY:McGraw-Hill;1991.
[6]2010ASMEboilercode.ASMEPublications;2010.
[7]ASMhandbook.Metallographyandmicrostructures,vol.9.ASM;1985.
[8]ColemanK.Developmentofanewnickelfillerfordissimilarmetalweldsandrepair.In:EPRIreport;2009.
[9]FrenchD.Metallurgicalfailuresinfossilfiredboilers.2nded.Wiley;1993.
[10]ChristoffelR,CurranR.Carbonmigrationinweldedjointsatelevatedtemperatures.WeldJ1956;35:457–68.
[11]Ul-HamidA,TawancyHM,AbbasNM.Failureofweldjointsbetweencarbonsteelpipeand304stainlesssteelelbows.EngFailAnal2005;12:181–91.
[12]ViswanathanR.Dissimilar-weldfailureanalysisanddevelopmentprogram.Volume8:designandprocedureguideforimprovedwelds.In:EPRI report;1989.