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Investigation into Properties of Laser Welded Similar and Dissimilar

Steel Joints

Article in Science and Technology of Welding amp Joining middot April 1998

DOI 101179stw199834177

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Iskenderun Technical University

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Ccedilinar Yeni

Dokuz Eylul University


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S Erim

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V Ventzke

Helmholtz-Zentrum Geesthacht


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Investigation into properties of laser weldedsimilar and dissimilar steel jointsG cam c Yeni s Erim v Ventzke and M Ko~ak

and narrow heat affected zone (HAZ) development com-pared to conventional fusion welding processes Despitethe high investment cost of laser welding equipment it isexpected that laser welding will have a great impact onfabrication and manufacturing industries for the welding ofmedium section steel structures within the next decade2However the significance of the metallurgical and mechan-ical properties of LB welds combined with the unique shapeof the weld joint still needs to be established for structuralcomponents

Laser welded joints like all other weld joints may containdefects in the form of cracks in the narrow weld area orcracks may develop from inhomogeneities during ser~iceThe size and location of such cracks associated with charac-teristics of the local microstructure and the level of mechan-ical strength mismatch between the weld region and theparent plate under certain service conditions directly affectthe joint performance and the lifetime of a structure It isnow known that the variation in mechanical properties ofdifferent regions (strength mismatch) of a conventional weldjoint can significantly influence the deformation character-istics of welds in service However LB welding produces avery narrow weld bead and HAZ which may be anadvantage over conventional processes if the weld jointshows high hardness-strength (ie low toughness) owing tothe occurrence of plastic deformation in the parent plateunder external stresses However for prequalificationor defect assessment purposes the determination of themechanical properties of a very narrow LB fusion zone cannot be done by standard testing procedures For instanceit is usually observed that transverse tensile specimens failin the softer base metal and that fracture path deviationoccurs in Charpy V notch and crack tip opening displace-ment (CTOD) fracture toughness testing of these weldsowing to mechanical property mismatch between the base

Laser beam welding is currently used in the welding ofsteels aluminium alloys thin sheets and dissimilarmaterials This high power density welding process hasunique advantages of cost effectiveness deep penetra-tion narrow bead and heat affected zone (H AZ)widths and low distortion compared to other conven-tional welding processes However the metallurgicaland mechanical properties of laser welds and theresponse of conventional materials to this new processare not yet fully established The welding process maylead to drastic changes in the microstructure withaccompanying effects on the mechanical properties andhence on the performance of the joint The thermalcycles associated with laser beam welding are generallymuch faster than those involved in the conventional arcwelding processes This leads to the formation of arather small weld zone that exhibits locally a highhardness in the case of C-Mn structural steels owingto the formation of martensite It is currently difficultto determine the tensile properties (full stress-straincurves) of the laser welded joint area owing to thesmall size (IV 2-3 mm) of the fusion zone Completeinformation on the tensile and fracture toughness prop-erties of the fusion zone is essential for prequalificationand complete understanding of the joint performancein service as well as for conducting a defect assessmentprocedure on such welded joints Therefore an experi-mental investigation into the mechanical properties oflaser welded joints was carried out to establish a testingprocedure using fiat micro tensile specimens (05 mm inthickness 2 mm in width) for determination of thetensile properties of the weld metal and H AZ of thelaser beam welds Three similar joints namelySt 37-St 37 St 52-St 52 and austenitic-austeniticand two dissimilar ferritic-austenitic joints were pro-duced by CO2 laser using 6 mm thickness plates Themechanical properties have been examined by micro-hardness survey and testing of conventional transversetensile round tensile and fiat microtensile specimensThe results for the micro tensile specimens were com-pared with those for standard round tensile specimensand this clearly showed the suitability of the micro-tensile specimen technique for such joints

I~--

1(c)

Dr ram Dipl-Phy Ventzke and Dr Korak are atthe GKSS Research Center Institute of MaterialsResearch D-21502 Geesthacht Germany and Dr Yeniand Dr Erim are in the Faculty of EngineeringMechanical Engineering Department Dokuz EyliilUniversity Izmir Turkey Manuscript received 12November 1997 in final form 16 December 1997

copy 1998 The Institute of Materials

INTRODUCTIONThe laser beam (LB) welding prQcess has unique advantagesof cost effectiveness deep penetration narrow bead width

a 8t 52-8t 52 b 8t 52-austenitic c austenitic-austeniticd 8t 37-austenitic e 8t 37-8t 37

1 Schematic iJIustration of LB welded joints platethickness 6 mm

6mm _ ~irweld

L~30mm r11

~gt ~--- I~--I

57mm------220 mm ------ __

2 Standard transverse tensile specimen

Science and Technology of Welding and Joining 1998 Vol 3 NO4 177

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2mm

178 (am et al Laser welded similar and dissimilar steel joints

Pre-shaped block ~

fl 1 at mlcrotensl e specImenextracted by spark erosioncutting technique

t

O5mm

Loading pins

3 Extraction of microtensile specimens from LB weldedplates

metal and the weld region Therefore these standardisedtest results may provide information only on the perform-ance of the entire joint under tensile impact and bendingloading conditions respectively They may fail in providingrequired intrinsic tensile and toughness properties of the

fusion zone owing to interaction (unavoidable) betweenthe weld region and the parent plate under applied deforma-tion For CTOD toughness determination the effects ofspecimen geometry (weld width crack size notch positionetc) and the degree of strength mismatch between the basemetal and the weld region on toughness have to be takeninto account3-11

With regard to the establishment of the flat micro tensilespecimen testing procedure and hence determination ofthe tensile property gradient existing in the LB fusion zonethis particular work has been conducted The flat microtens-ile specimen technique was originally developed for propertydetermination in HAZs of conventional multipass weldjoints used in the nuclear industry12 Successful applicationsof this technique to thick section similar and dissimilarelectron beam welds3 and to bond strength determinationfor diffusion bonded joints1314have also been carried outat the GKSS Research Center The present study is anextension of these experimental activities and specificallyaddresses the development and validation of the testingprocedure for LB steel welds Hence similar and dissimilarLB weld joints between ferritic and austenitic steels pro-duced by CO2 laser using 6 mm thickness plates weresystematically investigated

EXPERIMENTALIn the present study austenItIc stainless steel 14404(X 2 Cr Ni Mo 18 10) and ferritic steels (grades St 37 andSt 52) were used as the base metals Similar and dissimilarsingle pass full penetration CO2 LB welds were producedwithout using filler wire (Fig 1) Extensive microhardnessmeasurements (using 100 g load) were performed across thewelded regions at three different locations namely at theweld root midsection and top part of the joints In additionthe narrow HAZ region of the ferritic steel was extensivelyscreened by conducting microhardness measurements paral-lel to the fusion line

a macro section b higher magnification of region indicated in a4 Similar St 37 LB joint

Science and Technology of Welding and Joining 1998 Vol 3 NO4

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9am et al Laser welded similar and dissimilar steel joints 179

a macrosection b higher magnification of region indicated in a

5 Similar St 52 LB joint

Standard flat transverse tensile specimens were extractedfrom the welded plates and tested at room temperature(Fig 2) The weld reinforcement was machined before test-ing Sets of flat microtensile specimens were extracted byspark erosion cutting from the base metals HAZs andweld metals of all the joints studied as schematically shownin Fig 3 The flat micro tensile specimen preparation wasconducted mainly in two stages (a) extraction of a pre-shaped block with a laser weld in the centre (b) cutting ofspecimens from the etched preshaped block using a sparkerosion cutting technique (with 0middot1 mm diameter copperwire) parallel to the weld Owing to the small size of themicro tensile specimens loading was introduced using fourhigh strength round pins at the shoulders of the specimens(Fig 3) After testing the broken half of each specimen wasmounted for microstructural verification of the specimenlocation The fracture surfaces of selected specimens werealso examined by scanning electron microscopy

For optical metallography specimens were mounted inbakelite and ground with silicon carbide papers of 220 400800 1200 and 2400 grades followed by polishing on arotating wheel with 7 and 2 Jlm diamond paste Ferriticsteels were etched with a solution comprising 2 nitricacid in alcohol for 10 s while V2A etchant which consistsof 100 mL distilled water 100 mL HCI 10 mL HN03 and0middot3 mL Vogels Sparbeize (etching solution) was used toetch austenitic steels at 70degC the etching time being 5-10 s

RESULTS AND DISCUSSIONMicrostructural observationsMicrostructural examination showed that the weld regionsof all the joints with a ferritic constituent contained marten-site and bainite Ferritic-ferritic similar joints displayed aweld metal structure consisting of martensite and bainite(Figs 4 and 5) whereas austenitic-austenitic similar weldsexhibited an austenitic dendritic (cellular) structure with noevidence of martensite formation as expected (Fig 6)

Solidification cracking was not observed in the austeniticsimilar weld which might be a result of the very fineaustenite cell size characteristic of the primary austenitesolidification process of this steel grade The HAZ inferritic similar joints contained a refined ferrite-pearlitestructure and pearlite dissolution at the base metal sides

a macrosection b higher magnification of region indicated in a6 Similar austenitic LB joint


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180 (am et aT Laser welded similar and dissimilar steel joints

a macro section b higher magnification of region indicated in a7 Dissimilar St 37-austenitic LB joint

while no distinct HAZ was observed in austenitic similarjoints

Ferritic-austenitic dissimilar joints conversely showedan inhomogeneous weld metal microstructure (Figs 7 and8) A narrow HAZ was observed on the ferritic steel sidein contrast to the austenitic side where there was no distinct

Weld Centre

J

HAZ15 This is typical of dissimilar steel LB weldmentsThe HAZ on the ferritic steel side of the St 37-austeniticjoint contained no martensite in contrast to that of theSt 52-austenitic joint which exhibited some martensiticstructure The remainder of each weld in the centre dis-played an inhomogeneous microstructure which contained

a macro section b higher magnification of region indicated in a

8 Dissimilar St 52-austenitic LB joint

Science and Technology of Welding and Joining 1998 Vol 3 No4

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ram et al Laser welded similar and dissimilar steel joints 181

Weld Centre~

9 Solidification cracking in weld region of dissimilar joint

ferritic-austenitic and bainitic andor martensitic phases invarying degrees owing to an incomplete mixture of themolten metals of both sides in the weld pool duringsolidification Some austenitic dendritic (cellular) structurewas also observed at the austenitic steel side Moreoversome solidification cracks were observed in the weld regionsof the dissimilar joints (Fig 9) which indicates that stresslevels developed in these weldments sufficient to separatethe grain boundaries in the cellular structure (presentingrather flat smooth crack paths) during solidification It canalso be assumed that low melting constituents were segre-gated along these boundaries which resulted in solidifi-cation cracking during the final stages of solidification

Microstructural examination and microhardness meas-urements were also carried out on the microtensile speci-mens to correlate the mechanical properties with the micro-structure Compositional analyses of the weld metals arecurrently in progress to correlate the microstructures withthe Schaeffler diagram that was originally developed forconventional welds

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500 500(e) i--weld centre

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Distance from weld centre mm

a schematic illustration of microhardness measurement procedure b similar 8t 37 c similar 8t 52 d similar austenitic e dissimilar8t 37-austenitic f dissimilar 8t 52-austenitic

10 Hardness profiles of joints


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182 9am et al Laser welded similar and dissimilar steel joints

40

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determined by testing given tensile specimens

HardnessThe welding process may lead to drastic changes in themicrostructure with accompanying effects on the propertiesof the joint The thermal cycles associated with laser weldingare generally faster than those involved in the conventionalwelding processes This is a natural consequence of the lowheat input and high welding speed (rapid cooling rate) Itdoes mean however in C-Mn structural steels that theweld region will exhibit locally high hardness values Todetermine hardness profiles in the present work extensivemicrohardness measurements were conducted at threelocations (top middle and root) as shown in Fig lOa Themicrohardness results exhibited no significant differencebetween these three locations for all the welded jointsstudied It can be concluded therefore that no significantgradient in mechanical properties of laser welds along theplate thickness direction is expected

Similar ferritic steel joints displayed a high hardnessprofile in the weld region while similar austenitic weldsshowed no significant increase in hardness across the jointSimilar St 37 and St 52 joints exhibited hardness values of270-350 HVOl (Fig lOb) and 405-450 HVOl (FiglOc)respectively whereas similar austenitic joints displayedhardness values of 210 HVOmiddot1 in the weld region(Fig 10d) This is expected owing to the lack of bainiteandor martensite formation in the weld regions of austeniticjoints Dissimilar St 37-austenitic joints displayed a hard-ness peak in the weld metal which exhibited values of 380-400 HVOmiddot1 Dissimilar St 52-austenitic joints dis-

a 8t 37 b 8t 52 c austenitic steel12 Comparison of stress-strain curves for base metals

obtained by testing standard round and flat microtensilespecimens

played a hardness peak of 425 HVOl at the ferritic sideslightly higher than that of the weld metal which exhibitedhardness values of 400 HVOl this was caused by thepresence of martensite in the narrow HAZ region at theferritic side (designated as HAZ-F hereafter) as mentionedabove Higher hardness values obtained in the weld regionsof ferritic similar and dissimilar joints resulted from thepresence of bainite andor martensite in the microstructureHardness profiles of the dissimilar joints are shown inFig lOe and f The presence of high hardness peaks indicatesthe strength overmatching nature of the weld joints

Mechanical propertiesStandard round tensile specimens of the base metals weretested to determine the mismatch ratios M from the prop-erties given in Table 1 Stress-strain curves for the roundtensile specimens (diameter 4 mm gauge length 20 mm)extracted from the base metals are shown in Fig 11a Theyield strength mismatch ratios for the base plates ofSt 37-austenitic and St 52-austenitic dissimilar joints M =YSSt37YSausand M = YSausYSSt52were found to be 0middot76and 0middot8 respectively Standard flat transverse tensile


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Mismatch ratios M = YSSt 37 YSaus and M = YSausYSSt 52 whereYS is yield strength

specimens were also tested to determine the mechanicalproperties of the joints (Fig lIb) Similar and dissimilarjoints containing ferritic steel always failed in the lowerstrength ferritic base metal owing to the very high hardnessof the weld region The stress-strain curves obtained forthe flat transverse tensile specimens show some differencesfrom those obtained for the round tensile specimens owingto the presence of the LB weld region at the centre of theformer specimens (Fig 11) The stress-strain curves for thedissimilar joints lie between those of the similar joints ofthe constituent steels as expected (Fig lIb) Evidentlytransverse tensile testing particularly for ferritic steel con-taining joints where a very high hardness profile existsdoes not give any information on the local mechanicalproperties of the weld region

Stress-strain curves obtained for standard round and flatmicrotensile specimens of the base metals are compared inFig 12 Although there are slight differences between thecurves owing to the different geometries of these twospecimen types they are in good agreement which indicatesthat the flat microtensile specimen technique can be usedto determine local mechanical properties of the narrowLB welds

Hence all weld metal and all HAZ flat microtensilespecimens were prepared and tested to determine the local

Table 1 Mechanical properties of base metals

Base metal

St 37St 52Austenitic steel(14404)

YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00

51middot0650middot5849middot61


mechanical properties of the respective areas in the weldregions Table 2 summarises the mechanical properties ofthe ferriticbase metals (BM-F) austenitic base metal(BM-A) weld metals (WM) HAZs of the ferritic steels(HAZ-F) and HAZs of the austenitic steel (HAZ-A) insimilar and dissimilar joints determined using microtensilespecimens The weld metal regions of the joints containinga ferritic constituent exhibited high strength (overmatching)and low strain values whereas austenitic similar jointsshowed similar strength (even matching) and strain levelsin the weld metal HAZ and base metal regions as themicrohardness results indicated The strength mismatchratios for the weld metal regions and the respective basemetals (lower strength base material in the case of dissimilarjoints) M =YSWMYSBS are also given in Table 2 Thehighest mismatch (M = 309) existed between the weld metaland base metal of the similar St 37-St 37 joint The fullstress-strain curves for all specimens are shown in Fig 13The individual values of the yield strength (YS) tensilestrength (TS) and fracture strain with respect to specimenlocation for all the joints are shown in Fig 14 The charac-teristic microstructure for each micro tensile specimen waschecked (after testing) by optical metallography at thegauge length region of the specimens Figures 15-19 showrepresentative micrographs for all five weld joints Theseresults are discussed in detail below

Ferritic similar jointsFigure 13a and e show the stress-strain curves for micro-tensile specimens extracted from the similar ferritic jointsand Fig 14a and e show the variations in mechanicalproperties of these joints As is seen from these figures theweld metals particularly in the case of St 52 exhibited thehighest strength levels and the lowest strain values com-pared to the base metal and HAZ regions The HAZ regionsof these joints also exhibited higher strength levels andlower strain values than those of the respective base metals

The microstructures of the weld metal HAZ and basemetal specimens of the similar St 37 joint are shown in

Table 2 Summary of BM HAZ and WM mechanical properties of LB welded jointst determined by testing of microtensilespecimens values in parentheses are averages

St 37-St 37 St 37-austenitic Austeni tic-austeni tic St 52-austenitic St 52-St 52

YS TS YS TS YS TS YS TS YS TSMPa MPa MPa MPa MPa MPa MPa MPa MPa MPa

BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590

Mt 3middot09 2middot28 1middot13 2middot21 2middot53

YS yield strength TS tensile strengtht F ferritic A austenitict M = YSwMYSBMmiddot


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HAZ-A

20 30 40 50 60 70 80

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184 ram et al Laser welded similar and dissimilar steel joints

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a similar 8t 37 b dissimilar 8t 37-austenitic (HAZ-F next to fusion line) c similar austenitic d dissimilar 8t 52-austenitice similar 8t 52

13 Stress-strain curves for Oat microtensile specimens extracted from given joints

Fig 15 The base metal microstructure consisted of coarseferrite with some pearlite (Fig 15a) The HAZ microtensilespecimen displayed a similar microstructure of ferrite andpearlite containing finer regions (Fig 15b) indicating thatthe specimen was extracted from the base metal side of theHAZ The weld metal specimens on the other hand exhib-ited a microstructure comprising grain boundary ferritewith bainite and possibly martensite (Fig 15c) The fracturesurfaces of the all HAZ (extracted from the HAZ) and allWM (extracted from the weld metal) micro tensile specimensof the similar St 37 joint exhibited a predominantly ductilefailure mode (Fig 20) The fracture surface of the all HAZspecimen displayed extensive dimple formation (Fig20a)whereas that of the all WM specimen exhibited the forma-tion of a limited number of rather large voids and theircoalescence (Fig 20b)

The microstructures of the weld metal HAZ and basemetal specimens of the similar St 52 joint are shown inFig 16 The base metal microstructure consisted of coarseferrite with elongated pearlite (Fig 16a) The HAZ micro-tensile specimen displayed a finer microstructure than thatof the base metal with pearlite dissolution (Fig 16b) Theweld metal specimen on the other hand exhibited a micro-structure comprising martensite and bainite with somegrain boundary ferrite (Fig 16c) Fracture surfaces of themicro tensile specimens extracted from this similar ferriticjoint exhibited a predominantly ductile failure modeFigure 21 shows the fracture surfaces of the all HAZ andall WM specimens The fracture surface of the all HAZspecimen (Fig 21a) displayed a mixed brittle + ductile frac-ture mode (regions with a flat brittle fracture appearancecorresponding to the pearlite dissolution bands shown in


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(am et al Laser welded similar and dissimilar steel joints 185

1400 80(b) HAZ-A 701200

1000 60

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YS 20200 10

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1000 6mm 60

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30400 TS 20200 YS 10 ma

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a similar 8t 37 b dissimilar 8t 37-austenitic c similar austenitic d dissimilar 8t 52-austenitic e similar 8t 5214 Mechanical property variations across joints 0 represents weld centre

Fig 16b) whereas that of the all WM specimen exhibited apredominantly brittle fracture mode (Fig 21b)

Austenitic similar jointFor the austenitic similar joint the weld metal and HAZexhibited slightly lower strain values than that of the basemetal with no significant alterations in the strength level(Figs 13c and 14c) The microstructures of the base metalHAZ and weld metal specimens of the similar austeniticjoint are shown in Fig 17 The base metal and HAZmicro tensile specimens exhibited similar microstructuresconsisting of austenite grains with some 8 ferrite indicatingthat there is no appreciable alteration in the microstructurein the HAZ of austenitic steel joints (Fig 17a and b) Theweld metal specimen displayed a homogeneous dendriticstructure (Fig 17c) Fracture surfaces of the microtensilespecimens extracted from the similar austenitic joint alsoexhibited a predominantly ductile failure mode Figure22 shows the fracture surfaces of the all HAZ and allWM specimens The fracture surface of the all HAZ speci-men displayed extensive dimple formation (Fig 22a)whereas that of the all WM specimen exhibited the for-mation of limited and coarse voids and their coalescence(Fig 22b)

Dissimilar joints(St 37-austenitic and St 52-austenitic)In dissimilar joints the weld metals exhibited the higheststrength levels with limited strain values as seen in Figs 13band d and 14b and d The reason for the extremely lowstrain values exhibited by the weld metals is the presenceof harder microstructural constituents (bainitemartensite)as well as the solidification cracks in these regions as seenin Fig 9 The HAZs at the ferritic sides (HAZ-F) alsodisplayed relatively higher strength levels and lower strainvalues than those of the respective ferritic base metals TheHAZs at the austenitic sides (HAZ-A) on the other handdid not exhibit a significant increase in strength but somedecrease in strain value compared to the austenitic basemetal

The microstructures of the weld metal HAZ and basemetal specimens of the dissimilar St 37-austenitic joint areshown in Fig 18The ferritic base metal specimen exhibiteda microstructure comprising ferrite and some pearlite(Fig 18a) However the micrQstructure was significantlyfiner than that of the base metal of the ferritic similar jointwhich is the reason for the different stress-strain curvesobtained (Fig 13a and b) The difference between thestrengths of the St 37 base metals of similar and dissimilarjoints is indicated in Table 2 This difference is a result of


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a ferritic base metal b HAZ-F c weld metal18 Optical micrographs of microtensile specimens of

dissimilar St 37-austenitic joint extracted from givenlocations

the different welding directions with respect to the rollingdirections in similar and dissimilar joints of the St 37 gradeThe HAZ at the ferritic side (HAZ-F) exhibited a muchfiner ferrite + pearlite structure than that of the ferritic basemetal (Fig 18b) The weld metal specimen on the otherhand displayed an inhomogeneous microstructure contain-ing a mixture of ferrite and austenite solidification structures(Fig 18c) The HAZ at the austenite side (HAZ-A) and theaustenitic base metal displayed a microstructure similar tothat shown in Fig 17a and b

The microstructures of the weld metal HAZ and basemetal specimens of the dissimilar St 52-austenitic joint areshown in Fig 19 The ferritic base metal specimen exhibiteda microstructure comprising ferrite with elongated pearlite(Fig 19a) The HAZ at the ferritic side (HAZ-F) exhibiteda finer microstructure than that of the ferritic base metalwith pearlite dissolution (Fig 19b) Although a very narrowregion of martensite had been previously observed in theHAZ-F in this joint as also indicated by the hardnesstransverse the micro tensile specimen microstructure didnot reveal this phase as this small region was not sampledin the extraction of the specimens The weld metal speci-

am et al Laser welded similar and dissimilar steel joints 187



men on the other hand displayed an inhomogeneousmicrostructure containing a mixture of ferrite andaustenite solidification structures (Fig 19c) The HAZ atthe austenitic side (HAZ-A) and the austenitic basemetal displayed a microstructure similar to that shown inFig 17a and b

Fracture surfaces of the micro tensile specimens extractedfrom the base metals and the HAZs of the dissimilar jointsalso exhibited a predominantly ductile failure modeHowever the all WM specimens exhibited a non-uniformfracture surface which consisted of ductile regions andcleavage fracture of the dendritic zones (Fig 23) Figure 23ashows the fracture surface of the dendritic region wheresome microplastic zones were clearly seen Figure 23b illus-trates a correspondence with the optical micrograph of thedendritic structure formed in the weld region (Fig 9)

As discussed above the mechanical properties (includingfull stress-strain curves) of each zone of LB welded similarand dissimilar joints can be successfully determined usingthe flat micro tensile specimen technique Complete inform-ation (not only hardness values) relating to the localmechanical properties of laser welds is often essential for


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188 9am et at Laser welded similar and dissimilar steel joints

a fracture surface of HAZ showing extensive void formationb fracture surface of WM showing limited void formation

20 Fracture surfaces of HAZ and WM of similar St 37 joint

optImIsation of the laser welding process and filler wiredevelopment for various alloys as wellmiddot as quality controland fracture mechanics analyses (experimental and numer-ical) of the welds Development of filler wire compositionsto reduce the level of hardenability of C-Mn steel jointsand the level of softening of aluminium alloy weld joints iscurrently of great interest To take a step forward in theseareas complete information regarding the local propertiesof actual weld joints should be generated The testingtechnique described in the present paper can provide suchinformation

The present results are part of a large project carried outat the GKSS Research Center on the microstructural andmechanical characterisation of LB welded steels The cor-relation of microhardness measurements conducted onmicro tensile specimens with mechanical properties of therespective areas of the joints is currently being conductedFracture toughness (CTOD) testing of the joints at roomand low temperatures is also currently in progress and theresults will be reported in a future publication

CONCLUSIONS1 The microstructures of CO2 laser welded C-Mn steels

contain large proportions of bainitemartensite in the weldregion owing to the rapid cooling involved Thus anextreme hardness increase in the weld regions of ferriticsimilar and ferritic-austenitic dissimilar joints was observedin contrast to similar austenitic joints the weld region ofwhich displayed no significant hardness alteration

2 All transverse tensile specimens failed at the lowerstrength base metal sides owing to the strength mismatch


a fracture surface of HAZ showing mixed brittle + ductilemode of fracture (regions with flat brittle fracture appearanceindicated by arrows corresponding to pearlite dissolutionbands shown in Fig 16b) b fracture surface of WM showingpredominantly brittle fracture mode


effect Even the presence of some solidification cracks indissimilar joints did not change the fracture location causedby the strength overmatching of the weld region

3 Microtensile specimens extracted from the weld metalsof similar ferritic joints displayed significantly higherstrength values and markedly lower strain values than thoseofmiddot specimens extracted from the respective base metalsowing to the presence of bainitemartensite in the weldregions The all HAZ specimens also exhibited higherstrength values and lower strain values than those of thebase metals The base metal HAZ and weld metal ofsimilar austenitic steel joints exhibited similar strength andstrain values as expected since no hardness peak wasobserved in these joints

4 Microtensile specimens extracted from the weld zonesof dissimilar joints exhibited high strength and low strainvalues The all HAZ specimens extracted from the HAZsat the ferritic sides also displayed higher strength and lowerstrain values than those of the respective ferritic base metalswhereas the specimens extracted from the HAZs at theaustenitic sides and the austenitic base metals away fromthe weld regions exhibited similar strength and strain valueswith no significant alteration

5 Finally successful application pf the flat microtensilespecimen techniquemiddotmiddot to laser welded joints which exhibitvery narrow weld regions was demonstrated By using thistechnique it is possible tomiddot determine the local mechanicalproperties ofjoints which can be correlated with the respect-ive microstructure and hardness

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22 Fracture surfaces of HAZ and WM of similaraustenitic joint

ACKNOWLEDGEMENTSThis work is part of the German-Turkish joint projectfinanced by International Bureau KFA-Jiilich and TiirkiyeBilimsel Teknik Arastirma Kurumu Turkey The authorswould like to thank both organisations for their financialsupport They would also like to thank H Mackel and SRiekehr for their technical assistance in testing The metal-lography work of W-V Schmitz and P-M Fischer is alsogreatly appreciated

REFERENCES1 J MAZUMDER ASM handbook Vol 6 Welding brazing and

soldering 262-269 1993 Materials Park OH ASMInternational

2 E A METZBOWER Proc Indo-US workshops on solidificationprinciples and materials processing Hyderabad India January1988 Vol 22-25 655-669

3 M KOcAK and E JUNGHANS Proc 2nd European Conf onJoining Technology Florence Italy May 1994 Italian Instituteof Welding


a overview showing complete thickness of microtensilespecimen b higher magnification of a showing existingsolidification cracking (SC) in weld metal (also shown inFig 9)

23 Fracture surface WM of dissimilar joint

4 1 K KRISTENSEN Proc Conf Exploitation of laser processingin shipyards and structural steelworks Glasgow UK May1996

5 M KOcAK and K-H SCHWALBE Neu Entwicklungen im kon-struktiven Ingenieurbau (ed H Saal and 6 Bucak) 137-1551994 Karlsruhe University of Karlsruhe

6 J K KRISTENSEN and K BORGREEN Proc 5th European Confon Laser Treatment of Materials Bremen-Vegesack GermanySeptember 1994Bremer Institut flir Angewandte Strahltechnik

7 K-H SCHWALBE and M KOcAK Proc 3rd Int Conf on Trendsin Welding Research Gatlinburg TN USA June 1992 ASMInternational (ed S A David and J M Vitek) 479-494 1992Materials Park OR ASM International

8 Z SUN and T MOISIO Weld J April 1994 63-709 M KOcAK M ES-SOUNI L CHEN and K-H SCHWALBE Proc

8th Int Conf and Exhibition on Offshore Mechanics andArctic Engineering The Hague The Netherlands March 1989ASME 623-633

10 M T KIRK and R H DOODS Report UILU-ENG-92-2005University of Illinois Urbana IL 1992

11 H C CAO and A G EVANS Mech Mater 1989 7 295-30412 E KLAUSNITZER Materialpriifung 1976 11411-41613 G cAM K-H BOHM J MULLAUER and M KOcAK JOM 1996

48 (11) 66-6814 G cAM J MULLAUER and M KOcAK Sci Techno Weld Joining

1997 2 (5) 213-21915 C YENI S ERIM G cAM and M KOcAK Proc Int Symp

Welding Technology 96 Istanbul Turkey May 1996 GedikEducation Foundation 235-247


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Investigation into properties of laser weldedsimilar and dissimilar steel jointsG cam c Yeni s Erim v Ventzke and M Ko~ak

and narrow heat affected zone (HAZ) development com-pared to conventional fusion welding processes Despitethe high investment cost of laser welding equipment it isexpected that laser welding will have a great impact onfabrication and manufacturing industries for the welding ofmedium section steel structures within the next decade2However the significance of the metallurgical and mechan-ical properties of LB welds combined with the unique shapeof the weld joint still needs to be established for structuralcomponents

Laser welded joints like all other weld joints may containdefects in the form of cracks in the narrow weld area orcracks may develop from inhomogeneities during ser~iceThe size and location of such cracks associated with charac-teristics of the local microstructure and the level of mechan-ical strength mismatch between the weld region and theparent plate under certain service conditions directly affectthe joint performance and the lifetime of a structure It isnow known that the variation in mechanical properties ofdifferent regions (strength mismatch) of a conventional weldjoint can significantly influence the deformation character-istics of welds in service However LB welding produces avery narrow weld bead and HAZ which may be anadvantage over conventional processes if the weld jointshows high hardness-strength (ie low toughness) owing tothe occurrence of plastic deformation in the parent plateunder external stresses However for prequalificationor defect assessment purposes the determination of themechanical properties of a very narrow LB fusion zone cannot be done by standard testing procedures For instanceit is usually observed that transverse tensile specimens failin the softer base metal and that fracture path deviationoccurs in Charpy V notch and crack tip opening displace-ment (CTOD) fracture toughness testing of these weldsowing to mechanical property mismatch between the base

Laser beam welding is currently used in the welding ofsteels aluminium alloys thin sheets and dissimilarmaterials This high power density welding process hasunique advantages of cost effectiveness deep penetra-tion narrow bead and heat affected zone (H AZ)widths and low distortion compared to other conven-tional welding processes However the metallurgicaland mechanical properties of laser welds and theresponse of conventional materials to this new processare not yet fully established The welding process maylead to drastic changes in the microstructure withaccompanying effects on the mechanical properties andhence on the performance of the joint The thermalcycles associated with laser beam welding are generallymuch faster than those involved in the conventional arcwelding processes This leads to the formation of arather small weld zone that exhibits locally a highhardness in the case of C-Mn structural steels owingto the formation of martensite It is currently difficultto determine the tensile properties (full stress-straincurves) of the laser welded joint area owing to thesmall size (IV 2-3 mm) of the fusion zone Completeinformation on the tensile and fracture toughness prop-erties of the fusion zone is essential for prequalificationand complete understanding of the joint performancein service as well as for conducting a defect assessmentprocedure on such welded joints Therefore an experi-mental investigation into the mechanical properties oflaser welded joints was carried out to establish a testingprocedure using fiat micro tensile specimens (05 mm inthickness 2 mm in width) for determination of thetensile properties of the weld metal and H AZ of thelaser beam welds Three similar joints namelySt 37-St 37 St 52-St 52 and austenitic-austeniticand two dissimilar ferritic-austenitic joints were pro-duced by CO2 laser using 6 mm thickness plates Themechanical properties have been examined by micro-hardness survey and testing of conventional transversetensile round tensile and fiat microtensile specimensThe results for the micro tensile specimens were com-pared with those for standard round tensile specimensand this clearly showed the suitability of the micro-tensile specimen technique for such joints

I~--

1(c)

Dr ram Dipl-Phy Ventzke and Dr Korak are atthe GKSS Research Center Institute of MaterialsResearch D-21502 Geesthacht Germany and Dr Yeniand Dr Erim are in the Faculty of EngineeringMechanical Engineering Department Dokuz EyliilUniversity Izmir Turkey Manuscript received 12November 1997 in final form 16 December 1997

copy 1998 The Institute of Materials

INTRODUCTIONThe laser beam (LB) welding prQcess has unique advantagesof cost effectiveness deep penetration narrow bead width

a 8t 52-8t 52 b 8t 52-austenitic c austenitic-austeniticd 8t 37-austenitic e 8t 37-8t 37

1 Schematic iJIustration of LB welded joints platethickness 6 mm

6mm _ ~irweld

L~30mm r11

~gt ~--- I~--I

57mm------220 mm ------ __

2 Standard transverse tensile specimen

Science and Technology of Welding and Joining 1998 Vol 3 NO4 177

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Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




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0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

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Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




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Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




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yen 8t 37-BM I

HAZ-A

20 30 40 50 60 70 80

HAZ-A +

~



1400 1400(a) HAZ HAZ + (b)

1200 T

~

1200

1000 6mm 1000~

800 800600

HAZ600


0 00 5 10 15 20 25 30 35 40 0 101400 1400

(c) + (d)1200

~

1200

1000 1000ctSa 800 800~en HAZ


CJ) 400 400-~ VVM

200 200

0 00 10 20 30 40 50 60 70 80 0 10 20 30 40 50 60 70 80

1400 Strain 00(e) +1200

~

1000

800 600

400 bull

BM200

00 5 10 15 20 25 30 35 40

Strain ok






Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


20020

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8

1400 80

1200 70

1000 60

50800

40600

30400 20200 10

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations







Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd



Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd












Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
















Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
























Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd





Weld Centre

J





Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


Weld Centre~




500(b)

~weld centre

400

300

200

(a) + + bullbull

100-3 -2 -1 0 2 3



C~~c

~8~0 200~ 200(J

~

100 100-3 -2 -1 0 2 3 --3 -2 -1 0 2 3


400 400

300 300

200 200

100 100-3 -2 -1 0 2 3 -3 -2 -1 0 2 3





Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


40

80

353025

bullbullbull

2015


bullbull


10 15 20 25 30 35 40

Strain

10


5

5

10 20 30 40 50 60 70


~ 1

(b)

(c)

(a)



800

700

600500400

300200 -

100

oo

800700

ctSa 500~en 400~ 300l0-

U) 200

100

oo

800

700

600

500400

300

200100

oo

80

80

70

70

60

t

8~Bweld1

St 37

30 40 50Strain 00

30 40 50 60Eng Strain 00

20

20

Aus-AusI-------


10

10


~St52

(b)

St52-St52

800

700

800

700

600

CO 500a~()- 400()

~Ci5 300

200

100

00

600COa~ 500()-() 400~

Ci5cigt 300cw

200

100

00










Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd






Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Aus-BM

yen 8t 37-BM I

HAZ-A

20 30 40 50 60 70 80

HAZ-A +

~



1400 1400(a) HAZ HAZ + (b)

1200 T

~

1200

1000 6mm 1000~

800 800600

HAZ600


0 00 5 10 15 20 25 30 35 40 0 101400 1400

(c) + (d)1200

~

1200

1000 1000ctSa 800 800~en HAZ


CJ) 400 400-~ VVM

200 200

0 00 10 20 30 40 50 60 70 80 0 10 20 30 40 50 60 70 80

1400 Strain 00(e) +1200

~

1000

800 600

400 bull

BM200

00 5 10 15 20 25 30 35 40

Strain ok






Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


20020

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8

1400 80

1200 70

1000 60

50800

40600

30400 20200 10

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations







Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd



Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd












Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
















Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
























Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


Weld Centre~




500(b)

~weld centre

400

300

200

(a) + + bullbull

100-3 -2 -1 0 2 3



C~~c

~8~0 200~ 200(J

~

100 100-3 -2 -1 0 2 3 --3 -2 -1 0 2 3


400 400

300 300

200 200

100 100-3 -2 -1 0 2 3 -3 -2 -1 0 2 3





Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


40

80

353025

bullbullbull

2015


bullbull


10 15 20 25 30 35 40

Strain

10


5

5

10 20 30 40 50 60 70


~ 1

(b)

(c)

(a)



800

700

600500400

300200 -

100

oo

800700

ctSa 500~en 400~ 300l0-

U) 200

100

oo

800

700

600

500400

300

200100

oo

80

80

70

70

60

t

8~Bweld1

St 37

30 40 50Strain 00

30 40 50 60Eng Strain 00

20

20

Aus-AusI-------


10

10


~St52

(b)

St52-St52

800

700

800

700

600

CO 500a~()- 400()

~Ci5 300

200

100

00

600COa~ 500()-() 400~

Ci5cigt 300cw

200

100

00










Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd






Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Aus-BM

yen 8t 37-BM I

HAZ-A

20 30 40 50 60 70 80

HAZ-A +

~



1400 1400(a) HAZ HAZ + (b)

1200 T

~

1200

1000 6mm 1000~

800 800600

HAZ600


0 00 5 10 15 20 25 30 35 40 0 101400 1400

(c) + (d)1200

~

1200

1000 1000ctSa 800 800~en HAZ


CJ) 400 400-~ VVM

200 200

0 00 10 20 30 40 50 60 70 80 0 10 20 30 40 50 60 70 80

1400 Strain 00(e) +1200

~

1000

800 600

400 bull

BM200

00 5 10 15 20 25 30 35 40

Strain ok






Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


20020

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8

1400 80

1200 70

1000 60

50800

40600

30400 20200 10

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations







Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd



Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd












Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
















Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
























Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


40

80

353025

bullbullbull

2015


bullbull


10 15 20 25 30 35 40

Strain

10


5

5

10 20 30 40 50 60 70


~ 1

(b)

(c)

(a)



800

700

600500400

300200 -

100

oo

800700

ctSa 500~en 400~ 300l0-

U) 200

100

oo

800

700

600

500400

300

200100

oo

80

80

70

70

60

t

8~Bweld1

St 37

30 40 50Strain 00

30 40 50 60Eng Strain 00

20

20

Aus-AusI-------


10

10


~St52

(b)

St52-St52

800

700

800

700

600

CO 500a~()- 400()

~Ci5 300

200

100

00

600COa~ 500()-() 400~

Ci5cigt 300cw

200

100

00










Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd






Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Aus-BM

yen 8t 37-BM I

HAZ-A

20 30 40 50 60 70 80

HAZ-A +

~



1400 1400(a) HAZ HAZ + (b)

1200 T

~

1200

1000 6mm 1000~

800 800600

HAZ600


0 00 5 10 15 20 25 30 35 40 0 101400 1400

(c) + (d)1200

~

1200

1000 1000ctSa 800 800~en HAZ


CJ) 400 400-~ VVM

200 200

0 00 10 20 30 40 50 60 70 80 0 10 20 30 40 50 60 70 80

1400 Strain 00(e) +1200

~

1000

800 600

400 bull

BM200

00 5 10 15 20 25 30 35 40

Strain ok






Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


20020

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8

1400 80

1200 70

1000 60

50800

40600

30400 20200 10

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations







Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd



Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd












Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
















Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
























Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd






Base metal


YieldstrengthMPa

233382308

TensilestrengthMPa

368528626

Elongation00

363069

Reductionin area00









BM-F 230 (222) 370 (372) 330 (325) 419 (415) 355(363) 545 (535) 369 (372) 523 (536)215 376 327 404 372 522 379 536215 367 334 440 371 529 384 541228 374 307 398 355 545 357 545

BM-A 326 (319) 593 (598) 316 (319) 611 (607) 312 (317) 607 (607)304 573 326 609 318 601320 608 318 601 318 617325 616 316 607 320 602

WM 640 (685) 825 (851) 900 (740) 988 (797) 360 552 745 (702) 998 (860) 980 (930) 1232 (1155)730 893 580 606 658 722 900 1141638 804 910 1092732 880

HAZ-F 320 432 416 496 580 757 620 870316 435 378 472 424 624 564 760298 421 718 823 382 557280 406 370 540

HAZ-A 424 591 448 621 438 668410 613 430 619 396 590




Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Aus-BM

yen 8t 37-BM I

HAZ-A

20 30 40 50 60 70 80

HAZ-A +

~



1400 1400(a) HAZ HAZ + (b)

1200 T

~

1200

1000 6mm 1000~

800 800600

HAZ600


0 00 5 10 15 20 25 30 35 40 0 101400 1400

(c) + (d)1200

~

1200

1000 1000ctSa 800 800~en HAZ


CJ) 400 400-~ VVM

200 200

0 00 10 20 30 40 50 60 70 80 0 10 20 30 40 50 60 70 80

1400 Strain 00(e) +1200

~

1000

800 600

400 bull

BM200

00 5 10 15 20 25 30 35 40

Strain ok






Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


20020

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8

1400 80

1200 70

1000 60

50800

40600

30400 20200 10

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations







Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd



Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd












Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
















Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
























Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd

Aus-BM

yen 8t 37-BM I

HAZ-A

20 30 40 50 60 70 80

HAZ-A +

~



1400 1400(a) HAZ HAZ + (b)

1200 T

~

1200

1000 6mm 1000~

800 800600

HAZ600


0 00 5 10 15 20 25 30 35 40 0 101400 1400

(c) + (d)1200

~

1200

1000 1000ctSa 800 800~en HAZ


CJ) 400 400-~ VVM

200 200

0 00 10 20 30 40 50 60 70 80 0 10 20 30 40 50 60 70 80

1400 Strain 00(e) +1200

~

1000

800 600

400 bull

BM200

00 5 10 15 20 25 30 35 40

Strain ok






Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


20020

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8

1400 80

1200 70

1000 60

50800

40600

30400 20200 10

0 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations







Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd



Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd












Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
















Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd
























Pub

lishe

d by

Man

ey P

ublis

hing

(c)

IOM

Com

mun

icat

ions

Ltd


1400 80(b) HAZ-A 701200

1000 60

50800

40600 Strain 30400 TS

YS 20200 10

0 ~0-5 -4 middot3 -2 -1 0 1 2 3 4 5 6 7 8 9 c-

1400 80 sect

(d)U5

1200 70

1000 60

50800

TS 40600

30400 YS 20200 10

a 0-6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 8 9

Specimen Locations

1400 80(a) HAZ HAZ 701200 T

1000 6mm 60

-l 50800

40600 Strain

30400 TS 20200 YS 10 ma

0 0 ~-7 -6 -5 -4 -3 -2 -1 0 1 2 3 4 5 6 7 rE

0gt1400 200 c~

1200 180 U5trBT 1601000 Aus Aus rm

140ma 800 120 ~~ 0


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Documents

Investigation into Properties of Laser Welded Similar and ......hYbg]`YdfcdYfh]Yg cZ h\Y kY`X aYhU` UbXA :R cZ h\Y `UgYf VYUa kY`Xg* L\fYY g]a]`Uf ^c]bhg( bUaY`m Kh/3)Kh 15* Kh1.)Kh