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Journal of Materials Processing Technology 214 (2014) 402– 408

Contents lists available at ScienceDirect

Journal of Materials Processing Technology

jou rn al h om epage : www.elsev ier .com/ locate / jmatprotec

ffect of welding speed on microstructures, mechanical propertiesnd corrosion behavior of GTA-welded AISI 201 stainless steel sheets

ichan Chuaiphana,∗, Loeshpahn Srijaroenpramongb

Department of Industrial Engineering, Faculty of Engineering, Foundry & Metallurgical Technology Centre, Rajamangala University of Technologyrungthep, 2, Nanglinchee Road, Tungmahamek, Sathorn, Bangkok 10120, ThailandDepartment of Metallurgical Technology, Faculty of Education, Foundry & Metallurgical Technology Centre, Rajamangala University of Technologyrungthep, 2, Nanglinchee Road, Tungmahamek, Sathorn, Bangkok 10120, Thailand

r t i c l e i n f o

rticle history:eceived 7 March 2013eceived in revised form0 September 2013ccepted 21 September 2013vailable online 1 October 2013

a b s t r a c t

Three welding speeds designated as low (1.5 mm/s), medium (2.5 mm/s) and high (3.5 mm/s) were oper-ated during the gas tungsten arc welding (GTAW) process and joints made were subjected to analysis ofthe microstructures, mechanical and corrosion properties of the joints. It was found that the joints madeusing the high welding speed exhibited smaller weld bead size, higher tensile strength and elongation,higher hardness and higher pitting corrosion potentials than those welded with medium and low weld-ing speeds. The dendrite length and inter-dendritic spacing in the weld zone reduced when increasingthe welding speed which was the main reason for the observable changes in the tensile, hardness and

eywords:elding speed

ISI 201 stainless steelorrosion behaviorechanical propertiesicrostructureas tungsten arc welding

corrosion properties of the weld joints.© 2013 Elsevier B.V. All rights reserved.

. Introduction

AISI 304 stainless steel is a widely used material as it hasuperior corrosion resistance. In this alloy, 18 wt.% chromium isdded to improve corrosion resistance, whereas alloying nickelt 8 wt.% is used to stabilize the austenite matrix, as reported byavid and Cheryl (2005) and International Stainless Steel Forumembers (2005). However, the price of nickel is relatively high

nd fluctuating as compared to other austenite forming elements,articularly manganese. AISI 201 was then developed to be anption with the same 18 wt.% of chromium. Manganese is added tohis steel at 7 wt.% to stabilize the austenite phase instead of nickel,nd nickel is reduced from 8 wt.% to 3 wt.% in AISI 201 steel. An

ndustrial question in this study is that if an AISI 304 stainless steelart fails in service, is it possible to replace that part by a cheaperISI 201 stainless steel. If welding is applied to join the AISI 201

∗ Corresponding author at: Department of Industrial Engineering, Faculty of Engi-eering, Rajamangala University of Technology Krungthep (RMUTK), 2, Nanglincheeoad, Tungmahamek, Sathorn, Bangkok 10120, Thailand. Tel.: +66 2 287 9645;

ax: +66 2 287 9645; mobile: +66 89 789 8489.E-mail addresses: Wichan.c@rmutk.ac.th, choypun@hotmail.com

W. Chuaiphan), loeshpahn.s@rmutk.ac.th (L. Srijaroenpramong).

924-0136/$ – see front matter © 2013 Elsevier B.V. All rights reserved.ttp://dx.doi.org/10.1016/j.jmatprotec.2013.09.025

stainless steel, the optimum welding parameters must be able toprovide acceptable weld bead shape, appropriate microstructure,appropriate mechanical properties and pitting corrosion resistancefor the weld. Many researchers have focused on the microstruc-tures, mechanical properties and corrosion resistance of austeniticstainless steel AISI 304 weld joints. This study takes AISI 201 intoaccount. There is limited research in this area.

Wichan and Loeshpahn (2012) studied the effect of filler alloyon microstructure, mechanical and corrosion behavior of dissim-ilar weldment between AISI 201 stainless steel and low carbonsteel sheets produced by GTAW. It was concluded that the ER309Land ER316L fillers were the good candidates to promote the pit-ting corrosion resistance of weld metals and were comparable withthat of AISI 201 base metal. This is due to the high Cr content(24.791 wt.%) in AISI 309L filler, the Mo content (2 wt.%) and Crcontent (21.347 wt.%) in ER316L filler. Somrerk et al. (2012) car-ried out the plasma arc welding between AISI 304 and AISI 201stainless steels. It was found that mixing nitrogen in argon shiel-ding gas up to 12% (v/v) could reduce the amount of delta ferrite inaustenite matrix from 20 to 16%, v/v. It also increased pitting corro-

sion potential from 401 to 472 mV vs Ag/AgCl. This was due to theincreased nitrogen in the weld metal which was from nitrogen inshielding gas. Ahmet’s (2004) experiment on the effect of hydrogenin argon as a shielding gas in TIG welding of austenitic stainless steel

W. Chuaiphan, L. Srijaroenpramong / Journal of Materials Processing Technology 214 (2014) 402– 408 403

Table 1Chemical composition of base metal.

Materials Chemical composition (wt.%)

C Mn Si P S Cr

AISI 201 0.05 7.41 0.58 0.01 0.002 17.2

Table 2Parameter of welding.

Specimens Welding speed(mm/s)

Current (A) Voltage (V) Heat input(kJ/mm)

A (1.5 mm/s) 1.5 85 15 ± 1 0.850

simipeaopairpss

2

2

Tssapp

B (2.5 mm/s) 2.5 95 13 ± 1 0.494C (3.5 mm/s) 3.5 110 11 ± 1 0.345

howed that the mean grain size in the weld metal increased withncreasing hydrogen content, which resulted in increase in the weld

etal penetration depth and its width. Kumar and Shahi (2011)nvestigated the effect of varying heat inputs on the mechanicalroperties of weld metal the austenitic steels and found that as arcnergy increased, hardness of weld metal and the HAZ decreasednd width of the HAZ increased. Muthupandi et al. (2003) reportedn the effect of weld chemistry and heat input on the structure androperties of duplex stainless steel welds using autogenous-TIGnd electron beam welding process. The results showed that chem-cal composition exerts a greater influence on the ferrite–austeniteatio than the cooling rate. Shanping et al. (2009) reported in theiraper that small addition of oxygen content to the He–Ar mixedhielding could significantly change the weld shape from a widehallow type to a narrow deep one.

. Experimental material and procedure

.1. Material and welding procedure

The base metal for this study was AISI 201 stainless steel.heir chemical composition was listed in Table 1. Dimensions oftainless steel plate for welding were 150 mm × 100 mm × 2 mm. A

quare butt joint was prepared. The welding was carried out by anutomatic gas tungsten arc welding (GTAW), of which the weldingarameters were exhibited in Table 2. Other details related to therocess and procedures used in the present work include: Type

Fig. 1. Schematic illustration of the speci

Ni Mo Cu Al N Fe

2 3.12 0.009 2.13 0.019 0.28 Bal.

and size of the non-consumable for the joints investigated in thisstudy tungsten electrode = EWTh2 (Thoriated tungsten) of 2.4 mmdiameter, Nozzle size = 8 mm, Shielding gas flow rate of industri-ally pure Argon = 10 L/min and backing gas = 9 L/min, Polarity = DCelectrode positive. After welding, the specimens were cooled downto room temperature in laboratory. All the welds were examinedunder a stereo microscope. The widths of weld metal on face androot sides were determined by metallographic method.

2.2. Metallography

To examine the microstructural of the weldment, correspond-ing to each welding speed combination, specimens were machinedout from the weld pads as shown in Fig. 1. The microstructure, thewelded samples were mounted by molding epoxy, polished by SiCpaper, followed by 0.3 �m Al2O3 powders, and then electrolyti-cally etched in 10 g oxalic acid mixed with 100 ml distilled waterat a voltage of 6 V according to ASTM E407-07 specification. Themicrostructures of different zones of interest like weld metal, HAZand fusion boundary under different welding speed combinationswere viewed and captured with an optical microscope coupled withan image analyzing software. The macrostructures, after polishingand macroetching the cross sections of the joints were capturedwith the help of image analysis software coupled with a stereo-zoom microscope at a magnification of 5× to facilitate measuringof the details like cross sectional areas of the face and root of weldmetals.

2.3. Mechanical test

A Vickers hardness tester with a load of 2.942 N was used to mea-sure the hardness. Measurements were conducted on base metal,

heat affected zone (HAZ), weld metal (WM), heat affected zone(HAZ) and base metal. Thirty different testing points were mea-sured for specimen in each condition. For transverse tensile test,the sample was cut by aligning its main axis perpendicular to the

men sampling from the weld pads.

404 W. Chuaiphan, L. Srijaroenpramong / Journal of Materials Processing Technology 214 (2014) 402– 408

f the

wisb

2

smmecamiAt(ap

3

3

awowp

wbawrho

3

mwi

ftli

which in turn allow lesser time for the dendrites to grow, whereas atlow welding speed (high heat input), cooling rate is slow which pro-vides ample time for the dendrites to grow farther into the fusionzone.

Fig. 2. Specifications o

eld bead according to ISO 4136:2001(E) specification. The spec-men included weld metal, HAZ on both sides, and base metals ashown in Fig. 2. Fracture of specimen due to tension was observedy macroscopic method.

.4. Corrosion test

Potentiodynamic method was used to investigate the corro-ion behavior of weld metals. The welded samples including weldetals were cut to dimensions of 10 mm × 10 mm × 2 mm and thenounted by molding epoxy. They were polished with 600 grit

mery papers and further rinsed in distilled water, ultrasonicallyleaned by alcohol and then dried in air. A polymeric coating waspplied to cover the sample surface, except the area on the weldetal of 19.63 mm2. In the test, that area was exposed to the test-

ng solution where the sample was served as a working electrode. platinum wire was used as a counter electrode. A reference elec-

rode was a saturated calomel electrode (SCE). The testing solutionsynthetic sea water) was 3.5 wt.% NaCl aqueous solution at 27 ◦Cccording to the ASTM D1141 Standard. The sweeping rate of theotential was 1 mV/s.

. Results and discussion

.1. Weld bead shape

The experiment was conducted by varying the welding speednd using pure argon as shielding gas. It was found that use theelding speed lower than 1.5 mm/s, the weld defect was in the form

f excess penetration. And the welding speed faster than 3.5 mm/sas applied, there existed weld defect in the form of incompleteenetration.

The complete weld bead was obtained when the welding speedas in the range from 1.5 mm/s to 3.5 mm/s was observed weld

ead shape as shown in Fig. 3. Table 3 presents the width of facend root of weld metal produced using different welding speeds. Itas found that increasing welding speed reduced width of face and

oot weld metals. This was due to the lower heat input when theigher welding speed was applied, which is similar to the resultsf Nouri et al. (2007), Jaung and Tarng (2002) and Kim et al. (2003).

.2. Microstructure

The microstructure of the austenitic stainless steel AISI 201 baseetal is shown in Fig. 4. It was observed that the austenite grainsith twins were as a typical microstructure of stainless steel. Sim-

lar result is reported by Wichan and Loeshpahn (2012).Optical micrographs showing the microstructures of weld zone,

usion boundary and HAZ for different welding speed combina-ions are presented in Figs. 5–7. The measured values of dendriteengths and inter-dendritic spacings for these joints are mentionedn Table 3. It is observed from these optical micrographs that as

tensile test specimen.

welding speed increases, the dendrite size and inter-dendritic spac-ing in the weld metal reduced, supported these results by Kumarand Shahi (2011), Nowacki and Rybicki (2005) and Shyu et al.(2008). This dendrite size variation can be attributed to the factthat at high welding speed (low heat input), cooling rate is rela-tively higher due to which steep thermal gradients are establishedin the weld metal (Kumar and Shahi, 2011; Muthupandi et al., 2003)

Fig. 3. Weld metal on face side and on root side of weld metals produced usingdifferent welding speed: (a) welding speed 1.5 mm/s, (b) welding speed 2.5 mm/sand (c) welding speed 3.5 mm/s.

W. Chuaiphan, L. Srijaroenpramong / Journal of Materials Processing Technology 214 (2014) 402– 408 405

Table 3Macro and microstructure of weld metals.

Specimens Macrostructure details Microstructure details

Width of face weld (mm) Width of root weld (mm) Dendrite length in the weld zone (�m) Interdendrite spacing (�m)

A (1.5 mm/s) 6.4 5.1 198.67 20.11B (2.5 mm/s) 5.5 4.5

C (3.5 mm/s) 4.2 3.6

Fig. 4. Microstructure of AISI 201 base metal.

Fig. 5. Microstructure of weld metals produced by welding speed

Fig. 6. Microstructure of weld metals produced by welding speed

158.96 12.95102.21 8.44

3.3. Microhardness

Microhardness profile across the weld metals produced bywelding speed 1.5, 2.5 and 3.5 mm/s are shown in Fig. 8. From thisprofile it is observed that as the indentor traverses outwards (par-allel to the base plate surface) from the center of the weld/fusionzone toward the fusion boundary, microhardness increases from230 to 256 HV for welding speed 1.5 mm/s, 251 to 277 HV forwelding speed 2.5 mm/s and 258 to 280 HV for welding speed3.5 mm/s welded joint. From these results, the possible reason isassociated with welding heat input, because the welding speed1.5 mm/s has a heat input higher than that the welding speed 2.5and 3.5 mm/s, respectively, as shown in Table 2. Further analysisshowed that the welding speed 1.5 mm/s has a result in a slowercooling rate than the welding speed 2.5 and 3.5 mm/s, respectively.The ferrite–austenite transformation in this region occurs par-tially during solidification with the action of weld thermal cycles,

because there is sufficient time for the diffusion of alloying elementchromium throughout the ferrite phase; similar result is reportedby Wang et al. (2011). As a result, the ferrite-to-austenite trans-formation ratio decreases as a function of increased heat input,

1.5 mm/s: (a) weld metal and (b) fusion boundary and HAZ.

2.5 mm/s: (a) weld metal and (b) fusion boundary and HAZ.

406 W. Chuaiphan, L. Srijaroenpramong / Journal of Materials Processing Technology 214 (2014) 402– 408

speed

m3vbcithsadfwoi3wfpatteatlwftsw

Fd

percentage elongation decreases with increasing welding speed.Table 3 shows the microstructural details of the weld metal in

Fig. 7. Microstructure of weld metals produced by welding

ore austenite phase is generated in welding speed 1.5, 2.5 and.5 mm/s, respectively, during welding. Obviously, the hardnessalue of all weld metals was lower than that of the stainless steelase metal and the HAZ. This was due to the weldments structureontent delta-ferrite phase distribution in austenite matrix, whichn general the hardness of phase delta-ferrite was lower than thathe austenite phase (base metal). In addition, it was noticed thatardness value of weld metals increases with an increasing weldingpeed (1.5 mm/s, 2.5 mm/s and 3.5 mm/s); hardness values werepproximately 230 HV, 251 HV and 258 HV, respectively. It wasue to the high welding speed with low heat input it can be delta-errite in austenite matrix of weld metals decreases. Similar resultas reported by Wichan and Loeshpahn (2013). Fusion boundary

r transition zone encountered while traversing in this directions indicated by a steep rise in the microhardness with value of51 VHN, 365 VHN and 398 VHN, respectively, for 1.5, 2.5 and 3.5elding speed, respectively. High hardness as possessed by the

usion boundary zone (FBZ) in all the joints can be attributed to theresence of partially unmelted grains at the fusion boundary whichre partially adopted as nuclei by the new precipitating phase ofhe weld metal during the solidification stage; this result foundhat in researches of Wichan and Loeshpahn (2012) and Naffakht al. (2009). After reaching this peak value microhardness shows

decreasing trend in the HAZ. In all the joints, HAZ area adjacento the fusion boundary was coarse grained HAZ which possessedow hardness whereas the HAZ area adjacent to the base metal

as fine grained HAZ which possessed high hardness. The reason

or this trend of microhardness in the HAZ of all the joints is thathe area adjacent to the weld/fusion zone experiences relativelylow cooling rate and hence has coarse grained microstructure,hereas the area adjoining the base metal undergoes high cooling

ig. 8. Microhardness profile of weld metal produced by different welding speed atifferent zones (base metal, HAZ and weld metal).

3.5 mm/s: (a) weld metal and (b) fusion boundary and HAZ.

rate due to steeper thermal gradients and consequently has finegrained microstructure, supported this reason by examinations ofNematzadeh et al. (2012), Gharibshahiyan et al. (2011) and Karciet al. (2009). This is evident from the trend depicted by the micro-hardness profile within the HAZ of each of these joints. In generalit is observed from these microhardness studies that hardness fol-lows an increasing trend in the order of weld metal, HAZ, unaffectedbase metal and fusion boundary for all the joints made at differentwelding speed. It is also observed that there is significant graincoarsening in the HAZs of all the joints. Further it is observed fromthe optical micrographs shown in Figs.5b, 6b and 7b that the extentof grain coarsening in the HAZ increases with increase in heat input.

3.4. Tensile properties

The transverse tensile properties of weldment made usingdifferent welding speed conditions have been evaluated in Table 4.In each condition, three specimens have been tested and theaverage tensile strength is obtained to ensure repeatability. Thetensile strength of all weldments made by above mentioneddifferent welding speed had been evaluated and is shown in Fig. 9.The tensile strength of weld joint possessed using welding speed3.5 mm/s is 565 MPa, while those of using welding speed 2.5 mm/sand 1.5 mm/s weld joints are 546 MPa and 526 MPa respectively.It was found that the ultimate tensile strength (UST) increases and

terms of dendrite size and cell spacing, which indicates that hightensile strength and ductility is possessed by the joints at welding

Fig. 9. Fracture of the tensile specimens produced by different welding speed(a) welding speed 1.5 mm/s, (b) welding speed 2.5 mm/s and (c) welding speed3.5 mm/s.

W. Chuaiphan, L. Srijaroenpramong / Journal of Materials Processing Technology 214 (2014) 402– 408 407

Table 4Tensile properties of weld metals.

Specimens Tensile properties Location of fracture Joint efficiency (%)

Ultimate tensile strength (MPa) Percentage elongation (%)

AISI 201 515 40Weld metal 102.7Weld metal 106.0Weld metal 109.7

s(fMtdowapeawr

3

r1dastca

eusfsbbt

Fd

A (1.5 mm/s) 526 31

B (2.5 mm/s) 546 29

C (3.5 mm/s) 565 26

peed 3.5 mm/s, which can be attributed to smaller dendrite sizes102.21 �m) and lesser inter-dendritic spacing (8.44 �m) in theusion zone, where this result is similar to that performed by

ourad et al. (2012) and Wang et al. (2011). Relatively lowerensile strength and ductility are possessed by the joints with longendrite sizes and large inter-dendritic spacing in the fusion zonef the joint welded using low welding speed (1.5 mm/s). Further itas found that all the tensile specimens fractured in the weld metal

s shown in Fig. 9 which indicates that weld metal in all the jointsossessed lower tensile strength than the base metal and thus jointfficiencies [defined as (UTSweldjoint)/(UTSbasemetal) × 100] (Kumarnd Shahi, 2011) of 109.7%, 106.0% and 102.7% were achieved forelding speed 3.5 mm/s, 2.5 mm/s and 1.5 mm/s combination,

espectively.

.5. Corrosion properties

From Table 3, it was found that increasing welding speededuced dendrite size and cell spacing in austenite matrix from98.67 �m to 102.21 �m and from 20.11 �m to 8.44 �m. Theecrease of dendrite size and cell spacing related to the decreasedmount of delta-ferrite content in the weld when higher weldingpeed was applied. It was also possible that higher cooling rate dueo faster welding speed might help suppress the dendrite size andell spacing formation reported by Yousefieh et al. (2011), Kumarnd Shahi (2011).

Fig. 10 shows that the potentiodynamic polarization curvesxhibit the pitting corrosion potential of weld metals producedsing different welding speed. It was found that increasing weldingpeed from 1.5 to 3.5 mm/s shifted the pitting corrosion potentialrom 102 to 338 mVSCE. This might be due to the smaller dendrite

izes and lesser inter-dendritic spacing in the fusion zone producedy faster welding speed, and the pitted area was adjacent to phaseoundary between austenite and delta-ferrite as shown in Fig. 11;hese results are similar to that reported by Wichan and Loeshpahn

ig. 10. Potentiodynamic polarization curves of base metal and weld metals pro-uced by different welding speed.

Fig. 11. Example of pitted area on the weld metal produced using welding speed of3.5 mm/s.

(2012), Somrerk et al. (2012), Jaung and Tarng (2002). However,the pitting corrosion potential of weld metal produced by weldingspeed 1.5 mm/s, it could not raise the pitting corrosion potential upto the same value as that of the AISI 201 stainless steel base metalswas 202 mVSCE.

Thus, using the fastest studied welding speed, 3.5 mm/s, couldpromote the production rate of welding and still keep the den-drite size and inter-dendritic spacing content in the level that wascorrosion resistant.

4. Conclusions

The present work studied the effect of welding speed on themicrostructure, mechanical and corrosion behavior of weldmentAISI 201 stainless steel sheet produced by a gas tungsten arc weld-ing. The following conclusions can be drawn.

(1) The welding speed increases, the width of face and root weldreduced because of the low heat input in the weld pool. Signif-icant grain coarsening is found in the HAZs of all the joints andit is also observed that the extent of grain coarsening decreaseswith welding speed increase.

(2) The dendrite size in the fusion zone is smaller in weldingspeed 3.5 mm/s (high speed) joints than the dendrites in weld-ing speed 2.5 mm/s (medium speed) and 1.5 mm/s (low speed)joints, and it is found that maximum tensile strength and ductil-ity are possessed by the weld joints made using welding speed3.5 mm/s (high speed).

(3) The welding speed increases, the pitting corrosion potential ofweld metal also increases, due to small dendrite sizes and lessinter-dendritic spacing in the fusion zone.

(4) The hardness of the weld metal is lower than that of base metalby all the joints and it is also observed that the hardness valuesof weld metals increase with welding speed increase.

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stainless steels produced by gas tungsten arc welding. Appl. Mech. Mater. 248,395–401.

08 W. Chuaiphan, L. Srijaroenpramong / Journal of M

Based upon the present study it is recommended that weldingpeed 3.5 mm/s (high speed) should be preferred when weldingISI 201 stainless steel using GTAW process because of the reason

hat besides giving good mechanical properties (tensile strengthnd hardness), high corrosion resistance, the size of the weld beadnd the extent of grain coarsening obtained in these weld joints areess.

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