Effect of shielding gas composition on Ferrite Number, Mechanical & Microstructural Properties of GTAW deposited Austenitic Stainless Steel weld metal

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Mohan, Asst. Manager, Product Development (TDC – Welding Consumables)

Dinesh Giri, Team Leader, Product Development (TDC – Welding Consumables)

Ninad Thigale, Team Leader, Product Development (TDC – Welding Consumables) 

Hariganesh, Team Leader, Product Development (TDC – Welding Consumables)

Somnath Chakravarty, Head Of Department, Product Development (TDC – Welding Consumables)

Ador Welding Ltd-Pune

Abstract 

The stainless steels have been the primary alloys used for building and construction, Chemical industry, Oil & Gas and industrial applications. Most commonly used alloys types are 308, 316 and their low carbon versions types 308L and 316L. They have good fabricability, resistance to atmospheric corrosion and resistance to many organic and inorganic compounds. Austenitic stainless steels are commonly welded with 100%Ar in TIG process. At the end, weld metal contains some amount of ferrite to reduce the hot cracking. In shielding gas 2%N2 addition will be effect the ferrite formation and it concerns have emerged about possible effects on the mechanical properties of the weld metal. ER308L and ER316L austenitic stainless steels filler wire were used in this work and welded by Tungsten inert gas welding process. The properties of undiluted weld metal are evaluated with addition of nitrogen in shielding gas. This paper reports on tensile strength, impact toughness properties (at -196°C and -101°C), ferrite number, lateral expansion and microstructure of ER308L and ER316L weld deposited using 100%Ar and 98%Ar+2%N2 shielding gases. The undiluted weld metal microstructure was examined before and after nitrogen addition in shielding gases under optical microscope. The reduction of ferrite content by nitrogen was analyzed with WRC and Feritscope. The effect of 2%N2 addition in shielding gas was discussed.

Keywords: TIG welding, Austenitic stainless steel, Shielding gases, Microstructure, Tensile properties

  • Introduction 

Austenitic stainless steel is widely used among stainless steel group because of the properties of easily weldable and formable. They are most easily recognized as nonmagnetic. A literature survey indicates austenitic stainless steel used as heavy structures in ship building, pressure vessels and heavy vehicles,  in  order  to  meet  the  requirement  of  good  impact  properties  and adequate  strength  [1]. Austenitic stainless steel had less than 0.15% carbon, 16 to 28% chromium, 9 to 30 % nickel & 3 % Molybdenum. Chromium reacts with the atmosphere oxygen and form passive layer of chromium oxide. It prevents the further oxidation and nickel is enhancing the property of the toughness at cryogenic temperature. It can be divided rather loosely into three groups: common chromium-nickel (300 series), manganese-chromium-nickel-nitrogen (200 series) and specialty alloys. The most widely used austenite steel electrode is the E308L, E316L also known as 18/9, 18/12/3 for its composition of 18% chromium, 9% nickel and 18% chromium, 12% nickel & 3% Molybdenum. Austenitic stainless steel weldments are solidified as austenite as matrix and small amount of ferrite [2],[3]. This ferrite was act as barrier to hot cracks, small fissures during solidification of weld zone. [4]. Cooling rate of the weld metal  have some influence on the ferrite formation, but chemical composition have more influence on changing ferrite level in weldment compared to heat input [5]. Nickel, manganese, copper carbon and Nitrogen are austenite stabilizers. Comparatively nitrogen is one of the most influencing elements of ferrite formation. 

Table 2.1 Composition of  ER308L and ER 316L filler wire

 

Grade %C %Cr %Ni %Mo %Mn %Si %P %S %Cu %N
ER308L 0.025 20.23 9.45 0.017 1.62 0.45 0.029 0.011 0.146 0.06
ER316L 0.019 18.40 11.22 2.29 1.63 0.41 0.028 0.007 0.424 0.05

Table 2.2 Composition of weld metal with 100%Ar shielding gas

Grade %C %Cr %Ni %Mo %Mn %Si %P %S %Cu %Nb %N
ER308L 0.016 20.48 9.24 0.03 1.39 0.37 0.02 0.006 0.10 0.04 0.08
ER316L 0.022 18.35 10.89 2.23 1.48 0.31 0.02 0.003 0.10 0.01 0.06

 

Table 2.3 Composition of weld metal with 98%Ar+2%N2 shielding gas

Grade %C %Cr %Ni %Mo %Mn %Si %P %S %Cu %Nb %N
ER308L 0.015 19.28 9.29 0.045 1.45 0.37 0.02 0.007 0.11 0.035 0.33
ER316L 0.019 17.09 11.04 2.28 1.43 0.26 0.02 0.002 0.10 0.004 0.36

 

Table 2.4 Welding parameters

Shielding gas Grade Current(A) Voltage(V) Average       speed

(mm/min)

Average Heat Input

(KJ/mm)

Gas flow

(lit/min)

100%Ar ER308L 245-246 14.5-15.6 108 2.1 10-15
ER316L 244-245 16.8-17.3 110 2.3 10-15
98%Ar+2%N2 ER308L 243-244 14.6-16.3 105 2.2 10-15
ER316L 234-237 15.8-17.2 114 2.1 10-15

  • Experimental Work


ER308L and ER316L TIG filler rods were selected with two different shielding gases.

                                1.100%Ar

                                2.98%Ar + 2%N2

Table 2.5 Base material chemical composition (IS 2062)

%C %Mn %S %P %Si
0.13 0.93 0.015 0.021 0.38

GTAW is a Non consumable electrode process, so that the 308L and 316L filler materials are fed manually. 2.40mm filler wire is used for both Stainless steel welding. Welding parameters like root gap, Bevel angle, Interpass temperature, Back plate and Base plate dimensions are selected as per the ASME section II C – SFA 5.4. Because of Nitrogen addition in shielding gas 2% Thoriated Tungsten electrode was used to reduce the erosion of electrode. Commercially using shielding gas 100%Ar was welded with 2% Zirconated electrode. 

The base material used in the present investigation was IS 2062 grade-b plates basically low carbon steel of sizes 350mm X 125mm X 15mm.



Fig 2.1 Line diagram weld assembly

 


Fig 2.2 Assembly after welding

Backing plate of size 370mm X 30mm X 6.5mm. We have added buttering layer of 3mm of ER308L for 2 assemblies and ER 316L for 2 assemblies. By adding layer of buttering of weld metal on the base plate, dilution of base material into weld material was eliminated. Buttering layer model diagram is given in Fig 2.1. Plates are welded in flat (1G) position and DCEN polarity was used.

 

  1. Results and Discussion

3.1 Tensile strength of weld metals

 

Table 3.1 Tensile strength of  ER308L weld metal

S.No Properties Weld metal with

100%Ar shielding gas

Weld metal with

98%Ar+2%N2 shielding gas

1 Tensile strength (MPa) 670 684
2 Yield strength (MPa) 505.6 550
3 %Elongation

(50mm gaugelength)

39.26 43.60

 

The effect of shielding gases on mechanical properties is listed on table 3.1 & 3.2. it clearly shows a progressive increase on weldmetal ultimate tensile strength, yield strength & elongation after 2%N2 addition shielding gas. Added nitrogen content increase austentite phase on  weld metal and it increase ductility and nitrogen atom sit interstitial positions of the weld matrix crystal lattice  and it strengthen weld metal[9]. Because of the above solid solution strengthening UTS & Yield strength of weld increased after 2%N2 addition shielding gas.

 

Table 3.2 Tensile strength of  ER316L weld metal

S.No Properties Weld metal with

100%Ar shielding gas

Weld metal with

98%Ar+2%N2 shielding gas

1 Tensile strength (MPa) 602.5 663
2 Yield strength (MPa) 475 565
3 %Elongation

(50mm gauge length)

38.32 45.83

3.2 Impact strength of weld metals

 

Table 3.3 Impact strength of  ER308L weld metal with 100%Ar

S.No Impact energy

at -101°C (Joules)

Lateral expansion

at -101°C (mm)

Impact energy

at -196°C (Joules)

Lateral expansion

at -196°C (mm)

1 92 1.40 42 0.62
2 94 1.36 42 0.59
3 88 1.09 46 0.61
4 78 1.14 52 0.63
5 88 1.04 42 0.56

 

Table 3.4 Impact strength of  ER316L weld metal with 100%Ar

S.No Impact energy

at -101°C (Joules)

Lateral expansion

at -101°C

Impact energy

at -196°C (Joules)

Lateral expansion

at -196°C

1 138 1.81 86 1.21
2 154 2.02 82 1.16
3 146 1.91 104 1.51
4 146 1.99 76 1.15
5 146 1.92 74 1.06

Nitrogen addition promotes the austenite phase & reduces the ferrite content in the weld metal of austenitic stainless steel. This again promotes impact toughness[8]. Impact test results are listed on table 3.3 to 3.6.Lateral expansion is also increased when welded with 2% Nitrogen addition. Lateral expansion is directly proportional to elongation. 

 

Table 3.5 Impact strength of ER308L weld metal with 98%Ar+2%N2

S.No Impact energy

at -101°C (Joules)

Lateral expansion

at -101°C

Impact energy

at -196°C (Joules)

Lateral expansion

at -196°C

1 90 1.55 50 1.14
2 120 1.97 46 0.90
3 96 1.58 50 1.10
4 102 1.57 46 1.10
5 122 2.05 50 1.22

Table 3.6 Impact strength of ER316L weld metal with 98%Ar+2%N2

S.No Impact energy

at -101°C (Joules)

Lateral expansion

at -101°C

Impact energy

at -196°C (Joules)

Lateral expansion

at -196°C

1 134 1.75 82 1.01
2 160 2.06 84 1.04
3 158 1.85 102 1.50
4 162 1.98 94 1.40
5 149 1.82 86 1.08

 

3.3 Hardness values of weld metals

Hardness values are slightly increased after 2%N2 addition in shielding gas. Because of the sold solution strengthening Hardness on the weld metal was increased.

 

Table 3.7 Hardness of weld metals with different shielding gas

Grade Hardness with 100%Ar Hardness with 98%Ar+2%N2
ER308L 94,92,92 HRB 95,96,95 HRB
ER316L 87,88,87 HRB 88,89,89 HRB

 

3.4 Ferrite number analysis

Nitrogen content of weld metal was identified in both shielding gas weld metal with chromatography analysis. It results high nitrogen content in 98%Ar+2%N2 weld metal than the 100%Ar weld metal. Nitrogen content of wire also measured.

 

Table 3.8 Nitrogen values comparison

Grade Wire 100%Ar 98%Ar+2%N2
ER308L 0.06 0.08 0.33
ER316L 0.05 0.06 0.36

 

Table 3.9 Ferrite number

Shielding gas Filler wire WRC

(FN)

Ferritscope

(FN)

100%Ar ER308L 13 4.5
ER316L 8 3.5
98%Ar+2%N2 ER308L 0 0.1
ER316L 0 0.16

3.5 Microstructure analysis

ER308L weld microstructure with 100%Ar showing Austenite & vermicular Ferrite phases, which the ferrite number of weld metal is about 4.5 FN. It is well known that a small amount of ferrite in austenitic stainless steel weld metal is very effective for the prevention of hot cracking. Austenite is the bright phase and Ferrite is the Dark phase in microstructure color morphology. Ferrite morphology varies depending on the solidification mode.

                        500X

1000X


ER308L with 100%Ar


ER308L with 98%Ar+2%N2

Fig 3.1 ER308L with different shielding gases

500X                                                                1000X

ER316L with 100%Ar

 

 


ER316L with 98%Ar+2%N2

Fig 3.2 ER316L with different shielding gases

 

As the Cr/Ni ratio increases, the total ferrite increases and lacy ferrite will form. The Lacy ferrite was formed only in the ferrite phase primary solidification mode [7].

After 2%N2 addition in shielding gas Ferrite percentage was reduced [6]. Fully austenitic weld metal was observed. But the bottom of weld bead is contains very low amount of ferrite.  During solidification the transformation of eutectic ferrite to austenite immediately subsequent to weld metal solidification eliminates grain boundary pinning and allows considerable austenite grain growth after solidification is complete. So the ferrite formation is entirely suppressed by the nitrogen.

 

4.Conclusions

 

From this investigation, following conclusions are derived,

 

  • At 2% nitrogen in weld metal, Tensile strength and yield strength is increased. Compare to tensile strength, the yield strength was drastically increased and this is probably the evidence of solid solution strengthening effect of nitrogen. By the crystal lattice distortion due to nitrogen atoms in interstitial positions, markedly increase the yield strength without an accompanying loss in fracture toughness.
  • Both impact toughness and lateral expansion are increased while the amount of nitrogen content increased in the weld.
  • Results of lateral expansion and ductility shows both are directly proportional
  • Increased nitrogen contents promote weld metal solidification as primary austenite 

 

References

1)  E. R. SZUMACHOWSKI AND H. F. REID , Cryogenic Toughness of SMA Austenitic Stainless Steel Weld Metals Introduction Part I —Role of Ferrite, THE WELDING JOURNAL, NOVEMBER 1978.

2)  G. L. LEONE AND H. W. KERR, , The Ferrite to Austenite Transformation in Stainless Steels, Welding research supplement, JANUARY 1982-13s.

 

3)  V.  P.  KUJANPAA, S.  A.  DAVID AND C.  L.  WHITE, , Formation of Hot Cracks in Austenitic Stainless Steel Welds—Solidification Cracking, Welding research supplement, AUGUST 1986 –203s.

 

4)  C. D. LUNDIN, W. T. DELONG AND D. F. SPOND, , Ferrite- Fissuring Relationship in Austenitic Stainless Steel Weld Metals, Welding research supplement, august 1975, 241-S.

 

5)  V. Muthupandi, , Effect of weld metal chemistry and heat input on the structure and properties of duplex stainless steel welds, Materials Science and Engineering, A358 (2003).

 

[6] R.K.Okagawa, R.D.Dixon,The Influence of Nitrogen from Welding on Stainless Steel Weld Metal Microstructures, welding research supplement Pages 204-209, August 1983

 

[7] H.Inoue, T.Koseki, S.Ohkita, Formation mechanism of Lacy and Vermicular ferrite in austenitic weld metals,Science and technology of welding and joining, 2000, Vol 5, No.6

 

 [8] D.T.Read, H.I.Mchenry, Metallurgical Factors Affecting the Toughness of 316L SMA Weldments at Cryogenic Temperatures, Welding research supplement, April 1980, Pages 404-412

of AIME 

 

[9] K. Migiakis Æ G. D. Papadimitriou, Effect of nitrogen and nickel on the microstructure and mechanical properties of plasma welded UNS S32760 super-duplex stainless steels, Journal of Materials Science, April 2009, Pages 6372–6383.