Chapter 7 COMPARISON FSW WELD WITH TIG...
Transcript of Chapter 7 COMPARISON FSW WELD WITH TIG...
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Chapter 7
COMPARISON FSW WELD WITH TIG WELD
7.0 Introduction
Aluminium welding still represents a critical operation due to its complexity
and the high level of defect that can be produced in the joint. The main problems
related to the welding of aluminium are due to its high thermal conductivity, high
chemical reactivity with oxygen, and high hydrogen solubility at evaluated
temperature. All these factors lead defects in the weld bead. If fusion welding is
performed on aluminium alloy in a normal atmosphere, oxidization readily occurs and
this results in both slag inclusion and porosity in the weld, greatly reducing the
strength of the joint. TIG welding is one of the most common method used for
welding aluminium alloy. This method produces good welds, but more recently solid-
state methods for welding the material have been developed, one of these being
friction stir welding. So the comparative study conducted for the welding of
aluminium alloy 6082 using TIG welding process and then compare mechanical and
metallurgical properties of TIG welded joints with the mechanical and metallurgical
properties of FS Welded joints is discussed in this chapter.
7.1 Preparation of material
It is imperative to carry out welding of aluminium alloy sheet of same grade as
was used for friction stir welding. Aluminium alloy plates having dimensions 300 x75
x 6 mm were prepared for joining by TIG process.
7.2 Selection of process parameter and experimentation
It was decided to adopt manual welding technique for preparation of test
pieces as in actual practice, for welding industry. Before welding all the edges were
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thoroughly cleaned mechanically and chemically in order to avoid any source of
contamination like rust, scale, dust, oil, moisture etc. that could creep into the weld
metal and later on, could result possibly into a weld defect. The welding parameters
selected were based on extensive trials runs. It was found that for sheet of thickness of
6 mm, the current rating may be varied from around 80 Amp to 200 Amp. It was
further observed that below 80 Amp, it was difficult to maintain the arc and the joint
obtained was poor having uneven height. The current more than 200 Amp caused
burn through. So based on extensive trial runs a current range from 120 Amp to 180
Amp was selected. This range will give a steady arc with least spatters. So it was
decided to make minimum of four joints within the range of welding current. The
experiments were repeated thrice to reduce experimental error. The photo graphs of
TIG welded specimens shown in the Figure 7.1. Other details related to the process
and procedures used in the present work include:-
Weld joint was prepared by using commercial 4043 filler wire whose diameter
is 2.4 mm. The chemical composition of the filler wire is presented in the Table 7.1.
The commercially available argon was used as shielding gas at flow rate 15 l/min.
The electrode was the commercially available Tungsten EW-Th-2 (Thoriated
tungsten) of 3 mm diameter. Electrode to work angle was 45º.
7.3 Specimen sampling and testing
The specimens for tensile testing, micro hardness testing and microstructural
studies were taken from the weld pads as schematically illustrated in Figure 7.2.
Sample test pieces were prepared for mechanical and metallurgical testing and tests
were conducted as discussed in the chapter 4.
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7.4 Results and discussion
7.4.1 Tensile properties
The transverse tensile strength of all the joints prepared using TIG welding
process at different welding current conditions was evaluated. In each condition three
specimens were tested and the average tensile strength of three specimens and their
corresponding percentage elongations thus obtained are mentioned in Table 7.2. The
photo graph of some tensile test specimens before fracture is shown in Figure 7.3. The
tensile results show that maximum tensile strength of 204 MPa was possessed by the
specimens made using 140 Amp current and minimum tensile strength of 161 MPa
was possessed using 120 Amp welding current. This indicates that there was a 35% to
49% reduction in the strength due to the change in the micro structure. As shown in
Figure 7.5 to 7.8, the micro structures of the weld metal, the dendrite size and cell
spacing, indicate that high tensile strength and ductility was possessed by the joints at
140 Amp current. This can be attributed to smaller dendrite sizes and lesser inter-
dendritic spacing in the fusion zone. Relatively lower tensile strength and ductility
was possessed by the joints with long dendrite sizes and large inter-dendritic spacing
in the fusion zone of the joint welded using higher welding current (180Amp) and
lower welding current (120Amp). The joint efficiencies [defined as (UTS weld
joint)/(UTS base metal) x 100] of 55%, 66%, 59% and 56% were achieved at 120
Amp, 140 Amp, 160Amp and 180 Amp current respectively.
7.4.2 Comparison of tensile strength of FSW and TIG welded joints
The average transverse tensile strength of TIG welded joints is presented in
Table 7.2. The tensile strength of base metal was 310 MPa. The maximum tensile
strength obtained in TIG welded joint was 204 MPa. This indicates 35% reduction in
tensile strength of TIG welded joint. FSW joints showed the highest tensile strength
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of 271 MPa, this indicates 13% reduction in tensile strength. Though the tensile
strength of friction stir weld joints and TIG weld joints was lower than the base metal,
but tensile strength of friction stir weld joints was 22% higher than TIG welded joints.
This suggests that friction stir welded joints were stronger than TIG welded joints.
The elongation of parent metal was 14%. The TIG welded joints showed the
maximum elongation of 6.5%. This indicates that there was a 50% reduction in
ductility in TIG welded joints. The elongation of FSW joints was 9.5%. This indicates
that there was a 30% reduction in ductility in FS weld joints. Though, percentage
elongations of FS welded joints were lower than the base metal, but were 20% higher
than TIG welded joints. The comparative analysis shows that the TIG welding process
has strong influence on the tensile strength and elongation which decreases 35% and
50% respectively in comparison to that of the base material. If FSW was applied the
tensile strength and percentage elongation of the weld decreases 13% and 30%
respectively in comparison to that of the base material. Thus, the tensile strength of
aluminium alloy 6082 was affected by both the welding processes but affect is more
in the TIG as compared with FS welded joints.
7.4.3 Impact toughness of TIG welded aluminium alloy
The charpy test sample method of impact testing does possess certain
advantage, these include ease of preparation, simplicity of test method, and low cost
per test. The results of impact tests of TIG weld aluminium alloy 6082 joints are
presented in Table 7.2. Impact toughness of base material was 14 J. It was observed
that the impact toughness of the TIG welded aluminium alloy joints was lower as
compared to the base metal and varied from 4J to 8 J, by changing the welding current
as shown in the Table 7.2. Impact strength of TIG welded joints was lower due to
larger grain size of the welded joints and precipitate distribution. During the welding,
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liquid films were formed at grain boundaries adjacent to the fusion boundary. These
liquid films lead to the formation of microscopic inter granular cracks which, after
welding may provide path for subsequent brittle inter granular fracture. The variation
in the strength values is mainly due to the formation of these micro cracks. Grains of
the joint welded at 140 Amp current was uniformly distributed and the spacing
between the grains was lower as compared to the other microstructures. It may be the
reason of higher impact toughness of the joints welded at 140 Amp current.
7.4.4 Comparison of Impact strength of FSW and TIG welded joints
Friction stir welds showed a very interesting trend on impact toughness. The
mean results of the Charpy Impact test of FSW and TIG joints carried out at room
temperature are given in Table 7.2. The impact toughness of FSW was greater than
TIG joints and base material. In contrary to most of mechanical properties of welds,
that were either not altered or slightly deteriorated during FSW of AA 6082-T651
alloy, impact toughness was the property which improved significantly. The measured
value of impact toughness base material was 14 Joules, whereas the welds made by
FSW process showed impact toughness values much greater than base material (26 J).
This situation can be explained with the grain refinement of the stirring effect in the
FSW process. The impact toughness of the FSW joint was 48% greater than that of
the parent material but impact toughness of TIG weld joints was 40% lesser than that
of the base metal. This impact toughness difference is related to the weld structures
obtained with FSW and TIG processes. The stirring effect of FSW improves the
microstructure of the weld and increases the resistance to impact.
7.4.5 Micro hardness of TIG welded specimens
The micro hardness survey of TIG welded specimens at different welding
current from cross section is presented in Figure 7.4. In all the weld joints there was a
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hardness loss in the HAZ, fusion line area and weld zone. The average micro hardness
was 48 Hv for 120 Amp current, 58 Hv for 140 Amp current, 53 Hv for 160 Amp
current and 49 Hv for 180 Amp current in the weld zone. While moving from the
weld centre to base metal, an increasing trend in the order of weld metal, HAZ,
unaffected base metal for all the joints made at different welding currents was
observed. In all the joints, HAZ area adjacent to the fusion boundary was coarse
grained which possessed low hardness whereas the HAZ area adjacent to the base
metal was fine grained which possessed high hardness. The reason for this trend of
micro hardness in the HAZ of all the joints was that the area adjacent to the weld zone
experiences relatively slow cooling rate and hence has coarse grained microstructure,
whereas the area adjoining the base metal undergoes high cooling rate due to steeper
thermal gradients and consequently has fine grained microstructure. This is evident
from the trend depicted by the micro hardness survey within the HAZ of each of these
joints.
7.4.6 Comparison of micro hardness of FSW and TIG welded joints
The base metal in its initial condition showed a hardness value of 94 Hv. The
hardness was greatly reduced in the weld region of both the welding processes. This
was one of the reasons for the location of failure of all the tensile test specimens at the
weld region in TIG welding process but in FSW all the tensile test specimens failure
location was TMAZ of advancing side. TIG weld joints showed the highest average
micro hardness of 58 Hv at weld centre. This indicates that there was 40% reduction
in micro hardness in the weld zone due to welding heat. FS weld joint showed highest
average micro hardness of 65 Hv at the weld zone and this indicates that there was
30% reduction in the weld zone. Though micro hardness in both welding processes
was lower than the base metal, but micro hardness of the friction stir weld joint was
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10% higher than TIG weld joints. However friction stir weld specimens showed
higher micro hardness as compared to TIG weld joints and this was due to shear
stresses induced by tool motion which leads to generation of very fine grain structure
which allows partial recovery of hardness. In case of TIG welding, very high
temperature increases the peak temperature of the molten weld pool causing slow
cooling rate, in turn causes relatively wider dendritic spacing in the fusion zone.
These microstructures generally offer lower resistance to indentation and this may be
one of the reason for lower hardness and inferior tensile properties as compared to
FSW joints.
7.4.7 Microstructure of TIG welded specimens
Optical micro graphs of the TIG welded joints showing the micro structure of
fusion boundary along with HAZ, weld metal and heat affected zone, at different
welding currents are shown in Figure 7.5 to Figure 7.8. From the micrographs, it was
observed that there was an appreciable difference in grain size of the weld zone and
HAZ regions with different welding currents. This may be due to the rapid cooling
induced by good thermal conductivity and low thermal capacity of aluminium. The
grain size of the fusion zone and HAZ are influenced by the heat input of the welding
process. In the HAZ, the grains next to the fusion boundary were found to be grown
larger due to the intensive heat and high temperature experienced during welding.
Grain structure at the fusion boundary was very coarse and columnar showing that
epitaxial growth has taken place. Liquation can be seen along the grain boundary in
the region close to the fusion boundary. Fusion zone shows equiaxed grain structure
consisting of grains of aluminium solid solution and eutectic mixture and beta phase
along the grain boundary [Koteswara et al., 2008]. The fusion zone of TIG welded
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joints contain dendrites structure and this may be due to the fast heating of base metal
and fast cooling of molten metal due to welding heat [Venugopal et al., 2004].
7.4.8 Comparison of microstructure of FSW and TIG welded joints
Optical micrographs of the base metal and friction stir welded joints are
displayed in Figure 6.43. The base metal contains coarse and elongated grains in the
rolling direction. The weld region of FSW joint contains finer grains compared to TIG
welded joints. The weld region of TIG welded joints shows coarse and elongated
grains normal to the welding direction. However, the size and distribution of
strengthening precipitates are different in TIG welded joints and FSW joints. Fine and
evenly distributed precipitates, observed in friction stir welding were one of the
reasons for higher strength of the joints. The comparative analysis shows that the weld
region of FSW joint contains very fine, equiaxed grains and this may be due to
dynamic recrystallisation that occurred during FSW process [Barcellona et al., 2006].
The weld zone of TIG welded joints contain dendritic structure and this may be due to
fast heating of base metal and fast cooling of molten metal due to welding heat.
7.4.9 Fractographic observations of TIG welded joints
The fractured surfaces of the tensile specimens were analyzed using SEM and
are presented in Figure 7.9 (a) to Figure 7.9 (d). Dimples of varying size and shape
were observed in all the fractured surfaces which indicate that major fracturing
mechanism was ductile. From Figure 7.9 (b) it was observed that fractured surface of
the specimen at 140 Amp current contains a large population of small and shallow
dimples which was indicative of its relatively high tensile strength and ductility. From
Figure 7.9 (c) and Figure 7.9 (d) it was observed that as heat input increases, coarse
and elongated dimples are observed. It is also observed that small dimples are
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surrounded by the large ones in all the specimens and a small quantity of tearing ridge
is also present
7.4.10 Comparison of fractograph of FSW and TIG welded joints
The fracture surface of tensile test specimens, as observed under the
Scanning Electron Microscope (SEM) are displayed in Figure 5.50 and Figure 7.9 for
FSW and TIG joints. The fractrography consists of dimples, indication the failure of
the tensile specimen in a ductile manner under the action of tensile loading both in
TIG welding process and FS welding process. An appreciable difference exists in the
size and shape of the dimples with respect to welding processes. The dimple size has
directly proportional relationship with strength and ductility. If the dimple size is
finer, then the strength and ductility of the respective joint is higher. Coarse dimples
are seen in TIG joint and fine dimples in FSW joint. Since fine dimples are
characteristic feature of ductile failure, FSW joints have shown higher ductility as
compared to TIG joints. So the fine dimples in FSW are the reason of higher strength
properties as compare to TIG welded joints.
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Table 7.1: Chemical composition of the filler wire 4043
Si Fe Cu Mn Mg Cr Zn Ti Balance
4.5-6.0 0.8 0.3 0.05 0.05 0.0 0.10 0.20 Al
Table 7.2: TIG welding process parameters and experimental results
Specimen
Designation
Current
(Amp)
Gas flow
{lit/min)
Tensile strength
(MPa)
Impact
toughness (J)
A1 120 15 166 6
A2 140 15 205 8
A3 160 15 185 5
A4 180 15 174 4
Figure 7.1: Photographs of TIG welded specimens
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Figure 7.2: Schematic illustration of the specimen sampling from the weld pads.
Figure 7.3: Photographs of some tensile test specimens of TIG welded joints before
fracture
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Figure 7.4: Micro hardness profile showing micro hardness of different zones of the
weld joints at different welding currents
40
50
60
70
80
90
100
-20 -15 -10 -5 0 5 10 15 20
Mic
ro h
ard
ne
ss (
Hv)
Distance from the weld centre line (mm)
120 Amp 140 Amp 160 Amp 180 Amp
BM HAZ Weld metal HAZ BM
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(a) Fusion zone (b) weld bead
(c) HAZ
Figure 7.5: Optical micrograph showing microstructure of TIG welded specimen (a)
Fusion boundary (b) centre of the weld (c) HAZ ( 120 Amp, at 200X)
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(a) Fusion zone (b) weld bead
(c) HAZ
Figure 7.6: Optical micrograph showing microstructure of TIG welded specimen (a)
Fusion boundary (b) centre of the weld (c) HAZ (140 Amp, at 200X)
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(a) Fusion zone (b) Weld bead
(c) HAZ
Figure 7.7: Optical micrograph showing microstructure of TIG welded specimens (a)
Fusion boundary (b) centre of the weld (c) HAZ (160 Amp, at 200X)
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(a) Fusion zone (b) Weld bead
(c) HAZ
Figure 7.8: Optical micrographs showing microstructure of TIG welded specimens (a)
Fusion boundary (b) centre of the weld (c) HAZ (180 Amp, 200X)
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Figure 7.9(a): SEM fractograph showing fracture surface of tensile test TIG welded
specimen (120) Amp current
Figure 7.9 (b): SEM fractograph showing fracture surface of tensile test TIG welded
specimen (140) Amp current