[Kumar, 3(10): October, 2014]
ISSN: 2277-9655
Scientific Journal Impact Factor: 3.449
(ISRA), Impact Factor: 2.114
IJESRT
INTERNATIONAL JOURNAL OF ENGINEERING SCIENCES & RESEARCH
TECHNOLOGY
Friction Stir Welding Processes: A Review
Naveen Kumar *, Manjit Singh, Amit Handa
M.Tech Research Scholar, RIMT College of Engineering & Technology, Mandigobindgarh, Punjab,
India
Associate Professor, RIMT College of Engineering & Technology, Mandigobindgarh, Punjab, India
Associate Professor, RIMT College of Engineering & Technology, Mandigobindgarh, Punjab, India
Abstract
*
Friction Stir Welding is a novel green solid state joining process particularly used to join high strength
aerospace aluminum alloys which are otherwise difficult to weld by conventional fusion welding. Unlike other solid
state joining technique, in Friction stir welding a third body contact by tool will generate the additional interface
surfaces and finally all the surfaces are coalesced with each other by applied pressure and temperature and form
solid state weld. This review paper addresses the overview of Friction stir welding which includes the basic concept
of the process, microstructure formation, influencing process parameters, typical defects in FSW process and some
recent applications. The paper will also discuss some of the process variants of FSW such as Friction Stir
Processing, Friction Welding processes
Keywords: Friction stir Welding; dissimilar Al alloy; Al and cu alloys ; AISI 1021 steels
Introduction
Friction Stir Welding (FSW) is a solid state
material which can lead to the formation of unwanted
joining process that utilizes the heat produced
and detrimental intermetallic compounds often
between the material and a non-consumable rotating
present during the welding of dissimilar metals such
pin to join the desired materials or work pieces. This
as Magnesium and Aluminium. FSW is able to
rotation causes a plasticized region of material to
successfully join materials such as aerospace high
rotate about the tool. As the tool is moved through
alloy aluminium (2000 and 7000series), magnesium,
the material, the material on the leading edge enters
metal matrix composites, and dissimilar metals.
the plasticized region and is swept around to the back
Thermal heating and mechanical stirring originated
of the tool where the lagging material is left to form a
by the rotational tool with probe join two pieces of
solid joint. In order to obtain a properly consolidated
alloy plates. For light metal alloys, welding by FSW
weld it is also necessary for there to be a shoulder
is expected in transport industries due to the high
above the pin, typically 1.5-2 times the diameter of
quality of the joint because of the low temperature
the pin, which rides along the surface of the work
processing without melting. It is considered by many
piece in intimate contact, while pin is submerged in
to be the most significant development in metal
work piece providing the stirring and heating.It is
joining in a decade.[1]
important to note that while the process is named
Friction Stir Welding, friction is not main source of
energy for the weld but rather the shearing of the
material at the interface between the tool and the
material is.FSW presents numerous advantages over
conventional fusion welding techniques such as
eliminating the need for a shielding gas, requiring
less energy per weld, and the lack of a flame or arc
making it safer in the work place. Another advantage
of FSW is its ability to join materials that are
extremely difficult, or impossible to weld with 2
conventional fusion techniques. Also, since FSW is a
solid state process there is no melting of the parent
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ISSN: 2277-9655
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Fig.1. Schematic diagram of the Friction Stir Welding(1)
Friction stir welding
characteristics
Research studies and
A. Friction stir Welding of dissimilar aluminium
alloy.
Koilraj et al [2] optimized FSW process with respect to
tensile strength of the welds and the optimum
settings.Furthermore, the optimum values of the
rotational speed, transverse speed, and D/d ratio are 700
rpm, 15 mm/min and 3 respectively. In addition, they
concluded that the cylindrical threaded pin tool profile
was the best among the other tool profiles considered.
Palanivelet al [3] examined the influence of tool
rotational speed and pin profile on the microstructure and
tensile strength of the dissimilar friction stir welded
aluminum alloys AA5083-H111 and AA6351-T6. The
welds fabricated using straight tool profiles had no
defects while the tapered tool profiles caused a tunnel
defect at the bottom of the joints under the experimental
considered conditions. Furthermore, three different
regions namely unmixed region, mechanically mixed
region and mixed flow region were observed in the weld
zone [3]. Furthermore, Palanivel et al [4] joined
AA5083-H111 and AA6351-T6 using tool rotational
speed of 950 rpm and straight square pin profile which
resul ted into obtaining the highest tensile strength of
273 MPa. Moreover, the variation in the tensile strength
of the dissimilar joints was attributed to material flow
behaviour, loss of cold work in the HAZ of AA5083,
dissolution and over aging of precipitates of AA6351 and
formation of macroscopic defects in the weld zone. Da
Silva et al [5] investigated the mechanical properties and
microstructural features as well as the material flow
characteristics in dissimilar 2024-T3 and 7075-T6 FSW
joints. The welds were produced at fixed feed rate
(254 mm/min) varying the rotation speed in three levels
(400, 1000 and 2000 rpm).Da Silva et al [5] clearly
stated that, typical microstructural features of FSW
welds such as SZ, TMAZ and HAZ regions were seen. A
sharp transition from the HAZ/TMAZ to the SZ has been
observed in the advancing side; while in the retreating
side, such transition is moregradual. They found that the
minimum hardness value of naturally aged samples in
the HAZ at the retreating side was about 88% of 2024T3 base material. Furthermore, 96% ofefficiency in
terms of tensile strength was achieved using 1000 rpm
rotational speed. Fracture of the weld specimens
occurred in the HAZ at the retreating side (2024T3).Aval et al [6] investigated the microstructures and
mechanical propertiesin similar and dissimilar friction
stir welding of AA5086-O andAA6061-T6 using
thermomechanical modeland experimental observations.
They concluded that the hardness in AA5086 side mainly
depends on recrystallization and generation of fine grains
in the weld nugget whereas hardness in the AA6061 side
varies with the size, volume fraction and distribution of
precipitates in the weld line and adjacent heat affected
zone as well as the aging period after welding. Aval et al
[6] further observed grainrefinement in the stirred zone
for all their samples; however, the finer grain size
distribution is achieved within the AA6061 side where
higher strain rates are produced. Shen et al [7] in their
investigation on microstructures and electrochemical
behaviors of the friction stir welding dissimilar welds
observed that the microstructure of the FSW weld consist
of finer grains in comparison to that of the parent
material.Furthermore, intense plastic deformation and
frictional heating during welding resulted in the
generation of a dynamically recrystallized fine grained
microstructure within the stirred zone. Tran et al [8]
investigated the behavior of friction spot welding
between AA 5754-O and AA 7075-T6.They showed
that, under cyclic loading conditions, the micrographs
show that the 5754/7075 and 7075/5754 welds in crosstension specimens mainly failed from the fatigue crack
along the interfacial surface and from the fracture surface
through the upper sheet material[8].Jun et al [9]
investigated residual strains in dissimilar friction welds.
The research was conducted using the Eigen strain
Reconstruction Method in FSW between AA5083 and
AA6082-T3.They further observed that full-field residual
stress–strain distributions can be reconstructed relatively
easily based on limitedexperimental data sets using
transparent and straight forward FE modeling
framework. Another study was conducted by Ghosh et al
[10], they joined A356 and 6061 aluminum alloys using
FSW under different tool rotation and traversing speeds.
They found that the interface microstructure within the
weld nugget is dominated by the retreating side alloy as
the signature of Si rich particle distribution and it was
evident for all the samples produced. They further
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observed that welds fabricated at the lowest tool
rotational and traversing speed exhibited superior
mechanical properties when compared to the remaining
welds produced.
thickness on the laser peened samples. Recent studies on
friction stir welding of dissimilar aluminum and its
alloys have been reviewed and acomprehensive summary
of the results have been presented
Sundaram et al [11] friction stir welded AA2024-T6 and
AA5083-H321 using five different pin profiles
developed successfully and suitable for the dissimilar FS
welding of aluminum alloys. They further observed that
increasing the tool rotational speed or welding speed led
to the increase in the tensile strength; and it reachesa
maximum value and then decreases. Additionally, the
increase in the tool axial force led to the increase in the
tensile strength of the dissimilar FS welded joints. The
tensile strength decreases after it attains a maximum
value. Muruganandam et al [12] in FS Welding of
dissimilar 2024 and 7075 aluminum alloys, investigated
the microstructures, the results revealed that the process
led to recrystallized grain structure and precipitates
distribution.Moreira et al [13] produced friction stir butt
welds of AA6082-T6 with AA6061- T6. The welds
exhibited intermediate properties and the tensile tests
failures occurred near the weld edge line where a
minimum value of hardness was observed. Furthermore,
microstructural changes induced by the friction stir
welding process were clearly identified. Leitao et al [14]
used AA5182- H111 and AA6016-T4 sheet samples and
joined them using FSW. Welds between both alloys
exhibited a hardness variation consistent with the
microstructure evolution across the TMAZ and no
significant decrease in the hardness was observed for the
welds and its strength efficiency is about 90%. Still, its
ductility seriously decreases relative to the base materials
due to the heterogeneous characteristics of these welds.
Cavaliere et al [15] studied the mechanical and
microstructural behaviour of FSW between AA6082 and
AA2024. They noticed that the vertical force increased
as the travel speed for all the produced joints increases.
They also achieved the best tensile and fatigue properties
for the joints with the AA6082 on the advancing side and
welded with anadvancing speed of 115 mm/min. Leitao
et al [16] joined AA5182-H111 and AA 6016-T4 using
friction stir welding process. They found in the
dissimilar welds the presence of small defects at the weld
root of the dissimilar welds induced rupture of some of
the blanks during the formability tests. Hatamleh and
DeWald [17] joined AA 2195 and AA 7075 and
investigated the peening effect on the residual stresses of
the produced welds. Results showed that the surface
residual stresses resulting from shot peening on both AA
2195 and AA 7075 were higher compared to the laser
peening due to the high amount of cold work exhibited
on the surface from shot peening. Furthermore, high
values of tensile stresses were noticed in the mid-
A. Friction stir welding between aluminium and
copper alloys
The development of laboratory work on the friction
stir welding of dissimilar materials will provide a
good insight on their possible industrial application
and therefore enhance industrial development. Liu et
al [18] observed while welding copper (T2) to AA
5A06 that the distribution between the Copper (Cu)
and Aluminium (Al) has an evident boundary and the
material in the stir zone shows obvious
plasticcombination of both materials. Furthermore,
they observed clearly an onion ring structure in the
stir zone indicating good material flow. Additionally,
they indicated that the metal Cu and Al close to the
copper side in the Weld Nugget (WN) zone showed a
lamellar alternating structure characteristic [18].
However, a mixed structure characteristic of Cu and
Al existed in the aluminium side of the weld nugget
(WN) zone. The stir action of the tool, frictional heat
and heat conductivity of Cu and Al could have
induced the different structures of both sides in the
weld nugget zone. The X-ray diffraction (XRD)
analysis showed that there were no new Cu–Al
intermetallics in the weld nugget zone. Consequently,
the structure of the weld nugget zone was largely
plastic diffusion combination of Cu and Al [18].
However, Xue et al [19] successfully welded
AA1060 and 99.9% pure commercial copper
(annealed), they conducted XRD analysis and their
results revealed the existence of distinct characteristic
diffraction peaks of Al2Cu and Al4Cu9. Hence, they
stated that the Al2Cu and Al4Cu9 were generated
around the larger Cu particles, and for the smaller Cu
particles most of the copper were transformed into
these two intermetallics (IMCs). However, the
microstructures of the nugget zone consisted of a
mixture of the aluminium matrix and Cu particles.
The distribution of the Cu particles with irregular
shapes and various sizes was inhomogeneous in the
nugget zone and a particles-rich zone (PRZ) was
formed near the bottom of the weld [19].
Furthermore, they examined the presence of the
particles in the aluminium matrix of the nugget zone
and attributed that to the stirring action of the tool pin
that worn out the Cu pieces from the bulk copper,
breaking up and scattering them during the FSW
process [19]. AA5083 and commercially pure copper
were joined using FSW by Bisadi et al [20]. They
observed that a very low welding temperature led to
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considerably into the bottom plate while joining 1060
aluminium alloy to commercially pure copper. The
vertical transport of the interface is attributed to the
ring-vortex flow of materials created by the tool pin
threads [25]. At higher welding speeds, less vertical
transport of the interface was observed on the
retreating side [25]. Akinlabi et al [26] investigated
the microstructure of the joint interface of AA 5754
and C11000 copper welds. The mixing of both
materials was observed leading to good metallurgical
bonding at the joint interface. The aluminium rich
region was black/silver while golden yellow showed
copper rich regions. Furthermore, Akinlabi, et al [27]
observed a thickness reduction in the joint interface
but good mixing was achieved in the weld produced
at a constant rotational speed of 600 rpm and feed
rates of 50 and 150 mm/min. They attributed the
reduction in thickness at the joint interfacial regions
to heavy flash observed during the welding process
[27]. In addition, a good material mixing was
achieved in welds produced at lower feed rate due to
high heat generated while the welds produced at
highfeed rates resulted in worm hole defect formation
[27]. On the other hand, Galvao, et al [28] observed
that increasing the heat input, by performing welds
under higher ω/v ratio, resulted in the formation of
mixed material zones with increasing dimension and
homogeneity. Furthermore [28], the morphology of
the mixing zones and the type and amount of the
intermetallic phases, which they found to result from
a thermomechanically induced solid state process, are
also strongly dependent on the welding parameters.
Galvao et al [29] friction stir welded oxygen free
copper with high phosphorous content (Cu-DHP,
R240) and AA 5083-H111. They observed that the
welds performed with the aluminium placed at the
advancing side of the tool were morphologically very
irregular, being significantly thinner and exhibiting
flash formation due to the expulsion of the
aluminium from the weld area. Furthermore, the
aluminium, which is expelled, gave rise to the flash
displayed for the welds performed with aluminium at
the advancing side [29]. It was observed that when
the aluminium plate is located at the retreating side of
the tool, the material was dragged by the shoulder to
the advancing side, where the harder copper plate is
located [29]. In FSW of dissimilar metals, the pin
offset is a very important factor. Agarwal et al [30]
joined AA 6063 and 99.9% pure commercially
copper using FSW. They observed that as the pin
offset is increased there is improper mixing of the AlCu metals that resulted in the tunnelling defect. Singh
et al [31] observed that there were different
microstructure features in the different zones. At the
some defects like channels that showed up at a region
near the sheets interface especially in the Cu sheet.
Also, extremely high process temperature leads to
some cavities appearance at the interface of the
diffused aluminium particles and the copper sheet
material. Additionally, they found that increasing the
process temperature reportedly leads to higher
amounts of copper particles diffusion to the
aluminium sheet, increase in the intermetallic
composition]/’s and a number of micro crackswere
present.On the other hand, Xue et al [20] welded AA
1060aluminium to commercially pure copper. They
identified many defects in the nugget zone at the
lower rotation speed of 400 rpm considered; whereas
at higher rotation speeds of 800 and 1000 rpm, good
metallurgical bonding between the Cu pieces and Al
matrix was achieved. Furthermore, a large volume
defect was observed when the soft Al plate was
placed at the advancing side. They attributed that to
the hard copper bulk material which was hard to
transport to the advancing side during FS welding
[21]. Esmaeili et al [22] joined AA 1050 and
70%Cu–30% Zn brass, the results showed that the
structure of the sound joint at the nugget zone of
aluminium is made up of a composite structure,
consisting of intermetallics and brass particles,
mainly at the upper region of the weld cross section.
Furthermore, a multilayer intermetallic compound
was formed at the interface at rotational speeds
higher than 450 rpm. This layer is mainly composed
of CuZn, CuAl2 and Cu9Al4. Thedistribution, shape
and size of the particles are irregular and
inhomogeneous in the nugget zone of aluminium
[22]. Ouyang et al [23] also conducted dissimilar
FSwelds using AA 6061(T6) to copper. They
demonstrated that the direct FSW of AA 6061 to
copper has been difficult due to the brittle nature of
the intermetallic compounds formed in the weld
nugget. Moreover, the mechanically mixed region in
the dissimilar AA 6061 to copper weld consisted
mainly of several intermetallic compounds such as
CuAl2, CuAl, and Cu9Al4 together with small
amounts of α-Al and a facecentered cubic solid
solution of Al in Cu [23].Abdollah-Zadeh et al [24]
friction stir welded AA 1060 to a commercially pure
copper. They observed intermetallic compounds of
Al4Cu9, AlCu and Al2Cu near the Al/Cu interface,
where the crack can be initiated and propagated
preferentially during the tensile tests. They also
observed that higher rotational speeds increased the
amount of intermetallic compounds formed at the
aluminium / copper interface while low rotational
speed resulted in imperfect joints. Saeid et al [25]
stated that the interface in the central region moved
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weld centre line, mix region of aluminium and copper
were found. Small particles of aluminium and copper
were distributed in the opposite side by the stirring
forces of the tool. The Thermo Mechanically
Affected Zone (TMAZ) is clearly obtained in Copper
but it was not found in aluminium. Thus, in both the
metals, the Heat Affected Zone (HAZ) was not clear
[31]. Ratnesh and Pravin [32] successfully joined AA
6061 and copper by FSW. They produced sound
joints by shifting the centre line of the tool towards
the copper plate on the advancing side. A presence of
a ‘‘transition zone’’ was observed by Guerra et al
[33] while friction stir welding thick AA 6061 plates
with a thin high purity copper foil. This transition
zone was found to be about twice as thick on the
retreating side as it is on the advancing side. They
believed that the material in this zone rotates, but its
velocity decreases from the rotational velocity of the
pin at the inner edge of the transition zone to zero at
its outer edge [33]. Xue et al [34] joined 1060
aluminium alloy and commercially pure copper with
success through friction stir lap welds. They found
that the nugget zone consisted of pure Al material
and a composite structure in the upper and the lower
parts respectively. They found that the Al/Cu
interface was characterised by a thin, continuous and
uniform intermetallic layer, producing a good
interface bonding. Furthermore, good metallurgical
bonding was achieved between the Al matrix and the
Cu particles in the composite structure due to the
formation of a small number of intermetallics [34].
Akinlabi et al [35] observed that the joint interfaces
are characterised by mixed layers of aluminium and
copper as evident in the microstructures resulting
from the heat input into the welds by the stirring
action of the tool during the FSW process.
Furthermore, they observed that the percentage
decrease in the grain sizes increases towards the stir
zones of the welds. LI et al [36] used pure copper and
AA 1350 and successfully joined them through FSW
with the pin offset technique. They found that both
copper and aluminium are greatly refined after FSW
compared to the base materials. No intermetallic
compound was found according to the XRD results.
Esmaeili, et al [37] friction stir welded brass to AA
1050 at different rotation speeds. At low rotation
speeds and due to low levels of heat inputs, no
detectable intermetallic compound was observed. As
the rotation speeds increases, the gradual formation
of
intermetallics
is
initiated
at
the
interface.Additionally, the increase in the rotational
speed resulted in the thickening and development of
intermetallic layers.
A. Friction welding Processes AISI 1021 steel
Handa et al[38] study, an experimental set-up was
designed in order to achieve friction welding of
plastically deformed AISI 1021 steels. Low alloy
steel (AISI 1021) was welded under different welding
parameters and afterwards the mechanical properties
such as tensile strength, impact strength and hardness
were experimentally determined. On the basis of the
results obtained from the experimentation, the graphs
were plotted. It is the strength of welded joints, which
is fundamental property to the service reliability of
the weldments and hence present work was
undertaken to study the influence of axial pressure
and rotational speed in friction welded joints. Axial
pressure and rotational speed are the two major
parameters which can influence the strength and
hence the mechanical properties of the friction
welded joints. Thus the axial pressure and rotational
speed were taken as welding parameters, which
reflect the mechanical properties.
Handa et al[39] investigated that Joining of dissimilar
metals is one of the most essential needs of
industries. There are various welding methods that
have been developed to obtain suitable joints in
various applications. However, friction welding is a
joining process that allows more materials and
material combinations to be joined than with any
other welding process. Continuous drive friction
welding studies on austenitic stainless steel and
ferritic steel combinations has been attempted in this
investigation. Friction welding process parameter
optimization, mechanical characterization and
fracture behavior is the major contribution of the
study. The microhardness across the weld interface
was measured and the strength of the joint was
determined with tensile tests and impact tests. Also
the tensile fractured specimens were examined by
scanning electron microscopy so as to study its
fracture behavior. The experimental results indicate
that axial pressure has a significant effect on the
mechanical properties of the joint and it is possible to
increase the quality of the welded joint by selecting
the optimum axial pressure. Handa et al[40] studies
that austenitic stainless steel needs to be welded
specially
in
power
generation
industries.
Unfortunately the austenitic stainless welding has
several fabrication and metallurgical drawbacks when
welded by using conventional fusion welding
methods, which can often leads to in-service failure.
The most pronounced fabrication faults are hot cracks
due to inadvertent use of incorrect welding
electrodes, primarily carbon steel electrodes. The use
of carbon steel electrode results in the formation of
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very hard, crack-susceptible bulk structure on the
stainless steel side. Such hard and brittle zones may
render to localized pitting corrosion attack, hydrogen
embrittlement, sulfide stress cracking, and stress
rupture. Thus conventional fusion welding of many
metalsare not feasible owing to the formation of
brittle and low-melting inter-metallic. Solid state
welding processes that limit extent of intermixing are
generally employed in such situations. Friction
welding (FRW) is one such solid state welding
process that can be employed in such situations. In
the present investigation an experimental set-up was
made in order to achieve friction welding of
plastically deformed AISI 304 steels.In this
experimental study austenitic stainless steel (AISI
304) was welded under different welding parameters
and afterwards the mechanical properties such as
tensile strength, impact strength and hardness were
experimentally determined. It is the strength of
welded joints, which is fundamental property to the
service reliability of the weldments and hence present
work was undertaken to study the influence of axial
pressure and rotational speed in friction welded
joints.
Materials Transactions, Vol. 49, 2008, pp. 1129
-1131.
2. M. Koilraj, V. Sundareswaran, S. Vijayan, S.R.
Koteswara Rao,“Friction stir welding of
dissimilar aluminum alloys AA2219 to
AA5083– Optimization of process parameters
using Taguchi technique”
Materials and Design , 2012, pp. 1–7.
3. R. Palanivel, P. Koshy Mathews, N. Murugan, I.
Dinaharan, “Effect of tool rotational speed and
pin profile on microstructure and tensile strength
of dissimilar friction stir welded AA5083-H111
and AA6351 T6 aluminum alloys”, Materials
and Design ,2012 , pp. 7–16.
4. R. PalaniveI, P. Koshy Mathews, “Mechanical
and microstructural behaviour of friction stir
welded dissimilar aluminum alloy”, IEEE
International Conference On
Advances In
Engineering, Science And Management , 2012,
pp. 7- 11.
5. A.A.M. da Silva, E. Arruti, G. Janeiro, E.
Aldanondo, P. Alvarez, A. Echeverria, “Material
flow and mechanical behaviour of dissimilar
AA2024-T3 and AA7075-T6 aluminum alloys
friction stir welds”, Materials and Design ,2011 ,
pp. 2021–2027.
6. H. Jamshidi Aval, S. Serajzadeh, A.H. Kokabi,
“Evolution of microstructures and mechanical
properties in similar and dissimilar friction stir
welding of AA5086 and AA6061”, Materials
Science and En’gineering A 528 ,2011, pp.
8071– 80853.
7. Changbin Shen, Jiayan Zhang, Jiping Ge,
“Microstructures and electrochemical behaviors
of the friction stir welding dissimilar weld”,
Journal of Environmental Sciences, 2011,
23(Supplement) S32–S35.
8. V.-X. Tran, J. Pan, T. Pan, “Fatigue behavior of
spot friction welds in lap-shear and cross-tension
specimens
of
dissimilar
aluminum
sheets”,International Journal of Fatigue,2010, pp.
1022–1041.
9. T-S. Jun, K. Dragnevski, A.M. Korsunsky,
“Microstructure, residual strain, and eigenstrain
analysis of dissimilar friction stir welds”,
Materials and Design ,2010 , pp. S121–S125.
10. M. Ghosh, K. Kumar, S.V. Kailas, A.K. Ray,
“Optimization of friction stir welding parameters
for dissimilar aluminum alloys” Materials and
Design ,2010 , pp. 3033–3037.
11. N. Shanmuga Sundaram, N. Murugan, “Tensile
behavior of dissimilarfriction stir welded joints
of aluminum alloys” Materials and Design ,2010
, pp. 4184–4193.
Conclusion
The basic conclustion of friction stir welding
of dissimilar materials focusing on aluminum to other
materials has been conducted. The latter focuses on
dissimilar aluminium alloys, aluminum to
magnesium, aluminum to steel and titanium.
Furthermore, this paper review showed that there is
asignificant progress in FSW of dissimilar materials.
Most of the cited research studies are more focused
on understanding the microstructure and physical
properties of various welds. FSW technology need to
be more developed to enable the technique to be
employed industrially. The full understanding of the
dissimilar FSW process is needed to accommodate
the huge demand in the industries including
manufacturing andthe aerospace industry.
The conclustion of friction welding is that
mechanical properties were found to vary with the
applied axial pressure, which indicates that axial
pressure is an important welding axial pressure could
be successfully optimized for the friction welding
process on the basis of the results of the current
investigation.
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