laser welding titanium-ss
TRANSCRIPT
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Microstructures and mechanical property of laser butt welding
of titanium alloy to stainless steel
Shuhai Chen, Mingxin Zhang, Jihua Huang , Chengji Cui, Hua Zhang, Xingke Zhao
School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing 100083, PR China
a r t i c l e i n f o
Article history:
Received 8 March 2013
Accepted 12 July 2013
Available online 24 July 2013
Keywords:
Laser welding
Titanium alloy
Stainless steel
Intermetallic compounds
a b s t r a c t
Laser butt welding of titanium alloy to stainless steel was performed. The effect of laser-beam offsetting
on microstructural characteristics and fracture behavior of the joint was investigated. It was found that
when the laser beam is offset toward the stainless steel side, it results in a more durable joint. The inter-
metallic compounds have a uniform thickness along the interface and can be divided into two layers. One
consists of FeTi + a-Ti, and other consists of FeTi + Fe2Ti + Ti5Fe17Cr5. When laser beam is offset by 0 mmand 0.3 mm toward the titanium alloy side, the joints fracture spontaneously after welding. Durable join-
ing is achieved only when the laser beam is offset by 0.6 mm toward the titanium alloy. From the top to
the bottom of the joint, the thickness of intermetallic compounds continuously decreases and the follow-
ing interfacial structures are found: FeAl + a-Ti/Fe2Ti + Ti5Fe17Cr5, FeAl +a-Ti/FeTi + Fe2Ti + Ti5Fe17Cr5and FeAl + a-Ti, in that order. The tensile strength of the joint is higher when the laser beam is offsettoward the stainless steel than toward the titanium alloy, the highest observed value being 150 MPa.
The fracture of the joint occurs along the interface between two adjacent intermetallic layers.
2013 Elsevier Ltd. All rights reserved.
1. Introduction
The joining of titanium alloy to conventional structural steel has
many industrial applications[1,2]. However, it is difficult to weld
titanium alloysto steel dueto great differencesin thermal, physical,
and chemical properties. According to the FeTi phase diagram[3],
the solubility of Fe in Ti is very low (0.1 at.%, at room temperature),
beyond which, intermetallic phases FeTiand then Fe2Ti (600 HVand
1000 HV respectively) begin to form [4]. These intermetallic phases
are highly brittle, causing conventional fusion-welded joints to
crack spontaneously, due to thermal-stress mismatch between the
two parent materials. Therefore, suppressing the formation of brit-
tle intermetallic compounds (IMCs) is the key to realizing reliable
joining. Diffusion bonding[5,6], brazing[7,8], and explosive weld-
ing [9,10] of steel and titanium has been investigated for thispurpose. These methods are effective to some extent in controlling
the formation of brittle intermetallic compounds, but their applica-
tions are restricted by joint configurations.
Friction stir welding is a novel solid-state welding method
which has been considered for joining titanium alloys to steel. Fa-
zel-Najafabadi et al. [11,12] achieved defect-free dissimilar lap
joints of CP-Ti to 304 stainless steel by adjusting friction-stir weld-
ing parameters. The maximum failure load of the joint reached 73%
of that of CP-Ti. Liao et al.[13]investigated the microstructures at
the interface of friction-stir lap joints of pure titanium and steel.
Swirling macro- and micro-intermixing zones of titanium and steel
were found along the interface, where tiny FeTi intermetallic par-
ticles were mixed with b titanium [13]. The investigations on
friction stir welding of titanium and steel focused mostly on the
lap configuration, but it was insufficient to study the butt
configuration.
Fusion welding, which is widely applied in industry, is con-
fronted with a great challenge in joining titanium alloys to steel.
In traditional arc welding, it is very difficult to control the molten
pool of titaniumsteel mixture, so a mass of intermetallic com-
pounds are formed during welding. Recently, the development of
high energy beam welding such as laser beam welding and elec-
tron beam (EB) wending have made fusion welding of titanium
alloy to steel possible.To reduce the residual tensile stress of the joint and improve
metallurgical reaction of the molten pool, copper was selected to
be the filler metal for electron beam welding of titanium alloy to
steel[14,15]. Electron beam welding needs to be performed in a
vacuum environment, which restricts its application. Laser weld-
ing, a new joining technology, has great advantages, such as high
efficiency, excellent controllability, and ability to be performed in
a non-vacuum environment. Hiraga et al.[16]applied a pulse laser
lap welding technique to join thin sheets of pure titanium and
stainless steel 304. Zhao et al.[17], suggested the laser lap welding
technique for joining titanium alloy to steel. They also obtained
further understanding of the welding process by FEM model
0261-3069/$ - see front matter 2013 Elsevier Ltd. All rights reserved.http://dx.doi.org/10.1016/j.matdes.2013.07.044
Corresponding author. Tel.: +86 010 62334859.
E-mail address: [email protected](J. Huang).
Materials and Design 53 (2014) 504511
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Materials and Design
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calculation. The laser butt welding of titanium alloy to steel need
Cu interlayer to improve metallurgical reaction and decrease resid-
ual stress. Tomashchuk et al.[18]reported that welding of Ti6Al4 V
to stainless steel AISI 316L through pure copper interlayer carried
out by pulsed Nd:YAG laser. The tensile strength of the welds is up
to 359 MPa and is limited by brittleness of CuTi2 + FeTi + a-Ti layersituated next to the solid Ti6Al4 V. Groza et al. [19] welded
X5CrNi1810 to Ti6Al4V through a copper foil, with the thick-ness of 600 lm, as intermediary layer by continuous NdYAG laser.The average value of tensile strength reached 328 Mpa. Thus, Using
Cu foil as an interlayer leads to acceptable strength characteristics
during laser welding of titanium alloy to steel.
Laser butt welding of titanium alloy to steel without filler metal
is not pay more attention. In fact, direct laser butt welding of tita-
nium alloy to steel is convenience in technology. Satoh et al.[20]
attempt to weld titanium alloy to stainless steel without filler me-
tal by laser welding, but tensile strengths of the joints were ob-
served to be lower than the base materials with failure occurring
through brittle fracture. And, investigation on the microstructures
is insufficient. To improve mechanical property of the joint, it is
necessary to understand deeply the weldability of titanium alloy
to steel without filler. Therefore, the weld characteristics and
microstructure should be investigated systematically.
The present work focuses on laser butt welding of titanium al-
loy to stainless steel without a filler metal. To control metallurgical
reactions in the molten pool, the welding experiments were per-
formed with various laser beam offsets, either toward the titanium
alloy or toward the stainless steel. The effect of laser beam offset
on the microstructural characteristics and mechanical property of
the joint was investigated.
2. Experiments
The plates of Ti6Al4V titanium alloy (100 50 1 mm3) and
201 stainless steel (100 50 1 mm3) were selected as laser
welding materials and their chemical compositions were showninTable 1. The plates manufacturing of titanium alloy and stainless
steel confirm to GB/T3621-94[21]and GB/T3280-92[22], respec-
tively. The interface sides of the specimens were carefully polished
and then clamped in a butt-weld geometry. A high-power (4 kW)
CO2laser with welding-head focal distance of 200 mm was used.
The laser beam was made to focus on the upper surfaces of the
specimens. All of the specimens were welded at a power of 2000 W
and a welding speed of 2 m/min to ensure full penetration of the
specimens. Influence of the laser beam offsets on the mechanical
property and microstructures of the joints were investigated be-
cause the formation of the intermetallic compounds is sensitive
to the offsets. The offsets toward stainless steel were defined as po-
sitive and those toward titanium alloy as negative, as shown in
Fig. 1a). In this study, welding with offsets of 0.6 mm,0.3 mm, 0 mm, 0.3 mm and 0.6 mm were performed.
The microstructures of the joint were observed by scanning
electron microscope (SEM) equipped with an energy-dispersive
X-ray spectrometer (EDS) which has 2% error for middle atom
number, after standard grinding and polishing procedures. Crystal
phases of the joints were identified by microbeam X-ray diffrac-
tometer (XRD). To increase diffracted intensity of the phases and
analyze broken position of the joints, the XRD tests were per-
formed at the fracture surface of the tensile specimen after tensile
test. The tensile strength of the joints at room temperature was
evaluated by a mechanical testing frame (INSTRON MODEL 1186)
at a cross head speed of 1 mm/min. The schematic diagram of
the tensile specimen is shown inFig 1b). The tensile test standards
are in accordance with ISO 6892: 1998[23].
3. Results
3.1. Weld appearance
Fig. 2shows the effect of the laser beam offsets on the surface
appearance of weld. When the offset is 0.6 mm (toward titanium
alloy), a durable joining was realized, as shown inFig. 2a. If the off-
sets are 0 mm and 0.3 mm (toward titanium alloy), the speci-
mens crackle noticeably during welding and then fractured
spontaneously after welding.Fig. 2b shows surface appearance of
the weld with a 0 mm offset. A number of cracks appear in the cen-
ter of the weld, resulting in spontaneous fracture after welding. It
appears that the weldability is bad when laser beam is offset to-
ward titanium alloy.
When the laser beam is offset toward stainless steel, all of the
specimens are joined durably, and the quality of the joint is im-
proved significantly. Fig. 2c shows the surface appearance of a
weld with a 0.6 mm offset. Compared to the 0.6 mm-offset weld,the surface appearance of weld is relatively smooth. The weld zone
was narrower because stainless steel has higher thermal conduc-
tivity (12.1 W/m K, 20C) than titanium alloy (5.44 W/m K, 20C)
[24]. Therefore, laser butt welding of titanium alloy to stainless
steel has better weldability when the laser beam is offset toward
stainless steel than toward titanium alloy.
Table 1
Chemical composition of materials used (wt%).
Name Fe C N H O Al V Ti
Titanium 60.3 60.1 60.05 60.015 60.2 5.56.8 3.54.5 rest
Name C Si Mn Cr N Ni P S Fe
Steel 60.15 60.75 5.57.5 16.018.0 60.25 3.55.5 60.03 60.06 rest
Fig. 1. Schematic diagram of laser welding of titanium alloy to stainless steel. (a)
The process and (b) tensile specimen (thickness: 1 mm).
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of Al, as shown inTable 2. Zones E and F can then be considered a
FeCrTi ternary system and phase compositions can thus be con-
firmed. The locations of these phases on the FeCrTi ternaryphase diagram [26] are as shown by E and F in Fig. 5. It can be
deduced that the light grey phase (E zone) and the white phase
(F zone) are Fe2Ti ands (Ti5Fe17Cr5), respectively.It can be seen that gray phases (D zone) and light grey phase (E
zone) are Fe2Ti phases. The contrast difference of the phases is
caused by different average atom numbers between D and C zones.
Therefore, interfacial structures of the joint are FeAl + Ti/
FeTi + Fe2Ti + Ti5Fe17Cr5.
3.2.2. Offset toward titanium alloy
Fig. 6shows the microstructures of the joint made by the laser
beam offset of 0.6 mm toward titanium alloy. Complex structures
appear at the interface. First, partial melting of stainless steel
Fig. 5. Liquidus surface of the FeCrTi ternary phase diagram[26].
Table 2
EDS results of the joints (at.%).
Position Ti Fe Cr Ni V Al
A 57.51 24.31 5.31 1.78 1.52 9.57
B 60.77 20.90 5.58 2.10 1.77 8.87
C 49.58 32.18 7.06 3.22 1.14 6.83
D 40.92 36.38 9.97 5.18 1.59 5.96
E 25.99 51.31 11.84 7.17 0.49 3.13
F 12.24 58.87 18.55 5.73 1.01 3.60
G 27.35 53.44 13.36 3.47 0.64 1.73
H 15.71 57.34 19.17 4.85 0.53 2.40
I 4.43 66.06 22.55 4.95 0.69 1.32
J 70.02 21.06 7.97 0.24 0.70
Fig. 4. Liquidus surface of the FeTiAl ternary phase diagram [25].
Fig. 6. Microstructures of the joint at the offset of laser beam toward to titanium
alloy. (a) Macro cross-section, (b) microstructures at the top of the joint and (c)microstructures at the bottom of the joint.
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appears at the top of the joint, as shown inFig. 6a. Second, the
thickness gradually decreases from the top to the end of the joint.
Third, different interfacial structures appear at the top, middle and
bottom of the joint. At the top of the joint inFig. 6b, two reaction
layers are formed. A grey layer is close to the fusion zone, defined
as Layer III in this paper. It can be deduced that the phase com-
positions of Layer III is same with Layer I because they have the
same morphology. The other white layer is close to stainless steel,defined as Layer IV. In this layer, a light grey dendritic structure
grows into Layer IV from the interface of Layer III and Layer IV. A
light grey fusion line appears between Layer IV and parent stain-
less steel. In the middle of the joint indicated by a rectangle in
Fig. 6b, the interfacial structures are the same as that made by
the laser beam offset toward stainless steel, as shown in Fig. 3b.
The structures consist of two layers of FeAl + Ti/FeTi + Fe 2Ti + Ti5-Fe17Cr5. At the bottom of the joint inFig. 6c, only one reaction layer
is formed between titanium alloy and stainless steel. It is con-
firmed that this layer has same structures with Layer I (FeAl + Ti).
According to above observation on the microstructures of the
joint, the phase compositions of Layer IV need to be confirmed.
In Layer IV, since the Al content is relatively low, the phase compo-
sitions can be identified as a FeCrTi ternary system. The compo-
sitions of the grey dendritic phase growing into Layer IV (G zone)
and white phase of the Layer IV (H zone) in the FeCrTi ternary
phase diagram are shown by D and E in Fig. 4. It can be believed
that the grey dendritic phase is Fe2Ti and the white phase is ter-
nary intermetallic compound s (Ti5Fe17Cr5). At fusion line (I zone),
the content of Ti slightly increases, compared to parent stainless
steel (J zone).
Therefore, the interfacial structures of the joint are from the top
to the bottom confirmed orderly as FeAl + Ti/Fe2Ti + Ti5Fe17Cr5?
FeAl + Ti/ FeTi + Fe2Ti + Ti5Fe17Cr5? FeAl + Ti.
3.3. mechanical property of the joint
To evaluate the mechanical property of the joint, tensilestrength tests were performed.Fig. 7 shows the influence of la-
ser-beam offsets on the tensile strength of the joints. Because the
specimens with the offsets of0.3 mm and 0 mm fracture sponta-
neous after the welding, the tensile strength is zero. When the off-
set is 0.6 mm, the tensile strength of the joint is only 24.75 MPa.
In contrast, when the offsets are 0.3 mm and 0.6 mm, the tensile
strength of the joints increase significantly. When laser beam is
offset to 0.6 mm toward stainless steel, the tensile strength of
the joint reaches 150 MPa. Therefore, the joints have higher tensile
strength when the laser beam is offset toward the stainless steel
than the toward the titanium alloy.
3.4. Fracture behavior of the joint
Fig. 8shows fracture surface of the joint made with laser-beam
offset of 0.6 mm toward titanium alloy. The fracture exhibits typi-
cal brittle characteristics. A relatively smooth fracture surface witha river patten appears at the top of the joint. In contrast, the frac-
ture at the middle and end of the joint exhibits relatively rough
morphology. In addition, many cracks along the thickness direction
of the plate appear at the fracture surface. When the offset is
0.6 mm toward stainless steel, the fracture morphology still exhib-
its typical brittle characteristics. However, the relatively smooth
fracture surface with river patten disappears and all fracture sur-
face becomes to relatively rough, as shown in Fig. 9. Also, the
cracks along the thickness direction of the plate is more dense than
that with laser beam offset of 0.6 mm toward titanium.
To confirm phase compositions at the fracture surface, XRD was
performed on all the samples, as shown inFig. 10. Because there
are complex element compositions of the joints, distortion of crys-
tal lattice is inevitable. Thus, the location of the diffraction peaks ofthe phase compositions may be offset from the location of the stan-
dard diffraction peak. It was found that a-Ti and Fe2Ti appear at allof the fracture surfaces. Theb-Ti do not appears at the fracture sur-
faces, which indicates that theb-Ti in the eutectic structures ofb-Ti
and FeTi transforms into a-Ti during the cooling of the weld.Therefore, it is confirmed that the Layer I consists ofa-Ti and FeTi.
The presence of the a-Ti at all fracture surfaces may indicate-that the joint fractures along the layer which containsa-Ti and FeTi(Layer I or Layer III). However, the presence of the Fe2Ti seems to
indicate that the joint fractures along Layer II or Layer IV. There-
fore, it can be concluded that fracture only occurs along the inter-
face between two adjacent layers.
It should be noted that some of the phases observed in SEM
were not found by the XRD. In general, the XRD results dependon diffracted intensity of the phases. Thus, the XRD were per-
formed at fracture surface to increase the diffracted intensity
[27]. However, some of the intermetallic compounds in this study
are uncontinuous and inhomogeneous in distribution, such as Ti5-Fe17Cr5. And, the content is relatively low. Therefore, some of the
phases maybe are not found by the XRD, although the XRD were
performed at fracture surface.
4. Discussion
When titanium alloy is mixed with the stainless steel in the li-
quid state, a number of brittle intermetallic compounds are formed
inside fusion zone during welding. Meanwhile, a stress mismatch
arises in the seam due to great difference in thermal expansioncoefficients between titanium alloy (7.89 106/C) and stainless
steel (16.9 106/C)[24]. The specimens fracture spontaneously
when a sufficient amount of intermetallic compounds has formed.
To improve the weldability of titanium alloy to steel, the Cu inter-
layer was used during laser welding[18,19]. On the one hand, the
Cu interlayer improved metallurgical reaction of weld pool, which
leads to the formation of TiCu intermetallic compounds[19]. On
the other hand, the interlayer decrease residual stress of the joint
[14]. Therefore, the tensile strength of the joint with the Cu inter-
layer reached to 359 MPa[18].
Outside using the Cu interlayer, suppressing liquid-state mixing
between titanium alloy and steel is an important way to realize
strong joining. Satoh et al.[20]attempted to weld titanium alloy to
steel without interlayer by Nd: YAG laser welding, but liquid-statesmixing between titanium alloy and steel is not suppressed fully.Fig. 7. Influence of the offset of laser beam on the tensile strength.
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Perhaps samples were processed at laser beam offsets from the
interfacetowardthe Tiplate,which isnot goodway proved inthispa-per. In our study, the liquid-states mixing is suppressed better by
controlling laser beam offset toward titaniumalloy. Thus, laser beam
offsetting toward titanium alloy is an effective way to suppress li-quid-state mixing during welding of titanium alloy to stainless steel.
Fig. 8. Fracture surface of the joint with laser beam offset of 0.6 mm toward to
titanium. (a) Macro fracture surface, (b) magnification of P1 zone and (c)
magnification of P2 zone.
Fig. 9. Fracture surface of the joint with the offset of 0.6 mm toward to stainless
steel. (a) Macro fracture surface, (b) magnification of P3 zone and (c) magnification
P4 zone.
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According to the results of the experiment, laser butt welding of
titanium alloy to stainless steel has better weldability when the
laser beam is offset toward stainless steel than toward titanium
alloy. This is closely related to the distribution and compositions
of the intermetallic compounds, which depend on the laser beam
offsets.
The intermetallic compounds along the interface between
titanium alloy and stainless steel are more uniform in thickness
when the laser beam is offset toward stainless steel than when
it is offset toward titanium alloy. This difference in thickness isa result of great difference in thermal conductivity between
stainless steel (12.1 W/m K, 20C) and titanium alloy (5.44 W/
m K, 20 C)[24]. Stainless steel has a higher thermal conductivity
than titanium alloy, which means that the thermal conduction
from the high temperature zone of the molten pool to the low
temperature zone is easier when laser beam is offset toward
the stainless steel rather than titanium. Thus, a more uniform
temperature distribution is achieved when the laser beam is off-
set toward stainless steel, which is the side with higher thermal
conductivity. The low temperature gradient along the interface
induces uniform thickness of intermetallic compounds. The
uneven thickness distribution of the intermetallic compounds
has negative influence on the mechanical property of the joint.
First, it causes an uneven distribution of residual stress in theseam, compared to the joint with uniform distribution of the
intermetallic compounds. Furthermore, stress concentration is
induced inside the seam. The residual stress compromises
mechanical property of the joint. Second, the residual stress
causes cracks to initiate at the top of the joint, where the thick
intermetallic compounds layer is. In particular, this causes the
specimens with the 0.3 mm and 0 mm offsets fracture sponta-
neously after welding. Third, the uneven thickness distribution
of the intermetallic compounds makes it more difficult to
control mechanical property of the joint: when the amount inter-
metallic compounds at the top of the joint are limited to a
reasonable level, the bottom of the joint would not have been
reliably welded yet; when the bottom of the joint is welded with
a reasonable amount of intermetallics, too much intermetallicswould have formed on the top of the joint. Therefore, the joint
with uniform thickness of intermetallic compounds, made by a
laser beam offset toward the stainless steel, has high tensile
strength.
When the laser beam is offset toward titanium alloy, the rela-
tively smooth fracture surface with river patten at the top of the
joint indicates that the crack propagation only required low en-
ergy, as shown inFig. 8b. The low propagation energy of the crack
leads to low tensile strength of the joint. According to the micro-
structures inFig. 6, slight melting appears at the top of the joint,
which indicates the mixing between titanium alloy and stainlesssteel. This proves that the mixing between titanium alloy and
stainless steel adversely affects the mechanical property of the
joint. The fracture morphologies when laser beam is offset toward
titanium alloy are similar with that observed by Satoh et al.[20],
because similar processing parameters were used. Meanwhile, the
phase compositions of this zone (FeAl +a-Ti/Fe2Ti + Ti5Fe17Cr5)greatly differ with other areas (FeAl +a-Ti/FeTi + Fe2Ti + Ti5Fe17Cr5 or FeAl + a-Ti) of the joint. Therefore, phase compositionmay be another important factor which contributes to low tensile
strength of joint made when the laser beam is offset toward the
titanium alloy.
5. Conclusions
From the investigation on microstructures and mechanical
property of laser butt welding of titanium alloy to stainless steel,
conclusions were summarized as following:
(1) When thelaser beam is offsettoward thestainless steel,dura-
ble joining is realized. The intermetallic compounds have
uniform thickness along the interfaceand canbe divided into
two layers: FeTi + a-Ti and FeTi + Fe2Ti + Ti5Fe17Cr5.(2) When the laser beam is offset by 0 mm and 0.3 mm toward
the titanium alloy, the joints fracture spontaneously subse-
quent to welding. Durable joining is obtained only when
the laser beam is offset by 0.6 mm toward the titanium alloy.
From the top to the bottom of the joint, the thickness ofintermetallic compounds continuously decreases and the
Fig. 10. XRD patterns of fracture surface of the joint. (a) 0.6 mm, (b) 0.3 mm, (c) 0.3 mm and (d) 0.6 mm.
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following interfacial structures are found: FeAl +a-Ti/Fe2Ti + Ti5Fe17Cr5, FeAl + a-Ti/FeTi + Fe2Ti + Ti5Fe17Cr5 andFeAl + a-Ti, in that order.
(3) The tensile strength of the joint is higher when the laser
beam is offset toward stainless steel than toward titanium
alloy, the highest value being 150 MPa. Fracture occurs along
the interface between two adjacent layers.
Acknowledgments
The authors appreciate the financial support from the National
Natural Science Foundation of China (No. 51004009) and the Fun-
damental Research Funds for the Central Universities (FRF-TP-12-
044A). The authors would like to express their gratitude to Dr. Bert
Liu, Department of Materials Science and Engineering, The Ohio
State University, for his help in English revision of this article.
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