Effects
of the aging state and tensile strength on the fatigue properties of
6A01 aluminum alloy
B.S. Gong a,b, Z.J. Zhang a,b*, Q.
Q. Duan a,b, Z. Qu a,b, P. Zhanga,b, Z.F. Zhang a,b*
a Shi-changxu Innovation Center for Advanced
Materials, Institute of Metal
Research, Chinese Academy of Sciences, Shenyang, 110016, China
b School of Materials Science and Engineering,
University of Science and Technology of China. Hefei 230026, China
Abstract
To study the effects of the aging state and tensile strength on the
fatigue properties of 6A01 Al alloy, the high-cycle fatigue (HCF)
experiments were carried out for different aging states. The results
show that the 6A01 Al alloy with the highest tensile strength at
peak-aging state can exhibit the highest fatigue strength in comparison
with the overaged state and the underaged state. The main reason is that
the increased strength of the 6A01 Al alloy at peak-aging state can
improve the plastic deformation resistance and inhibit the fatigue crack
initiation. Besides, the intermittent distribution of grain boundary
precipitates at the peak-aging state is beneficial for reducing the
fatigue damage. From these results, it is verified that the tensile
strength plays a key role in the fatigue strength relative to the aging
state for the low-strength Al alloys.
Keywords:6A01 Al alloy; Aging state; Tensile strength; Fatigue strength
___________________
*Corresponding authors:
Z. J. Zhang, Email:zjzhang@imr.ac.cn,Z. F. Zhang, Email:zhfzhang@imr.ac.cn
Introduction
Low weight and high strength are the main basis for the selection of
materials for high-speed trains. 6XXX series Al alloys have been widely
used in the body structural parts due to their low density, medium
strength, good-forming ability and excellent welding performance
[1-4]. However, fatigue cracks
usually happen in the Al alloy components because of the alternating
load during long-term service [5-10]. It is estimated that
80%~90% failures of engineering components may result
from fatigue fracture [6,9], therefore, it is necessary to optimize
the fatigue performance of the 6XXX series Al alloy to improve their
fatigue damage resistance.
The fatigue performance of Al alloys is generally affected by two kinds
of factors: i.e external factors such as service environment [11-14]
and loading mode [12,15-17], and intrinsic factors including grain
size, inclusion size and microstructure homogeneity [17-20]. These
internal defects often lead to the initiation of fatigue cracks and
control their high-cycle fatigue (HCF) properties [21]. However, no
matter what kind of defects, the initiation of fatigue cracks is always
caused by the localization of plastic deformation under cyclic stress
lower than the nominal yield strength of the alloy. Therefore, how to
inhibit strain localization during cyclic loading is the key factor to
improve the fatigue performance.
For heat-treatable strengthening Al alloys, it is also found the aging
state affects the fatigue property through influencing the strain
localization. Zhang et al. [22] found that at the underaged
(UA) state the fatigue life is higher than that of peak-aging (PA) for
the high-strength Al alloys. The reason is that during fatigue loading,
plastic deformation becomes localized in the soft precipitate-free zone
(PFZ) of the PA state, which provides conditions for the initiation of
fatigue cracks. Besides, Li et al . [23] found that at the UA
state the fatigue life is twice that of the overaged (OA) state at the
same stress amplitude for 2E12 Al alloy, which was also attributed to
the high slip reversibility of dislocations and strain uniformity at the
UA state. However, Leng et al . [24] found that the OA state
of 7075 Al alloy with higher yield strength and elongation can exhibit
higher fatigue strength relative to the UA state. They attributed the
reason to the high fatigue cracking resistance of the UA state because
of the high strength.
From the research results above, it is still puzzled that there is not
clear rule for the effect of aging state on the fatigue properties of Al
alloys. Apart from the effect of the aging state, the tensile strength
itself may also have a great effect on the fatigue strength. This is
because normally, increasing the tensile strength can improve the
fatigue cracking resistance [25,26], therefore, both the aging state
and tensile strength should have significant effects on the fatigue
properties of Al alloys.
For further evaluating the coupling effect of tensile strength and aging
state on the fatigue properties, in this study, we employed the
low-strength 6A01 Al alloy with three aging states (UA, PA and OA). Then
the HCF tests were carried out on the 6A01 Al alloy with different
tensile strengths. Finally, the influencing mechanisms of the tensile
strength and aging state on the fatigue properties were deeply analyzed
by investigating the microstructure evolutions at different aging
states.
Experimental procedures
In this study, the industrial 6A01 Al alloy was selected as a rolling
plate. The chemical composition of the 6A01 Al alloy was 0.48 pct. Si,
0.59 pct. Mg, 0.14 pct. Fe, 0.14 pct. Cr, 0.05 pct. Cu, 0.05 pct. Zn and
balanced Al. To revel the influence of the aging states on the fatigue
properties, we carried out heat treatment experiments. The specific heat
treatment process is shown in Fig.1.
Hardness tests were administrated by a Vickers hardness tester employing
a loading force of five hundred gf and a habitation time of 10
s.
Seven indentations were tested for every specimen, and therefore the
norm of the center 5 indentations was adopted. The size of tensile and
fatigue specimens of 6A01Al alloy are shown in Fig. 2 and Fig. 3.
Tensile tests were performed on an Instron 5982 universal mechanical
testing machine with a strain rate of
10-3s-1 at room temperature (RT).
The tension- tension HCF tests were carried out on a GPS20 testing
machine with a frequency of 100 Hz and load ratio R = 0 controlled by
the stress amplitude.
The grain size of the 6A01 Al alloy was observed by optical microscope
(OM). Besides, the fatigue fracture and precipitated phase of 6A01 Al
alloy were observed by scanning electron microscope (SEM) and
transmission electron microscope (TEM), respectively.
OM observations were conducted on a BX53M instrumentation, automatically
ground and polished, and treated with an anodic membrane in the solution
(1.1 g H3BO3 + 3 ml HF+ 97 ml
H2O) for 75 s at an applied voltage of 25 V. The sample
observed by TEM were punched into 3 mm diameter disks from slices, and
then mechanically thinned to a thickness of 50 μm. Then TEM samples were
prepared by Struers-Tenupol-5 twinjet electro polishing device. with
polishing solution of 10% HClO4 and 90%
C2H5OH, operated at -25 °C and 35 V. TEM
examinations were performed an FEI Tecnai F20 transmission electron
microscope with a working voltage of 200 kV.
Experimental results
Hardness variation
To quickly determine the proper aging states, we systematically studied
the hardness variation with aging time of the 6A01 Al alloys at 175 °C,
and the result is shown in Fig. 4. It can be seen that the highest
hardness appears at an aging time of 8 h. Besides, the hardness values
are nearly the same when the aging times are 1 h and 72 h, which are
much lower than that of 8 h. Therefore, we choose the aging times of 1
h, 8 h and 72 h as the UA, PA and OA states for 6A01 Al alloys,
respectively, as marked in Fig. 4.
On the other hand, it could be seen that the hardness values the aged
6A01 Al alloy show two peaks and a valley in between, which can be owing
to the microstructure evolution with the aging time. It is generally
explained that the occurrence of the first peak may be attributed to the
high density of the GP zones. With the increase of aging time, the GP
zones gradually transform into the β′′ phase, and the second peak starts
to appear due to the accumulation of the β′′ phase. Therefore, the
valley of the hardness value should result from the transition of the
two strengthening mechanisms.
Microstructures and precipitates
The microstructures of the 6A01 Al alloy at different aging states are
shown in Fig. 5. It is seen that the grains are elongated along the
rolling direction for the three aging states, which is a typical
microstructure of Al alloys formed by hot extrusion [27, 28].
Besides, with the increase of aging time, the grain size remains
unchanged. Although the aging treatment does not affect the grain size,
it still has a great influence on the size and volume fraction of the
precipitated phases, which will be elaborated in the following
paragraphs.
Figs. 6(a)-3(c) shows the TEM images of the matrix precipitates for the
UA, PA and OA states, severally. It is apparent that the precipitated
phases are equally distributed within the matrix. Besides, with the rise
of aging time, the sizes of precipitated phases step by step increase,
while the density firstly increases and so decreases.
After solution aging treatment of the Al-Mg-Si alloys, it was found that
the precipitation sequence of the strengthening phase during the aging
process followed: SSSS → GP (I, II) zones → metastable β′′→ β
(Mg2Si) [29-33]. Therefore, the precipitated phases
are mainly GP zones at the UA state, as shown in Fig. 6(a). The GP zones
are coherent with the Al matrix. Besides, a large amount of needle-like
β′′ (Mg2Si) phases appeared at the PA state, as shown in
Fig. 6(b). The needle-like β′′ phases are semi-coherent with the Al
matrix and play the main role in strengthening. The β equilibrium phase
precipitated at the OA state, as shown in Fig. 6(c). The β phases are
incoherent with the Al matrix. Fig. 6(d) summarizes the average size of
precipitated phases at different aging states. The precipitated phases
size of the UA, PA and OA states are 34 nm, 45 nm and 100 nm,
respectively.
Tensile and fatigue properties
Fig. 7(a) displays the tensile stress-strain curves of the 6A01 Al alloy
at different aging states. It is apparent that the tensile and yield
strengths are the highest for the PA state, and those of the UA and OA
states are very close to each other. The tensile strength of the UA, PA
and OA states are 282 MPa, 324 MPa and 286 MPa, respectively.
The relationship between uniform elongation and tensile strength of the
6A01 Al alloy is shown in Fig. 7(b). It is found that the UA state shows
a better matching of strength and plasticity than that at the OA state.
According to the previous studies [34-36], the materials with high
strength-plasticity matching will yield a higher fatigue strength.
Therefore, it is expectant that the UA state should show better fatigue
properties than the OA state.
The S-N curves of the 6A01 Al alloy at different aging states are shown
in Fig. 8, in which the fatigue strength was calculated by the staircase
method. From Fig. 8, it is obvious that the fatigue lives of the PA
state are higher than those of the UA and OA states, besides, those of
UA are higher than OA. As the fatigue strength can intuitively reflect
the fatigue performance, we summarized the relationship between the
aging time and fatigue strength, as shown in the Fig. 8(b). It can be
seen that with the increase of aging time, the fatigue strength firstly
increases and then decreases, and the PA state displays the highest
fatigue strength.
Fatigue fractographies
The fatigue fracture surfaces of the three states are shown in Fig. 9.
It may be seen that the fatigue fracture morphologies are basically the
same for the three aging states, and the fatigue cracks mainly initiated
on the free surface of the specimens. Therefore, we can infer that the
fatigue damage mechanism should be similar for the different aging
states. For Al alloys, the fatigue sources usually originate from
inclusions, porosity and heterogeneous microstructure [37-42].
However,
compared with cast Al alloy, there are almost no inclusions and porosity
in wrought aluminum alloy. It is also true through the observation of
fatigue fractures. Therefore, it will be inferred that the fatigue
cracking ought to be mainly caused by the heterogeneous microstructure
or surface stress concentration.
Discussions
Influence of tensile strength on fatigue strength
From the experimental results above, it can be concluded that the PA
state displays both the highest tensile and fatigue strength. Besides,
the UA state with lower tensile strength but higher uniform elongation
relative to the OA state shows higher fatigue strength. These results
indicate that both the strength and elongation have important effects on
the fatigue properties, as claimed by the previous studies [35,43].
In view that the tensile strength under the true stress-strain
coordinate (named as the true tensile strength) can reflect the tensile
strength and uniform elongation simultaneously, we summarize the
relationship between the fatigue strength and the true tensile strength,
as shown in Fig. 10(a). It is apparent that increasing the true tensile
strength can effectively improve the fatigue strength. The main reason
is that the true tensile strength is a comprehensive reflection of both
the yield strength and the work-hardening capacity, both of which affect
the fatigue damage significantly. In general, the yield strength affects
the plastic deformation resistance, while the work-hardening capacity
influences the strain homogeneity during cyclic deformation [44,45].
Fig. 10(b) shows the work-hardening curves and the true stress-strain
curves of 6A01 Al alloy at the three aging states, which indicates that
the UA state has higher strain-hardening ability that the OA state.
Therefore, it is consistent with the fact that the UA state exhibits
higher fatigue properties than the OA state. These experimental results
also clarify the fact that the effect of tensile strength on the fatigue
strength is greater than that of aging states for the low-strength Al
alloys.
Besides, it can be found that the tensile strength of the 6A01 Al alloy
at the UA state is similar with the OA state, but the fatigue strength
at the UA is higher than that at the OA state. The reason may be
explained that the elongation at the UA state is higher than that at the
OA state, so the slip distance of dislocations is increased, inducing
the reduced plastic deformation inhomogeneity and the inhibited fatigue
crack initiation.
According to the study of Pang et al. , the relationship between
the fatigue strength and tensile strength of AISI 4340 high-strength
steel displays a parabolic form on the whole [46]. However, our
results between fatigue strength and tensile strength still show a
monotonous relationship. In comparison with the high-strength steel,
titanium alloy and hard Al alloy, the present 6A01 Al alloy belongs to
the low-strength material. Although the tensile strength of the 6A01 Al
alloy at the PA state is the highest among the three aging states, the
tensile strength may have not yet reached the peak of the parabola. In
other words, the tensile strength and fatigue strength are still in the
positive correlation stage. Therefore, the fatigue strength of the 6A01
Al alloy can be further improved by increasing the tensile strength.
Influence of grain boundary precipitates on the fatigue
properties
For materials with low strength and high plasticity, grain boundary (GB)
is that the most common initiation site for fatigue cracks [47].
Previous studies on the HCF properties of wrought alloys also indicate
that the localization of plastic deformation around GB is the main
reason for fatigue crack initiation [22,48]. Therefore, we
investigated the microstructures of the GBs for various aging states.
Fig. 11 shows the GB precipitates (GBP) and the PFZ at different aging
states. It is quite clear from Figs. 10(a)-10(c) that the spacing of GBP
and the width of PFZ firstly increase and then decrease with the
increase of aging time, and they are the largest at the PA
state. According to our previous
study [48], increasing the space of the GBP ought to facilitate the
penetration of dislocations across GBs. Besides, increasing the
dimension of PFZ also benefits for the evacuation of dislocations from
GBs, which also relieves the pilling-up of dislocations on GBs. Both of
the on top of factors might decrease the fatigue damage along GB and
improve the fatigue properties finally.
On the other hand, the dense chain-like GBP in the UA and OA states may
reduce the binding energy of GBs, so that the pilling-up of dislocations
is easy to prompt cracks at the GBs. However, the GBP with intermittent
distribution in the PA state has little reduction on binding energy of
GBs, so that the GBs are more tolerant to the dislocation impingement.
This may be also the reason why the PA state has the highest fatigue
strength in the 6A01 Al alloy.
Conclusions
Through studying the fatigue properties of the 6A01 Al alloy at
different aging states, the following conclusions can be drawn.
- Among the three aging states, the PA state displays both the highest
strength and the highest fatigue strength. This indicates that the
effect of the tensile strength on the fatigue strength is greater than
that at the aging state for the low-strength Al alloy.
- For the 6A01 Al alloy at the PA state, the discontinuous distribution
of the GBP and the increased width of the PFZ also contribute to the
improved fatigue property.
- The 6A01 alloy at the UA state has higher strain hardening ability,
better plasticity and higher true tensile strength that the OA state.