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Citation: Wang, G.; Peng, C.; Zhang,
B.; Xu, Z.; Li, Q.; Liu, K.; Lu, P. Effect
of the Annealing Process on the
Microstructure and Performance of
5056 Aluminum Alloy Wires. Metals
2022,12, 823. https://doi.org/
10.3390/met12050823
Academic Editor: Thomas Niendorf
Received: 11 April 2022
Accepted: 7 May 2022
Published: 10 May 2022
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metals
Article
Effect of the Annealing Process on the Microstructure and
Performance of 5056 Aluminum Alloy Wires
Gaosong Wang 1,* , Chong Peng 2, Boyang Zhang 1,2, Zhaoyu Xu 1,2, Qiangqiang Li 2, Kun Liu 3
and Pengwei Lu 2
1Key Laboratory of Electromagnetic Processing of Materials, Ministry of Education, Northeastern University,
Shenyang 110819, China; zbyang1216@163.com (B.Z.); wgs2424@163.com (Z.X.)
2School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China;
18204058239@163.com (C.P.); 2110249@stu.neu.edu.cn (Q.L.); 13390140921@163.com (P.L.)
3Department of Applied Science, University of Quebec at Chicoutimi, 555, Boulevard de l’University,
Chicoutimi, QC G7H 2B1, Canada; kun.liu@uqac.ca
*Correspondence: wanggs@epm.neu.edu.cn; Tel.: +86-13998192419
Abstract:
Recrystallization can affect the mechanical properties of aluminum alloys by changing
the grain structure, and even the secondary recrystallization will cause a sudden change in the
grain size in the alloy. In this work, by choosing different annealing treatments on the cold-drawn
5056 aluminum wire, the microstructure evolution in the alloy homogenized at different annealing
processes was discussed, and its influence on the mechanical properties was tested. The results
demonstrated that the different annealing treatments had a great effect on the recrystallized structure
in the 5056 aluminum alloy. During the annealing, it was observed that the recrystallization started at
250
◦
C and completed at 310
◦
C, leading to a significant decrease in the mechanical properties. When
the temperature was further increased to 530
◦
C, the secondary recrystallization occurred, and the
grain size of the secondary recrystallization was larger than that when the annealing temperature
was 560
◦
C. However, there was only a minor decrease in the mechanical properties. The reasons and
laws of the secondary recrystallization are analyzed and discussed in this paper.
Keywords: 5056 aluminum alloy; recrystallization; annealing process; microstructure
1. Introduction
The 5056 alloy is a high-magnesium aluminum alloy with good strength among the
non-heat treatable aluminum alloys. It has a good processing plasticity and corrosion
resistance. As a rustproof aluminum alloy with excellent comprehensive performance,
it is widely applied in the fields of aerospace and shipbuilding [
1
–
3
]. After anodizing
treatment, the alloy exhibits a good riveting performance and can be used as a rivet for
riveting aerospace structural parts [
4
]. The cold drawing of the 5056 aluminum alloy
can increase the strength while decreasing the plasticity, thereby affecting the quality of
products and even the subsequent processing, which goes against improving the use ratio
of the material [
5
]. Therefore, it is often necessary to anneal 5056 aluminum alloy wires
before the forming process. The movement of dislocations and defects in the aluminum-
magnesium alloy during the recovery process is utilized to reduce the strength, improve
the plasticity, eliminate the stress, and change the textural configuration of the alloy and
grain orientation while maintaining the effect of work hardening [6–8].
Although there are many studies on Al-Mg alloys, there are few studies on 5056 alu-
minum alloys. The 5056 aluminum alloy, similar to other conventional Al-Mg alloys,
contains less recrystallization-inhibiting elements; the grains tend to grow up during the
annealing process. Especially for alloys after cold deformation, grain growth is more
likely to occur during the annealing process. With the occurrence of recrystallization, the
deformation texture generated after cold deformation will transform to the recrystallization
Metals 2022,12, 823. https://doi.org/10.3390/met12050823 https://www.mdpi.com/journal/metals
Metals 2022,12, 823 2 of 13
texture [
9
–
11
]. In the grain growth process, large grains augment while small grains shrink
until they disappear, so that the average grain size of the system increases. However, if a
second-phase grain overtexture exists, the grain growth process will deviate from the nor-
mal kinetic characteristics and will be prone to abnormal grain growth, namely secondary
recrystallization [
12
,
13
]. Regarding the research on the recrystallization of Al-Mg alloys, the
recrystallization after cold rolling has mainly been studied. Ma Pengcheng et al. studied
the effects of the cold rolling process and annealing temperature on the microstructure and
performance of an Al-Mg alloy [
14
]. The results showed that when the total reduction ratio
was constant, the cold rolling process with a primary cold rolling reduction of 33.3% and
secondary cold rolling reduction of 75% can achieve high strength and excellent formabil-
ity. In the temperature range of 350~450
◦
C, the alloy exhibits excellent formability after
final annealing at 450
◦
C. Some scholars have also studied the recrystallization behavior
of Al-Mg alloys obtained by extrusion, such as Liu Jinan et al. who studied the effect
of annealing on the texture of 5B02 aluminum alloy pipes [
15
]. The texture strength of
grains in the alloy, especially the cubic texture and Goss texture, was significantly reduced
under the 2-h annealing process at 380
◦
C; during the plastic deformation, the number of
grains involved in the slip significantly increased, improving the homogeneity of the plastic
deformation of the pipes. A few researchers have studied the recrystallization behavior
after cold drawing deformation but there is limited open literature about the secondary
recrystallization behavior after cold drawing deformation in Al-Mg alloys.
With the 5056 aluminum alloy wires obtained from the drawing process of extrusion
poles through a cold deformation of 60% as the research object, this paper studied the
influence of the annealing process on the microstructure, mechanical properties, and texture
of the specimens, analyzed the mechanism of secondary recrystallization after annealing,
and summarized the rules in order to provide a theoretical basis for the drawing production
of 5056 aluminum alloys.
2. Materials and Methods
The experimental raw material was 5056 aluminum alloy extrusion poles with a
diameter of 9.5 mm. The nominal composition and actual composition (mass fraction) are
shown in Table 1.
Table 1. Mass fraction of 5056 aluminum alloy elements.
Element Cu Mg Mn Zn Cr Fe Si Al
Nominal 0.10 4.5–5.6 0.05–0.20 0.10 0.05–0.2 0.40 0.30 Bal
Experimental 0.003 5.01 0.16 0.01 0.15 0.12 0.04 Bal
After the 5056 aluminum alloy extrusion poles underwent repeated cold drawing, the
5056 aluminum alloy cold-drawn specimens were obtained with a total deformation of
60% or 6 mm. The RJ2-35-6 pit furnace was used for the heat treatment. According to the
literature [
16
,
17
], the annealing process in the present work was designed in three parts:
(1) the holding time was kept unchanged for 2 h, the holding temperature was from 190
◦
C
to 560
◦
C, and a group of experiments were carried out at intervals of 30
◦
C; (2) the holding
temperature was kept unchanged at 530
◦
C, and the temperature was kept for 10 min,
20 min, and 60 min respectively; (3) the holding temperature was kept unchanged at 560
◦
C
for 5 min, 10 min and 20 min, respectively. The annealing behavior and texture evolution
rule of the cold-drawn 5056 aluminum alloy wires at different annealing temperatures
were studied by hardness testing, a tensile test, microstructure observation, and texture
measurement. The hardness test was conducted on the HV-10Z micro-Vickers hardness
tester by measuring each specimen at no less than 5 hardness points and taking the average.
The metallographic specimens were mechanically ground and polished before anodic
coating treatment (with Baker’s reagent as the coating liquid), and their microstructure was
observed through a Leica 5000M upright polarizing microscope (Leica, Wetzlar, Germany).
Metals 2022,12, 823 3 of 13
EBSD analysis was conducted on the specimens using a Crossbeam 550 FIB (Oxford
Instruments, London, UK) focused ion beam scanning electron microscope (SEM) (Zeiss,
Dresden, Germany). The specimens for texture analysis were mechanically ground and
polished before electropolishing treatment to eliminate residual stress on their surface.
3. Results
3.1. Microstructures of Extrusion Poles and Drawn Wires
Figure 1is a polarized-light microstructure diagram obtained after the 5056 aluminum
alloy extrusion poles with a diameter of 9.5 mm were planed axially. The upper part of the
figure is the edge of the extrusion poles. The microstructure obtained through extrusion
deformation was basically equiaxial grains, and the grain size was significantly smaller
at the edge than that at the core, so that the area of grains at the edge was about 515
µ
m
2
while the area of grains at the core was about 2290 µm2.
Figure 1.
The polarization structure of the 5056 aluminum alloy extruded rod of
ϕ
9.5 mm after
planing along the axis direction.
Figure 2is a polarized-light microstructure diagram after the 5056 aluminum alloy
drawn wires of
ϕ
6 mm were planed axially. The left and right sides of the figure are
the edge of the wire. The grain morphology of the 5056 aluminum alloy changed from a
near-spherical shape in the as-extruded state into a near-spindle shape in the as-drawn
state. The direction of the two sharp corners of the spindle shape was the direction of
drawing deformation, and the grain size was significantly smaller at the edge than at the
core, so that the area of spindle-shaped grains at the edge was about 567
µ
m
2
while the
area of spindle-shaped grains at the core was about 2447 µm2.
Figure 2.
The polarized light microstructure of 5056 aluminum alloy drawn wires of
ϕ
6 mm after
being planed axially.
Figure 3shows the metallographic photos after as-extruded state and the as-drawn
state. During the extrusion, the residual particles fragmented into small particles distributed
along the grain boundaries (Figure 3a). During further cold-drawing, little change was
observed on the residual particles due to the minor deformation (from
ϕ
9.5 mm to
ϕ
6 mm)
and they were still evenly distributed along the grain boundaries.
Metals 2022,12, 823 4 of 13
Figure 3.
Metallographic photographs of the as-extruded and as-drawn states: (
a
) As-extruded state
(b) As-drawn state.
3.2. Effect of Annealing Treatments on the Microstructure and Performance of an as-Drawn
5056 Aluminum Alloy
In the present work, it is observed that the grain structure is similar in the temperature
range of 190–220, 220–310, 310–400, and then 530 and 560
◦
C, therefore, the grain structure
at typical temperatures is selected and shown in Figure 4, which shows the polarized-light
microstructure of a
ϕ
6 mm thick 5056 aluminum alloy wire after 2-hour annealing at 220,
250, 310 and 400
◦
C while more grain structure at higher temperatures (530 and 560
◦
C)
is shown in Figures 5and 6. From Figure 4a, it can be seen that the alloy preserved the
spindle-shaped drawing deformation microstructure without undergoing recrystallization
after being annealed at 220
◦
C for 2 h; however, it can be seen from Figure 4b that some fine
equiaxial grains were generated, which means that partial recrystallization occurred after
annealing at 250
◦
C for 2 h. As the annealing temperature kept rising, Figure 4c,d were
obtained, from which can be seen that the alloy underwent a complete recrystallization
such that its interior was teeming with uniformly distributed equiaxial grains without any
spindle-shaped deformation microstructure [18,19].
Figure 5shows the polarized-light microstructures of as-drawn state 5056 aluminum
alloy wires after 10-, 20-, and 60-min thermal insulations at 530
◦
C, respectively. It can
be seen from the figure that the alloy underwent a complete recrystallization after being
treated at 530
◦
C for 10 min, such that its interior was teeming with uniformly distributed
equiaxial grains without any spindle-shaped deformation microstructure. After the alloy
was treated at 530
◦
C for 20 min, a few extraordinarily large grains appeared at the edge of
the wires. After the alloy was treated at 530
◦
C for 60 min, secondarily recrystallized grains
appeared everywhere except at one edge where normal recrystallized grains remained.
The area of the grains was about 5,742,301
µ
m
2
, while the area of the normal primarily
recrystallized grains at the exceptional edge was only about 56 µm2.
Figure 6shows the polarized light microstructure of the as-drawn state 5056 aluminum
alloy wires after 5-min, 10-min, and 20-min thermal insulations at 560
◦
C, respectively.
It can be seen from the figure that the alloy underwent a complete recrystallization after
being treated at 560
◦
C for 5 min, such that there was no spindle-shaped deformation
microstructure but a certain number of secondarily recrystallized grains in the exterior of
the alloy and still a large number of primarily recrystallized grains that were not swallowed.
There was basically no obvious qualitative change in the microstructure of the alloy which
was treated at 560
◦
C for 10 min, as compared to that which was treated at 560
◦
C for
5 min. However, after the alloy was treated at 560
◦
C for 20 min, other a certain number of
primarily recrystallized grains that remained amid the secondarily recrystallized grains,
most regions were teeming with secondary recrystallized grains, and the area of secondarily
Metals 2022,12, 823 5 of 13
recrystallized grains after 560
◦
C/20 min treatment was about 120,572
µ
m
2
, far smaller
than the area of secondarily recrystallized grains after the 530
◦
C/60 min treatment. The
area of normal primarily recrystallized grains after 560
◦
C/20 min treatment was about
78.5 µm2.
Figure 4.
The polarized-light microstructure of a
ϕ
6 mm thick 5056 aluminum alloy wire after 2-h
annealing: (a) 220 ◦C; (b) 250 ◦C; (c) 310 ◦C; (d) 400 ◦C.
Figure 5.
The polarized-light microstructure of as-drawn state 5056 aluminum alloy wires after
thermal insulation at 530 ◦C for different durations: (a) 10 min; (b) 20 min; (c) 60 min.
Metals 2022,12, 823 6 of 13
Figure 6.
The polarized-light microstructure of as-drawn state 5056 aluminum alloy wires after
thermal insulation at 560 ◦C for different durations: (a) 5 min; (b) 10 min; (c) 20 min.
Figure 7is a Vickers hardness data map of 5056 aluminum alloy drawn wires after dif-
ferent annealing processes. It can be seen from the figure that the as-drawn state hardness
of 5056 aluminum alloy was 123 HV. After the 2-h annealing treatment of thermal insulation
at different annealing temperatures, the hardness decreased to varying degrees with the
rise in temperature. The whole decreasing process roughly fell into four stages: (1) when
the annealing temperature ranged between 190
◦
C and 310
◦
C, the hardness of 5056 alu-
minum alloy wires decreased dramatically with the rise in the annealing temperature, from
103 HV at 190
◦
C to 73 HV at 310
◦
C of the annealing temperature; (2) when the annealing
temperature ranged between 310
◦
C and 500
◦
C, the hardness of 5056 aluminum alloy
wires basically leveled off without significant variation; (3) when the annealing tempera-
ture ranged between 500
◦
C and 560
◦
C, the hardness of 5056 aluminum alloy wires first
decreased slightly and then increased slightly with the rise in the annealing temperature.
Figure 7.
Vickers hardness of a cold-drawn 5056 aluminum alloy after annealing at different temperatures.
Figure 8shows the change in the mechanical properties of 5056 aluminum alloy
drawn wires after different annealing processes. It can be seen from the figure that the
maximum tensile strength of the cold-deformed alloy was 422 MPa while the minimum
elongation percentage was 10.30%. After the 2-h annealing treatment of thermal insulation
at different annealing temperatures, the strength of the alloy decreased while the elongation
percentage increased by distinct rates within distinct temperature ranges with the rise in the
annealing temperature. When the annealing temperature was 190
◦
C, the tensile strength
Metals 2022,12, 823 7 of 13
was 363 MPa, 14% lower than when the wires were unannealed, and the elongation
percentage increased to 14.95%; when the annealing temperature was 190~250
◦
C, the
strength of the alloy decreased slightly with the rise in the annealing temperature; when the
annealing temperature rose from 250
◦
C to 280
◦
C, the tensile strength and yield strength of
the alloy both decreased significantly, and the elongation percentage of the alloy increased
significantly; when the annealing temperature was 310~500
◦
C, the strength and elongation
percentage of the alloy changed little with the rise in the annealing temperature; when the
annealing temperature was 530
◦
C, the strength decreased slightly; when the annealing
temperature rose to 560 ◦C, the strength increased slightly again.
Figure 8.
Tensile property curves of a cold-drawn 5056 aluminum alloy after annealing at differ-
ent temperatures.
3.3. Textural Change
Figure 9shows the curves of the specimens and the distribution of grain boundary
misorientation angles. From Figure 9d, the distribution of misorientation angles in the
as-drawn state of the alloy can be observed. The number of small-angle grain boundaries in
the as-drawn state of the alloy was large, accounting for 30.9% of the total grain boundaries,
while the number of large-angle boundaries was extremely small. There were a large
number of grain boundaries of less than 2
◦
in the specimens. It can be observed from
Figure 9b that after the alloy was annealed at 400
◦
C for 2 h, its interior microstructure was
predominated by equiaxial grains without any spindle-shaped deformation microstructure,
and the sizes of the recrystallized grains were relatively uniform. Observing the distribution
of misorientation angles, large-angle grain boundaries accounted for 67.4% of the total
number of grain boundaries. It can be observed from Figure 9c that there were a certain
number of large grains in the alloy after 560
◦
C/2 h annealing. The grain size difference was
very significant in the field of view. From Figure 9f, it can be observed that the large-angle
grain boundaries of the interior microstructure of the alloy after 560
◦
C/2 h annealing
accounted for 56.3% of the total number of grain boundaries.
Figure 10 is the ODF cross-sectional views of the cold-drawn state and temperature-
varying annealed state 5056 aluminum alloy sheet specimens. As can be seen from
Figure 10a
, the 5056 aluminum alloy wires with a drawing deformation of 60% con-
tain strong textures. The main texture components were at (90
◦
, 45
◦
, 45
◦
) and (30
◦
, 80
◦
,
45
◦
),
i.e., {441}<232>
with the maximum intensity of 30.3 in the as-drawn state 5056 alu-
minum alloy. However, compared with the cold-drawn state alloy, after annealing at 400
◦
C
(Figure 10b), the textures after annealing at 400
◦
C were totally eliminated, which can be
attributed to a fully recrystallization microstructure composed of equiaxed grains with
nearly random orientations, as shown in Figure 9b. Meanwhile, Figure 10c is the ODF
image after secondary recrystallization. It can be seen that the ODFs were still lack of
texturing despite the appearance of a few orientations [20].
Metals 2022,12, 823 8 of 13
Figure 9.
Curves and distribution of grain boundary misorientation angles after a 5056 aluminum
alloy was annealed at different temperatures: (a,d) cold-drawn state; (b,e) 400 ◦C; (c,f) 560 ◦C.
Figure 11 shows the orientation density of each texture under different conditions.
It can be seen from the figure that after annealing at 400
◦
C and 560
◦
C, the orientation
density of the texture decreases significantly compared with the as-drawn state. This is the
same phenomenon as in Figure 9. The drawn wires were annealed at 400
◦
C and 560
◦
C,
complete recrystallization and secondary recrystallization occurred, which was one of the
reasons why the strength of the drawn wire decreased after annealing.
Figure 10. Cont.
Metals 2022,12, 823 9 of 13
Figure 10.
ODF cross-sectional views of a 5056 aluminum alloy after annealing at different tempera-
tures (a) cold drawing; (b) 400 ◦C; (c) 560 ◦C.
Metals 2022,12, 823 10 of 13
Figure 11.
Orientation density of textures of the 5056 aluminum alloy was annealed at different
temperatures (a)α-fiber; (b)β-fiber.
4. Discussion
There are few alloying elements that inhibit recrystallization in 5056 aluminum alloys.
The plastic deformation of high-temperature large deformation occurs in the extrusion
deformation process, and dynamic recrystallization occurs in the plastic deformation
process. The metal flow at the edge is larger in the extrusion deformation process, resulting
in a large amount of deformation at the edge of the extrusion poles. According to the
Johnson–Meir equation [
21
,
22
], the large deformation at the edge of the extrusion poles is
responsible for the small size of the recrystallized grains at the edge.
Combined with the microstructure changes, the mechanical properties of the alloy
through different annealing processes have been analyzed. From Figures 7and 8, it can
Metals 2022,12, 823 11 of 13
be found that when the annealing time was 2 h and the annealing temperature is in the
range of 190
◦
C to 560
◦
C, the mechanical properties of the drawn wire after annealing will
be greatly reduced compared with the as-drawn wire. The trend can be divided into the
following stages:
(1)
When the annealing temperature is up to 220
◦
C, the mechanical properties of the
drawn wire after annealing are remarkable reduced compared with that of the unan-
nealed drawn wire. Comparing Figures 2and 4a, it can be found that the grain size of
the drawn wire after annealing at 220
◦
C has no obvious change. Hence, it is believed
that the reason for the reduction of the strength of the drawn wire in this stage is
dominantly resulted from the release of work-hardening effect at relative temperature;
(2)
When the annealing temperature increased from 220
◦
C to 310
◦
C, the strength of the
drawn wires decreases significantly, the elongation increases rapidly, which can be
attributed to the static recrystallization during the annealing process. As shown in
Figure 4a, the grains are still elongated when annealed at 220
◦
C while the some fine
equiaxed grains along grain boundaries are observed (Figure 4b) when annealed at
250
◦
C. With further increasing annealing temperature to 310
◦
C (Figure 4c), all the
grains are completely transformed into equiaxed grains. This is due to the fact that
the higher the annealing temperature, the greater the driving energy of grain growth,
so that the recrystallization of the drawn wire occurs;
(3)
When the annealing temperature increased from 310
◦
C to 500
◦
C, the strength of the
drawn wires did not change significantly, which can be attributed to the stable stage
of grain structure. Comparing Figure 4c,d, it can be found that the grain size of the
drawn wire after annealing at 400
◦
C had no obvious change from that after annealing
at 310
◦
C. From this it can be concluded that the drawn wire is fully recrystallized
within this annealing temperature range, and the size change of the recrystallized
grains inside the drawn wire is small, so that the hardness and strength of the drawn
wire remain stable within this annealing temperature range [23];
Comparing Figures 4–6, it is found that when annealed at 530
◦
C and 560
◦
C, the alloy
underwent secondary recrystallization, and with the increase in the annealing duration,
the number of secondarily recrystallized grains inside the alloy increased. The secondary
recrystallization of the alloy led to a slight decrease in the hardness and strength of the
alloy [
24
,
25
]. Furthermore, since the grain size at the annealing temperature of 560
◦
C was
smaller than that at the annealing temperature of 530
◦
C, the hardness and strength of
the alloy annealed at 560
◦
C were slightly higher than at 530
◦
C. At this time, the internal
strengthening mechanism of the alloy was predominated by solid solution strengthening
rather than by fine grain strengthening. Therefore, the strength and hardness of the alloy
decreased insignificantly within this annealing temperature range.
The aluminum alloy underwent recovery and recrystallization while annealed, and
the deformation texture tended to transform into a recrystallization texture along a specific
crystallographic direction. The phenomenon that the constituents of deformation texture
remained unchanged while the strength increased in the low-temperature annealing re-
covery stage has been reported in relevant studies [
26
,
27
]. The main reason is that the
merger and rotation of substructures in the recovery stage leads to a decrease in the average
orientation deviation between adjacent subgrains, so that the grains deviating from the
central position of a specific orientation concentrate towards the central position during
drawing, thereby increasing the strength of that orientation. As the annealing temperature
rises, the alloy undergoes a recrystallization, while the evolution of the recrystallization
texture is strongly dependent on the annealing temperature. With the further rise in the
annealing temperature, the alloy undergoes secondary recrystallization, resulting in a
decrease in the number of grains and an increase in the re-ratio of small-angle grains.
5. Conclusions
(1)
The interior microstructure of 5056 aluminum alloy wires in the as-extruded state is
a recrystallization texture, and the size of recrystallized grains at the edge is smaller
Metals 2022,12, 823 12 of 13
than at the core; after the 5056 alloy is drawn and deformed by a deformation amount
of 60%, its edge texture is rougher and larger than its core texture due to the effect of
the nonhomogeneous interior microstructure of the as-extruded state wires;
(2)
After 5056 aluminum alloy cold-drawn state wires were treated at different annealing
temperatures, it was found that the hardness and strength of the alloy decreased
significantly after annealing. When the annealing temperature reached 250
◦
C, the
alloy became recrystallized; when the annealing temperature increased to 310
◦
C,
it underwent the entire recrystallization. The hardness and strength of the alloy
decreased significantly within this annealing temperature range. When the annealing
temperature of 5056 aluminum alloy drawing wires was above 310
◦
C and below
530
◦
C, the interior microstructure of the alloy was predominated by equiaxial grains,
without a significant fluctuation in the mechanical properties of the alloy;
(3)
When the annealing temperature reached 530
◦
C, a few grains grew abnormally,
gradually swallowing a large number of equiaxial grains, and the secondary recrys-
tallization occurred. With the prolongation of the annealing duration, the number of
secondarily recrystallized grains increased, at which time the hardness and strength of
the alloy decreased. When the annealing temperature reached 560 ◦C, the size of the
secondarily recrystallized grains was smaller than that at the annealing temperature
of 530
◦
C, at which time the hardness and strength of the alloy were higher than when
it was annealed at 530 ◦C.
(4)
A strong microstructure predominated by a fiber texture was produced from the
cold-drawn 5056 aluminum alloy wires. After recrystallization, the fiber texture
transformed into the recrystallization texture. The strength of the recrystallization
texture somewhat declined as compared to that of the cold-deformed 5056 aluminum
alloy wires.
Author Contributions:
Conceptualization, G.W. and K.L.; methodology, G.W. and C.P.; investigation,
C.P., B.Z., Q.L. and P.L.; writing—original draft preparation, G.W. and C.P.; writing—review and
editing, Z.X., G.W. and K.L.; supervision, G.W. and K.L. All authors have read and agreed to the
published version of the manuscript.
Funding:
This research was funded by the Fundamental Research Funds for the Central Universities
(Nos. N2109006, N2002025).
Institutional Review Board Statement: Not applicable.
Informed Consent Statement: Not applicable.
Data Availability Statement: Not applicable.
Conflicts of Interest:
The authors declare no conflict of interest. The funders had no role in the design
of the study.
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